Title of Invention	A CAST OR BLOWN TRANSPARENT EASY TEARABLE FILM AND PROCESS OF MANUFACTURE THEREOF
Abstract	A cast or blown transparent easy tearable film and process of manufacture thereof are disclosed. The cast film or blown film has a composition comprising 80 to 95 wt% of a polypropylene matrix (A) with an MFR2 of 1 to 30 g/10min being a homopolymer or a copolymer, which has a comonomer content of less than 3 wt%, 5 to 20 wt% of an ethylene-propylene-rubber (EPR) (B) with at least 55 wt% propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and 0.0001 to 1 wt% of an α-nucleating agent.

Title of Invention

A CAST OR BLOWN TRANSPARENT EASY TEARABLE FILM AND PROCESS OF MANUFACTURE THEREOF

Abstract

A cast or blown transparent easy tearable film and process of manufacture thereof are disclosed. The cast film or blown film has a composition comprising 80 to 95 wt% of a polypropylene matrix (A) with an MFR2 of 1 to 30 g/10min being a homopolymer or a copolymer, which has a comonomer content of less than 3 wt%, 5 to 20 wt% of an ethylene-propylene-rubber (EPR) (B) with at least 55 wt% propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and 0.0001 to 1 wt% of an α-nucleating agent.

Full Text	The present invention relates to a cast film or blown film having a high transparency, easy tear features and low extractables. Furthermore, the invention is related to a process for making the films as well as to the use of a heterophasic propylene composition for cast films and blown films. In the recent years there has been an increasing demand of heat-sealed pouches, in particular in the food industry, for example for rice or fodder for dogs and cats. A very well-known problem of such filled pouches is their opening. Often, the pouches can only be opened with a high effort at a predefined indentation (or perforation or notch) without using tools like knives and scissors. Another problem is that a manula opening does not lead to a straight crack in the pouches but to a curved one increasing the risk that the content of the pouches ooze out unintended. Hence, there is a demand to develop films for pouches which can be easily opened manually at the notch leading to a straight crack in the pouch. Described with physical parameters, it means that the tear energy has to be minimized and that the crack should develop straight in a pre- defined direction starting from the notch and usually in parallel direction to the upper side of the pouch. The materials used for such purpose have to be tough enough to resist impact loading at room or sub-ambient temperatures. Resins like polypropylene homopolymers and ethylene-propylene random copolymers which are brittle under severe loading are therefore excluded. Impact polypropylenes which are known for their high toughness are normally hazy and tend to develop plasticity when deformed, a property which limits the propagation of a linear crack through the pouch. Thus, they are no candidates of choice. Additionally the film shall fulfill certain standards issued by the food and drug administration (FDA), i.e. inter alia having low C6-extractables. Certainly the transparency of the film should also be good as the market favors transparent pouches. Therefore, it is the object of the present invention to provide a cast film or blown film having a high transparency, easy tear features and low extractables. The finding of the present invention is to provide a cast film or a blown film comprising a composition of a polypropylene matrix and an ethylene-propylene rubber (EPR) whereby the particles of the ethylene-propylene rubber (EPR) in the matrix develop a high orientation in one direction when the film is casted or blown. Hence, the present invention is related to a cast film or blown film comprising a composition comprising a) 80 to 95 wt% of a polypropylene matrix (A) with an MFR2 of 1 to 30 g/10 min being a homopolymer or a copolymer which has a comonomer content of less than 3 wt%; b) 5 to 20 wt% of an ethylene-propylene rubber (EPR) (B) with at least 55 wt% propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and c) 0.0001 to 1 wt% of an alpha-nucleating agent (C). Surprisingly, it had been found that such a cast film or blown film possesses a high transparency, low extractables and also very good tear features expressed in a low tear resistance, low tear whitening, low tear plasticity and a low tear angle. Definition of tear features Tear resistance, tear whitening, tear plasticity and tear angle have been used to describe the easy-tear performance of the different materials. Tear resistance (W), also called tear energy in the following, is that energy needed to propagate a crack in a precut sample at room temperature according to ISO 6383-2. It is commonly known as Elmendorf test. Tear resistance was determined at room temperature on 75630.1 mm or 75630.05 mm samples with a precut slit of 20 mm according to ISO 6383-2. The force required to tear the specimen completely along its length was used to calculate the tear resistance. Tear whitening (TW), tear plasticity (TP) and tear angle (TA) have been determined post mortem on the fractured samples used to assess the tear energy within 48 hours after having performed the Elmendorf test. Values provided in the following are valid for these fractured samples and correspond to about half of what would have been measured considering the whole samples (which consist of two broken halves). The tear whitening corresponds to the degree of whitening of the area around the fracture surface. It has been determined with a ruler and rationalized with marks: 0 correspond to no tear whitening at all, 1 to a tear whitening 2 to a tear whitening in between 0.3-0.5 mm (0.5 mm excluded), 3 to a tear whitening in between 0.5-1.0 mm (1.0 mm excluded), 4 to a tear whitening in between 1.0-2.0 mm (2.0 mm excluded), 5 to a tear whitening above 2.0 mm (2 " mm included)" The tear plasticity corresponds to the size of the damaged area around the fracture surface. This damaged zone is often called plastic zone. Depending on the polymer composition it will or won't exhibit whitening. It has been determined with a ruler and rationalized with marks: 0 correspond to no plasticity at all, 1 to a localized damage near the crack which size is to a damage localized in a zone of 1-2 mm around the main crack (2 mm excluded), 3 to a damage localized in a zone of 2-5 mm around the main crack (5 mm excluded), 4 to a damage localized in a zone of 5-10 mm around the main crack (10 mm excluded), 5 to a damage localized in a zone of > 10 mm around the main crack. The tear angle corresponds to the deviation of the crack towards a straight propagation. It has been measured with a protractor. All the above mentioned parameters have to be fulfilled to consider a material as easy tearable: Usually the notch (precut) is made in the machine direction, since the energy needed to propagate the crack is there the lowest. However, if WTD (preferably perfectly adapted as tear direction. To achieve these very good tear features, it is in particular necessary that the ethylene-propylene rubber (EPR) particles are expanded in one direction, i.e. that they are oriented in the direction in which the crack develops. To achieve this aim, a composition is needed as defined above. Hence the synergistic effect of all features contributes to a deformation of the ethylene-propylene rubber (EPR) particles in the propylene matrix leading to the orientation effect, which is mainly responsible for the good tear features but has also a positive influence on the transparency and low extractable properties. An important requirement in this context is the intrinsic viscosity of the ethylene-propylene rubber (EPR). The mtrinsic viscosity (IV) is a measure of the capability of a polymer in solution to enhance the viscosity of the solution. Intrinsic viscosity (IV) is correlated positively with the polymer molecular weight. The intrinsic viscosity (IV) is defined as the limiting value of the specific viscosity/concentration ratio at zero concentration. It thus becomes necessary to find the viscosity at different concentrations and then extrapolate to zero concentration. The variation of the viscosity number with concentration depends on the type of molecules as well as on the solvent. In general, the intrinsic viscosity of linear macromolecular substances is related to the molecular weight or degree of polymerization. With linear macromolecules, viscosity number measurements can provide a method for the rapid determination of molecular weight when the relationship between viscosity and molecular weight has been established. The intrinsic viscosity (IV) in this application is measured according to DIN ISO 1628-1 (October 1999). Accordingly, if the intrinsic viscosity (IV) of the ethylene-propylene rubber (EPR) is too high, i.e. higher than 2.5 dl/g, then the film will have a too high impact strength, which influences the tear resistance negatively, i.e. the tear energy is rather high. Moreover a high intrinsic viscosity (IV) is also correlated with rather big particles (with a diameter above 500 nm as observed on electron microscopy micrographs). Big particles, however, diminish the transparency of the film. On the other hand, if the intrinsic viscosity (IV) is too low, i.e. lower than 1.0 dl/g, then a production of the composition is rather difficult. It is in particular preferred, that the intrinsic viscosity (IV) is not higher than 2.3 dl/g, more preferably not higher than 2.2 dl/g and most preferably not higher than 2.1 dl/g. In turn, the lower limit of the intrinsic viscosity (IV) is preferably not lower than 1.2 dl/g, more preferably not lower than 1.4 dl/g. Preferred ranges are 1.0 to 2.3 dl/g, more preferably 1.2 to 2.3 dl/g, still more preferably 1.2 to 2.2 dl/g and most preferably 1.2 to 2.1 dl/g. Preferably, not only the intrinsic viscosity (IV) of the ethylene-propylene rubber (EPR) alone should be considered, but also the polypropylene matrix used. It should be in particular avoided that the ethylene-propylene rubber (EPR) has a similar intrinsic viscosity (IV) to the polypropylene matrix. A good elongation of the ethylene-propylene rubber (EPR) is especially achieved if the intrinsic viscosities of the ethylene-propylene rubber (EPR) particles and the polypropylene matrix differ to some extent. Therefore to further improve the orientation effect, it is preferred that the polypropylene matrix has a higher intrinsic viscosity (IV) than the ethylene-propylene rubber (EPR). This proportion of the polypropylene matrix and the ethylene-propylene rubber (EPR) to each other enables a specifically good elongation of the ethylene- propylene rubber particles in the polypropylene matrix. It has been, in particular, found out that it is especially preferred that the ratio of the intrinsic viscosity (IV) of the ethylene-propylene rubber (EPR) to the polypropylene matrix (IVEPR/IVmatrix) is not higher than 0.85, more preferably not higher than 0.8. Preferably, the polypropylene matrix has an intrinsic viscosity (IV) of 1.8 to 4.0 dl/g, more preferably of 2.0 to 3.5 dl/g. As stated above the intrinsic viscosity (IV) is of particular relevance in this application, as it influences the orientation effect needed. On the other hand the intrinsic viscosity (IV) is an indicator of the molecular weight. A high intrinsic viscosity (IV) results from a high molecular weight. Another way to express the molecular weight of a polymer is by way of its melt flow rate (MFR). The melt flow rate mainly depends on the average molecular weight. This is due to the fact that long molecules render the material a lower flow-tendency than short molecules. An increase in molecular weight means a decrease in the MFR-value. The melrflow rate (RFR) is measured in g/10 min of the polymer discharged through a defined dye under specified temperature and pressure conditions and the measure of viscosity of the polymer which, in turn, for each type of polymer is mainly influenced by its molecular weight but also by its degree of branching. The melt flow rate measured under a load of 2.16 kg (ISO 1133) is denoted as MFR2. Hence as both measuring methods are interlinked by the molecular weight of the polymer, also the melt flow rate (MFR) has to be carefully considered. Therefore it is required, that the polypropylene matrix shall have a specific melt flow rate (MFR). If the melt flow rate MFR2 is too low (high molecular weight polymer matrix), i.e. lower than 1 g/10min, then, the easy tear features are far from target due to the high ductility of the matrix which promotes plastic deformation. Hence, the polypropylene matrix shall have an MFR2 of not lower than 1 g/lOmin, more preferably not lower than 1.5 g/lOmin. On the other hand, if the MFR2 is too high, i.e. higher than 30 g/lOmin, then the polypropylene matrix has inferior transparency and can not easily been processed. Moreover a too high melt flow rate (MFR2) of the polypropylene matrix boosts the particle size of the ethylene-propylene rubber (EPR) which is also detrimental for the orientation effect as well as for the transparency of the film. It is in particular preferred, that the MFR2 of the polypropylene matrix is not higher than 20 g/10 min, more preferably not higher than 10 g/10min. In addition it is preferred, that the composition has a MFR2 of at least 1.5 g/10 min, more preferably of at least 2 g/lOmin. The type of polypropylene matrix is not restricted to a specific one, as long as the matrix fulfills the above mentioned requirements. Hence, each homopolymer or copolymer can be used. In case a copolymer is used, the comonomer content, however, shall be less than 3 wt%, otherwise the film gets too ductile affecting negatively the easy tear features. Preferably, the comonomer is ethylene. The choice of ethylene-propylene rubber (EPR) must conform with the orientation requirement and the transparency targeted. Hence an ethylene- propylene rubber (EPR) is needed having a high propylene amount, i.e. a propylene amount of at least 55 wt% in the rubber. More preferably the amount of propylene in the ethylene-propylene rubber (EPR) is at least 58 wt%, more preferably at least 60 wt%. Moreover to achieve good tear features the weight ratio of the polypropylene matrix and the ethylene-propylene rubber (EPR) must be kept in a specific range. Accordingly, the composition does not have more than 20 wt% of the ethylene-propylene rubber (EPR), otherwise the film will be too soft and a linear crack cannot be guaranteed anymore. Therefore the amount of polypropylene matrix must range from 80 to 95 wt%, preferably in the range of 82 to 93 wt%. In turn, the ethylene-propylene rubber (EPR) must be in the range of 5 to 20 wt%, preferably in the range of 7 to 18 wt%. To achieve the desired properties of the present invention, it has been further found out, that also the film must have a high cristallinity. A highly structured (crystal) polymer has improved optical and mechanical properties, i.e. a good tear performance expressed by a low tear energy. Therefore the composition employed must comprise an alpha-nucleating agent in the amount of 0.0001 to 1 wt%, preferably in the amount of 0.001 to 0.5 wt%. Alpha-nucleating agents of polypropylene are substances with the ability to act as substrates for crystal formation by epitaxy thus increasing the number of nuclei of the system. Thereby the nucleating agents improve the crystallization behavior in processing, i.e. decreasing the cycle time or increasing the line speed, increase the crystallinity in the final product and, additionally, improve the optical and mechanical properties in terms of improved stiffness and here of lower tear energy. Any suitable alpha-nucleating agent known in the art can be used. However, it is preferred to use at least one alpha-nucleating agent selected from the group consisting of sodium benzoate, l,3:2,4-bis-(3,4-dimethyl-benzylidene)-sorbitol, sodium-2,2l-methylenebis-(4,6-di-tert-butyl-phenyl)-phosphate and hydroxybis-(2,4,8,10-tetra-tert-butyl-6-hydroxy-12h-dibenzo-(d,g)( 1,3,2)- dioxaphosphocin-6-oxidato)-aluminium. A further a-nucleation method, herein referred to as "BNT", is a special reactor technique, where the catalyst is prepolymerised with monomers like vinylcyclohexane (VCH). This method is described in greater detail in e.g. EP 0 316 187 A2. For the purpose of this invention "BNT" is referred to as a-nucleating agent. Preferably, the thickness of the film should not be too high since otherwise a significant loss in transparency will be the effect. Therefore, it is preferred that the film has a thickness of 5 to 200 µm, more preferably of 10 to 150 µm. Preferably, the film shall have only few C6-extractables measured according to FDA-HHS 177.1520 where 2.5g of the sample are extracted at 50°C with 1 1 hexane in a Soxhlet apparatus for 24 h. It is in particular preferred that the amount of C6-extractables shall be equal or lower than 2.6 wt%, more preferably equal or lower than 2.4 wt%. It is in particular preferred that the film of the present invention has a tear resistance in machine direction (WMD) determined by ISO 6383-2 of lower than 20 N/rnm, more preferably of lower than 15 N/mm, most preferably of lower than 12.5 N/mm when measured on 100 µm thick films. More preferably, the inventive film has a WTD/WMD-ratio of more than 2, more preferably of more than 2.3, whereby WTD is the tear-resistance of the film in a transverse direction determined by ISO 6383-2 when measured on 100 um thick films. In addition, it is preferred that the film has a tear-angle (TA) in machine direction of equal or less than 2.5°, more preferably equal or less than 2.2°, most preferably equal or less than 2.0° when measured on 100 µm thick samples after having performed a test according to ISO 6383-2. Moreover, it is preferred that the film has tear angle (TA) in transverse direction of less than 4.5°, more preferably less than 4.0° when measured on 100 µm thick samples after having performed a test according to ISO 6383-2. Further, it is preferred that the film has a haze of lower than 21%, more preferably lower than 18%, most preferably lower than 15%, determined according to ASTM D 1003-92 when measured on 100 urn thick films. Preferably, the film has a gloss of better than 42%, more preferably better than 48%, most preferably better than 52%, determined according to ISO 2813 when measured on 100 µm thick films. Moreover, the present invention comprises the use of the composition as defined above for producing a cast film or blown film. In particular, it is preferred that the composition and the cast film or blown film as defined above is used for producing a pouch, label film, twist film, form-fill-and-seal (FFS) film and vertical-bag-form-fill-and-seal (VFFS) film. Furthermore, the present invention is related to a process for producing a cast film as defined above comprising the steps of (i) pouring or spreading a solution, hot melt or dispersion of a material onto a temporary carrier, (ii) hardening the material, and (iii) stripping the hardened film from the surface of the carrier, whereby the material is a composition as described above, in particular a composition comprising a. 80 to 95 wt% of a polypropylene matrix with an MFR2 of 1 to 30 g/10min being a homopolymer or a copolymer, which has a comonomer content of less than 3 wt%; b. 5 to 20 wt% of an ethylene-propylene-rubber (EPR) with at least 55 wt% propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and c. 0.0001 to 1 wt% ot an a-nucieating agent. Further, the present invention is related to a process for producing a blown film as described above thereby comprising the steps of (i) blowing up a tube of molten material with air perpendicularly to the upwards direction from a side-fed blown film die; (ii) cooling it down with air from the outside on a cooling ring; (iii) folding it and guiding it over deflector rolls onto the winder wherein the material is a composition as defined above, in particular a composition comprising a) 80 to 95 wt% of a polypropylene matrix with an MFR2 of 1 to 30 g/10 min being a homopolymer or a copolymer, which has a comonomer content of less than 3 wt%; b) 5 to 20 wt% of ethylene-propylene rubber (EPR) with at least 55 wt% propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and c) 0.0001 to 1 wt% of an alpha-nucleating agent. Alternatively, the blown films may be produced by tubular quench technology with water cooling. The propylene polymer blends of the present invention are preferably produced by combining the propylene polymer A in the form of powder or granules, the elastomeric copolymer B, and the α-nucleating agent C in a melt mixing device. Melt mixing devices suited for this process are discontinuous and continuous kneaders, twin screw extruders and single screw extruders with special mixing sections and co-kneaders. The residence time must be chosen such that a sufficiently high degree of homogenisation is achieved. Production of polypropylene matrix A The propylene polymer may be produced by single- or multistage process polymerisation of propylene or propylene and α-olefin and/or ethylene such as bulk polymerisation, gas phase polymerisation, slurry polymerisation, solution polymerisation or combinations thereof using conventional catalysts. A homo- or copolymer can be made either in loop reactors or in a combination of loop and gas phase reactor. Those processes are well known to one skilled in the art. A suitable catalyst for the polymerisation of the propylene polymer is any stereospecific catalyst for propylene polymerisation which is capable of polymerising and copolymerising propylene and comonomers at a temperature of 40 to 110°C and at a pressure from 10 to 100 bar. Ziegler Natta catalysts as well as metallocene catalysts are suitable catalysts. One skilled in the art is aware of the various possibilities to produce propylene homo- and copolymers and will simply find out a suitable procedure to produce suitable polymers which are used in the present invention. Production of ethylene-propylene rubber An ethylene-propylene-rubber (B) may be produced by known polymerisation processes such as solution, suspension and gas-phase polymerisation using conventional catalysts. Ziegler Natta catalysts as well as metallocene catalysts are suitable catalysts. A widely used process is the solution polymerisation. Ethylene, propylene and catalyst systems are polymerised in an excess of hydrocarbon solvent. Stabilisers and oils, if used, are added directly after polymerisation. The solvent and unreacted monomers are then flashed off with hot water or steam, or with mechanical devolatilisation. The polymer, which is in crumb form, is dried with dewatering in screens, mechanical presses or drying ovens. The crumb is formed into wrapped bales or extruded into pellets. The suspension polymerisation process is a modification of bulk polymerisation. The monomers and catalyst system are injected into the reactor filled with propylene. The polymerisation takes place immediately, forming crumbs of polymer that are not soluble in the propylene. Flashing off the propylene and comonomer completes the polymerisation process. The gas-phase polymerisation technology consists of one or more vertical fluidised beds. Monomers and nitrogen in gas form along with catalyst are fed to the reactor and solid product is removed periodically. Heat of reaction is removed through the use of the circulating gas that also serves to fluidise the polymer bed. Solvents are not used, thereby eliminating the need for solvent stripping, washing and drying. The production of ethylene propylene rubber (B) is also described in detail in e.g. US 3,300,459, US 5,919,877, EP 0 060 090 Al and in a company publication by EniChem "DUTRAL, Ethylene-Propylene Elastomers" , pages 1-4(1991). Alternatively, ethylene-propylene rubber (B), which are commercially available and which fulfil the indicated requirements, can be used. Alternatively, polymers A and B may be produced in a series of reactors, i.e. starting with the production of polymer A in a loop reactor and transferring the product into a gas phase reactor, where copolymer B is polymerised. It is additionally preferred that the films are oriented by monoaxial or biaxial orientation processes. In this way the tearability can be enhanced even further, especially beyond that of standard block-copolymers. In another embodiment the polymer composition can be coextruded to afford a multi-layered film. The main layer thereby preferably comprises the described polymer composition, while one or more outside layers can be added. It is preferred that the outside layers have the same or a lower tearability. Exploiting this arrangement leads to highly tearable films. The outside layer can also be a thin layer of an especially transparent RACO (random copolymer)film. Description of measurement methods MFR The melt flow rates were measured under a load of 2.16 kg at 230°C. The melt flow rate is that quantity of polymer in grams which the test apparatus standardized to ISO 1133 extrudes within 10 minutes at a temperature of 230°C under a load of 2.16 kg. Intrinsic Viscosity Intrinsic viscosity was measured according to DIN ISO 1628-1 (October 1999) in Decalin at 135°C. Gloss Gloss was determined according to ISO 2813 on 100 urn thick films at an angle of 20°. Haze Haze was determined according to ASTM D 1003-92 on 50 and 100 µm thick films. C6-solubles C6-solubles were determined according to FDA-HHS 177.1520 where 2.5 g of the sample are extracted at 50°C with 11 n-hexane in a Soxhlet apparatus for 24h. Tear Resistance Tear resistance was determined at room temperature on 75630.1 mm or 75630.05 mm samples with a precut slit of 20 mm according to ISO 6383-2 (Elmendorf test). The force required to tear the specimen completely along its length was used to calculate the tear resistance. Tear whitening Tear whitening was determined on the fractured samples used to measure the tear resistance according to an internal Borealis method. It has been assessed with a ruler and rationalized with marks: 0 corresponds to no tear whitening at all, 1 to a tear whitening mm (0.5 mm excluded), 3 to a tear whitening in between 0.5-1.0 mm (1.0 mm excluded), 4 to a tear whitening in between 1.0-2.0 mm (2.0 mm excluded), 5 to a tear whitening above 2.0 mm (2 mm included). Tear Plasticity Tear plasticity was determined on the fractured samples used to measure the tear resistance according to an internal Borealis method. It has been assessed with a ruler and rationalized with marks: 0 correspond to no plasticity at all, 1 to a localized damage near the crack which size is localized in a zone of 1-2 mm around the main crack (2 mm excluded), 3 to a damage localized in a zone of 2-5 mm around the main crack (5 mm excluded), 4 to a damage localized in a zone of 5-10 mm around the main crack (10 mm excluded), 5 to a damage localized in a zone of > 10 mm around the main crack Tear Angle Tear angle was determined on the fractured samples used to measure the tear resistance according to an internal Borealis method. It corresponds to the deviation of the crack towards a straight propagation. It has been measured with a protractor. Dart Drop Impact Dart Drop Impact (DDI) was determined according to ISO 7765-1 at room temperature. The energy (here expressed in form of weight in g) that causes films to fail under specified conditions of impact of a free-falling dart from a height of 660 mm that would result in 50% failure of the specimen is determined (F50). 20 specimens were tested for each weight. Production of films Cast films were produced: A) on a single screw extruder with a barrel diameter of 30 mm and a slot die of 200 x 0.5 mm in combination with a chill- and a take up-roll. Melt temperature was 260 °C in the die; the chill-roll was kept at 15 °C and the take-up roll at 15 °C. The film thickness was adjusted through the ratio between extruder output (4,5 kg/h) and takeoff speed (10,5 m/min), B) on a single screw extruder with a barrel diameter of 60 mm and a slot die of 800 x 0.9 mm in combination with a chill- and a take up-roll. Melt temperature was 250 °C in the die; the chill-roll was kept at 30 °C and the take-up roll at 22 °C. A film thickness of 50 urn was adjusted through the ratio between extruder output (60 kg/h) and takeoff speed (30 m/min). Blown films were produced on a single screw extruder with a barrel diameter of 60 mm and a tubular die of 200 mm diameter x 1.2 mm die gap. Melt temperature was 190 °C in the die; the cooling air was kept at 15°C internal and external of the film bubble. A film thickness of 50 µm was adjusted through the ratio between extruder output (60 kg/h), blow up ratio (2:1) takeoff speed (20 m/min). Examples Preparation of polymers A The propylene polymers A1-A4 and A6 used for the present invention were prepared according to the following procedure: Raw Materials: Hexane dried over molecular sieve (3/10A) TEAL: 93 % from Sigma-Aldrich Donor: Dicyclopentyldimethoxysilane: ex Wacker Chemie (99%). N2: supplier AGA, quality 5.0; purification with catalyst BASF R0311, catalyst G132 (CuO/ZNO/C), molecular sieves (3/10A) and P2O5. Propylene: polymerisation grade Hydrogen: supplier AGA, quality 6.0 The catalyst ZN104 is commercially available from Basell. Sandostab P-EPQ is commercially available from Clariant. A 5 1 autoclave reactor has been purified by mechanical cleaning, washing with hexane and heating under vacuum/N2 cycles at 160 °C. After testing for leaks with 30 bar N2 over night reactor has been vacuumed and filled with 1110 g propylene by weighing and 8 nl H2 by pressure monitoring from a 50 1 steel cylinder. 10 mg of ZN104-catalyst are activated for 10 minutes with a mixture of Triethylaluminium (TEA1; solution in hexane lmol/1) and Dicyclopentyldimethoxysilane as donor (0.3 mol/1 in hexane) - in a molar ratio of 5 after a contact time of 5 min - and 10 ml hexane in a catalyst feeder. The molar ratio of TEA1 and Ti of catalyst is 250. After activation the catalyst is spilled with 300 g propylene into the stirred reactor with a temperature of 23 °C. Stirring speed is hold at 250 rpm. After 6 min prepolymerisation at 23 °C temperature is increased to 70 °C in about 14 min. After holding that temperature for 1 hour polymerisation is stopped by flashing propylene and cooling to room temperature. After spilling the reactor with N2 the homopolymer powder is transferred to a steel container and stabilized with 0.1 wt% of Sandostab P-EPQ and 0.2 wt% of Ionol in acetone and dried over night in a hood and additionally for 2 hours at 50 °C under vacuum. The amount of polymer powder (A3) was 113 g and the MFR (230 °C, 2.16 kg) of the powder was 5 g/10 min. Procedure for random copolymer The propylene copolymer A5 used for the present invention was prepared according to the following procedure: Raw Materials: Hexane dried over molecular sieve (3/10A) TEAL: 93 % from Sigma-Aldrich Donor: Dicyclopentyldimethoxysilane: ex Wacker Chemie (99%). N2: supplier AGA, quality 5.0; purification with catalyst BASF R0311, catalyst G132 (CuO/ZNO/C), molecular sieves (3/10A) and P2O5. Propylene: polymerisation grade Ethylene: polymerisation grade Hydrogen: supplier AGA, quality 6.0 Sandostab P-EPQ is commercially available from Clariant. A 5 1 autoclave reactor has been purified by mechanical cleaning, washing with hexane and heating under vacuum/N2 cycles at 160°C. After testing for leaks with 30 bar N2 over night reactor has been vacuumed and filled with 1110 g propylene by weighing and 5 nl H2 by pressure monitoring from a 50 1 steel cylinder. 8 mg of ZN104-catalyst are activated for 10 minutes with a mixture of Triethylaluminiurn (TEA1; solution in hexane lmol/1) and Dicyclopentyldimethoxysilane as donor (0.3 mol/1 in hexane) - in a molar ratio of 25 after a contact time of 5 min - and 10 ml hexane in a catalyst feeder. The molar ratio of TEA1 and Ti of catalyst is 250. After activation the catalyst is spilled with 300 g propylene into the stirred reactor with a temperature of 23 °C. Stirring speed is hold at 350 rpm. After 6 min prepolymerisation at 23 °C temperature is increased to 70 °C in about 14 min. While heating the ethylene flow has been raised continuously up to the final flow of 340 ml/min during the prepolymerisation. After holding a polymerisation temperature of 70°C for 60 min at constant temperature, constant ethylene flow and constant stirrer rotation polymerisation is stopped by stopping the ethylene flow, by flashing propylene and cooling down the reactor to room temperature. After spilling the reactor with N2 the homopolymer powder is transferred to a steel container and stabilized with 0.1 wt% of Sandostab P-EPQ and 0.2 wt% of Ionol in acetone and dried over night in a hood and additionally for 2 hours at 50 °C under vacuum. The amount of polymer powder (A5) was 98 g, the MFR (230 °C, 2.16 kg) of the powder was 3 g/10 min and its C2-content was 4.5 wt%. The following homopolymers and random copolymers were prepared analogously according to the above procedure (Table 1): Preparation of ethylene-propylene rubber (B) The elastomeric copolymers of the present invention were prepared according to the following procedure: A 5 1-reactor (autoclave) filled with about 0.2 barg propylene (polymerisation grade) is pressured up with the required amount of H2 in order to achieve the targeted intrinsic viscosity of the elastomeric copolymer. Then 300 g of propylene are added. 5 mg of a ZN101 (supplied by Basell) catalyst is contacted with 0.3 ml white oil for about 16 hours and then activated for 5 minutes with a mixture of Triethylaluminium (TEA1; solution in hexane 1 mol/1) and an alkoxysilane (Dicyclopentyldimethoxysilan in the examples) as donor (0.3 mol/1 in hexane) - in a molar ratio of 16 using a contact time of 5 min. The molar ratio of TEA1 and Ti of catalyst was 380 and TEA1 concentration in TEAl/donor mixture 12.6 mg/ml hexane. After activation the catalyst is transferred to the reactor by spilling in with 500 g propylene. After 12 min pre-polymerisation at 30 °C a specified amount of ethylene is added to the reactor and the temperature is increased to the target polymerisation temperature (55 °C in the examples). During heating up additional ethylene dosing is started to achieve the target total pressure at the target polymerisation temperature. Total pressure is hold constantly via continuously dosing of ethylene during polymerisation. 30 min after end of prepolymerisation the reaction is stopped by flashing of monomers and cooling. The polymer is stabilized with 0.1 wt% of Sandostab P-EPQ and 0.2 wt% of Ionol in acetone and dried over night in a hood and additionally for 2 hours at 50 °C under vacuum. The following elastomeric ethylene-propylene copolymers were prepared according to the above procedure(s), except that H2 and ethylene amounts were varied to achieve different intrinsic viscosities and comonomer concentrations. They are reported in Table 3. The amounts of each component and the results of the measurements are shown in Tables 4 and 5. Tests were performed on 100 µm thick cast films obtained according to method A. In addition, cast and blown films of 50 µm thickness of E1 and CE1 were tested to assess the difference of the different technologies. Results are listed in Table 6. A remarkable DDI performance for blown films can be seen with E1. WE CLAIM: 1. A cast film or blown film having a composition comprising: a. 80 to 95 wt% of a polypropylene matrix (A) with an MFR2 of 1 to 30 g/10min being a homopolymer or a copolymer, which has a comonomer content of less than 3 wt%; b. 5 to 20 wt% of an ethylene-propylene-rubber (EPR) (B) with at least 55 wt% propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and c. 0.0001 to 1 wt% of an α-nucleating agent. 2. A film as claimed in claim 1, wherein the comonomer is ethylene. 3. A film as claimed in claim 1 or 2, wherein at least one α-nucleating agent is selected from the group consisting of sodium benzoate, 1;3;2,4-bis-(3,4-dimethyl-benzylidene)- sorbitol, sodium-2,2'-methylenebis-]4,6-di-tert-butyl-phenyl)-phosphate and hydroxybis-(2, 4,8, 10-tetra-tert-butyl-6-hydroxy-12h-dibenzo-(d, g) (1 ,3,2)-dioxaphosphocin-6-oxidato)- aluminium, or those based on prepolymerisation of the catalyst with monomers like vinylcyclohexane (VCH). 4. A film as claimed in any one of the preceding claims 1 to 3, wherein the polypropylene matrix has a higher intrinsic viscosity (IV) than the ethylene-propylene- rubber (EPR). 5. A film as claimed in any one of the preceding claims,wherein the polypropylene matrix has an intrinsic viscosity (IV) of 1.8 to 4.0 dl/g. 6. A film as claimed in any one of the preceding claims, wherein the ratio (IVEPR /IVmatrix) of the intrinsic viscosity (IV) of the ethylene-propylene rubber (EPR) to the polypropylene matrix is not higher than 0.85. 7. A film as claimed in any one of the preceding claims, wherein the film has C6- extractables equal or lower than 2.6 wt%. 8. A film as claimed in any one of the preceding claims, wherein the composition has an MFR2 of at least 2.0 g/10min. 9. A film as claimed in any one of the preceding claims, wherein the film has a thickness of 5 to 200 µm. 10. A film as claimed in any one of the preceding claims, wherein the film has a tear resistance in the machine direction (WMD) determined by ISO 6383-2 of lower than 20 N/mm when measured on 100 µm thick samples. 11. A film as claimed in any one of the preceding claims, wherein the film has a WTD/ WMD-ratio of more than 2, whereby WTD is the tear resistance of the film in the transverse direction determined by ISO 6383-2 when measured on 100 µm thick samples. 12. A film as claimed in any one of the preceding claims, wherein the film has a tear angle (TA) in machine direction equal or less than 2.5° so and a tear angle (TA) in transverse direction of less than 4.5° when measured on 100 µm thick samples after having performed a test according to ISO 6383-2. 13. A film as claimed in any one of the preceding claims, wherein the film has a haze of lower than 21 % determined according to ASTM D 1003-92 when measured on 100 µm thick samples. 14. A film as claimed in any one of the preceding claims, wherein the film has a gloss of better than 42 % determined according to ISO 2813 when measured on 100 µm thick samples. 15. Process for producing a cast film as claimed in any one of the preceding claims 1 to 14, comprising the steps of: i) pouring or spreading a solution, hot-melt or dispersion of a material onto a temporary carrier ii) hardening the material, and iii) stripping the hardenedfilm from the surface of the carrier whereby the material is a composition comprising a. 80 to 95 wt% of a polypropylene matrix with an MFR2 of 1 to 30 g/10min being a homopolymer or a copolymer, which has a comonomer content of less than 3 wt%; b. 5 to 20 wt% of an ethylene-propylene-rubber (EPR) with at least 55 wt% propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and c. 0.0001 to 1 wt% of an α-nucleating agent. 16. Process for producing a blown film as claimed in any one of the preceding claims 1 to 14, comprising the steps of: (i) blowing up a tube of molten material with air perpendicularly to the upwards direction from a side-fed blown film die; (ii) cooling it down with air from the outside on a cooling ring; (iii) folding it and guiding it over deflector roils onto the winder wherein the material is a composition comprising: a. 80 to 95 wt% of a polypropylene matrix with an MFR2 of 1 to 30 g/10min being a homopolymer or a copolymer, which has a comonomer content of less than 3 wt%; b. 5 to 20 wt% of an ethylene-propylene-rubber (EPR) with at least 55 wt% propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and c. 0.0001 10 1 wt% of an a-nucleating agent. 17. Process as claimed in claim 15 or 16, wherein the composition is further defined by anyone of the claims 2 to 8. ABSTRACT A CAST OR BLOWN TRANSPARENT EASY TEARABLE FILM AND PROCESS OF MANUFACTURE THEREOF A cast or blown transparent easy tearable film and process of manufacture thereof are disclosed. The cast film or blown film has a composition comprising 80 to 95 wt% of a polypropylene matrix (A) with an MFR2 of 1 to 30 g/10min being a homopolymer or a copolymer, which has a comonomer content of less than 3 wt%, 5 to 20 wt% of an ethylene-propylene-rubber (EPR) (B) with at least 55 wt% propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and 0.0001 to 1 wt% of an α-nucleating agent.

Full Text

The present invention relates to a cast film or blown film having a high
transparency, easy tear features and low extractables. Furthermore, the
invention is related to a process for making the films as well as to the use of a
heterophasic propylene composition for cast films and blown films.
In the recent years there has been an increasing demand of heat-sealed pouches,
in particular in the food industry, for example for rice or fodder for dogs and
cats. A very well-known problem of such filled pouches is their opening.
Often, the pouches can only be opened with a high effort at a predefined
indentation (or perforation or notch) without using tools like knives and
scissors. Another problem is that a manula opening does not lead to a straight
crack in the pouches but to a curved one increasing the risk that the content of
the pouches ooze out unintended. Hence, there is a demand to develop films for
pouches which can be easily opened manually at the notch leading to a straight
crack in the pouch. Described with physical parameters, it means that the tear
energy has to be minimized and that the crack should develop straight in a pre-
defined direction starting from the notch and usually in parallel direction to the
upper side of the pouch. The materials used for such purpose have to be tough
enough to resist impact loading at room or sub-ambient temperatures. Resins
like polypropylene homopolymers and ethylene-propylene random copolymers
which are brittle under severe loading are therefore excluded. Impact
polypropylenes which are known for their high toughness are normally hazy
and tend to develop plasticity when deformed, a property which limits the
propagation of a linear crack through the pouch. Thus, they are no candidates
of choice. Additionally the film shall fulfill certain standards issued by the food
and drug administration (FDA), i.e. inter alia having low C6-extractables.
Certainly the transparency of the film should also be good as the market favors
transparent pouches.

Therefore, it is the object of the present invention to provide a cast film or
blown film having a high transparency, easy tear features and low extractables.
The finding of the present invention is to provide a cast film or a blown film
comprising a composition of a polypropylene matrix and an ethylene-propylene
rubber (EPR) whereby the particles of the ethylene-propylene rubber (EPR) in
the matrix develop a high orientation in one direction when the film is casted or
blown.
Hence, the present invention is related to a cast film or blown film comprising
a composition comprising
a) 80 to 95 wt% of a polypropylene matrix (A) with an MFR2 of 1 to 30
g/10 min being a homopolymer or a copolymer which has a comonomer
content of less than 3 wt%;
b) 5 to 20 wt% of an ethylene-propylene rubber (EPR) (B) with at least 55
wt% propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and
c) 0.0001 to 1 wt% of an alpha-nucleating agent (C).
Surprisingly, it had been found that such a cast film or blown film possesses a
high transparency, low extractables and also very good tear features expressed
in a low tear resistance, low tear whitening, low tear plasticity and a low tear
angle.
Definition of tear features
Tear resistance, tear whitening, tear plasticity and tear angle have been used to
describe the easy-tear performance of the different materials. Tear resistance
(W), also called tear energy in the following, is that energy needed to propagate
a crack in a precut sample at room temperature according to ISO 6383-2. It is
commonly known as Elmendorf test. Tear resistance was determined at room
temperature on 75*63*0.1 mm or 75*63*0.05 mm samples with a precut slit of
20 mm according to ISO 6383-2. The force required to tear the specimen
completely along its length was used to calculate the tear resistance.

Tear whitening (TW), tear plasticity (TP) and tear angle (TA) have been
determined post mortem on the fractured samples used to assess the tear energy
within 48 hours after having performed the Elmendorf test. Values provided in
the following are valid for these fractured samples and correspond to about half
of what would have been measured considering the whole samples (which
consist of two broken halves).
The tear whitening corresponds to the degree of whitening of the area around
the fracture surface. It has been determined with a ruler and rationalized with
marks: 0 correspond to no tear whitening at all, 1 to a tear whitening 2 to a tear whitening in between 0.3-0.5 mm (0.5 mm excluded), 3 to a tear
whitening in between 0.5-1.0 mm (1.0 mm excluded), 4 to a tear whitening in
between 1.0-2.0 mm (2.0 mm excluded), 5 to a tear whitening above 2.0 mm (2
" mm included)"
The tear plasticity corresponds to the size of the damaged area around the
fracture surface. This damaged zone is often called plastic zone. Depending on
the polymer composition it will or won't exhibit whitening. It has been
determined with a ruler and rationalized with marks: 0 correspond to no
plasticity at all, 1 to a localized damage near the crack which size is to a damage localized in a zone of 1-2 mm around the main crack (2 mm
excluded), 3 to a damage localized in a zone of 2-5 mm around the main crack
(5 mm excluded), 4 to a damage localized in a zone of 5-10 mm around the
main crack (10 mm excluded), 5 to a damage localized in a zone of > 10 mm
around the main crack.
The tear angle corresponds to the deviation of the crack towards a straight
propagation. It has been measured with a protractor.
All the above mentioned parameters have to be fulfilled to consider a material
as easy tearable:

Usually the notch (precut) is made in the machine direction, since the energy
needed to propagate the crack is there the lowest. However, if WTD (preferably perfectly adapted as tear direction.
To achieve these very good tear features, it is in particular necessary that the
ethylene-propylene rubber (EPR) particles are expanded in one direction, i.e.
that they are oriented in the direction in which the crack develops. To achieve
this aim, a composition is needed as defined above. Hence the synergistic effect
of all features contributes to a deformation of the ethylene-propylene rubber
(EPR) particles in the propylene matrix leading to the orientation effect, which
is mainly responsible for the good tear features but has also a positive influence
on the transparency and low extractable properties.
An important requirement in this context is the intrinsic viscosity of the
ethylene-propylene rubber (EPR).
The mtrinsic viscosity (IV) is a measure of the capability of a polymer in
solution to enhance the viscosity of the solution. Intrinsic viscosity (IV) is
correlated positively with the polymer molecular weight. The intrinsic viscosity
(IV) is defined as the limiting value of the specific viscosity/concentration ratio
at zero concentration. It thus becomes necessary to find the viscosity at
different concentrations and then extrapolate to zero concentration. The
variation of the viscosity number with concentration depends on the type of
molecules as well as on the solvent. In general, the intrinsic viscosity of linear
macromolecular substances is related to the molecular weight or degree of
polymerization. With linear macromolecules, viscosity number measurements
can provide a method for the rapid determination of molecular weight when the
relationship between viscosity and molecular weight has been established.

The intrinsic viscosity (IV) in this application is measured according to DIN
ISO 1628-1 (October 1999).
Accordingly, if the intrinsic viscosity (IV) of the ethylene-propylene rubber
(EPR) is too high, i.e. higher than 2.5 dl/g, then the film will have a too high
impact strength, which influences the tear resistance negatively, i.e. the tear
energy is rather high. Moreover a high intrinsic viscosity (IV) is also
correlated with rather big particles (with a diameter above 500 nm as observed
on electron microscopy micrographs). Big particles, however, diminish the
transparency of the film. On the other hand, if the intrinsic viscosity (IV) is too
low, i.e. lower than 1.0 dl/g, then a production of the composition is rather
difficult.
It is in particular preferred, that the intrinsic viscosity (IV) is not higher than
2.3 dl/g, more preferably not higher than 2.2 dl/g and most preferably not
higher than 2.1 dl/g. In turn, the lower limit of the intrinsic viscosity (IV) is
preferably not lower than 1.2 dl/g, more preferably not lower than 1.4 dl/g.
Preferred ranges are 1.0 to 2.3 dl/g, more preferably 1.2 to 2.3 dl/g, still more
preferably 1.2 to 2.2 dl/g and most preferably 1.2 to 2.1 dl/g.
Preferably, not only the intrinsic viscosity (IV) of the ethylene-propylene
rubber (EPR) alone should be considered, but also the polypropylene matrix
used. It should be in particular avoided that the ethylene-propylene rubber
(EPR) has a similar intrinsic viscosity (IV) to the polypropylene matrix. A
good elongation of the ethylene-propylene rubber (EPR) is especially achieved
if the intrinsic viscosities of the ethylene-propylene rubber (EPR) particles and
the polypropylene matrix differ to some extent. Therefore to further improve
the orientation effect, it is preferred that the polypropylene matrix has a higher
intrinsic viscosity (IV) than the ethylene-propylene rubber (EPR). This
proportion of the polypropylene matrix and the ethylene-propylene rubber
(EPR) to each other enables a specifically good elongation of the ethylene-
propylene rubber particles in the polypropylene matrix. It has been, in
particular, found out that it is especially preferred that the ratio of the intrinsic

viscosity (IV) of the ethylene-propylene rubber (EPR) to the polypropylene
matrix (IVEPR/IVmatrix) is not higher than 0.85, more preferably not higher than
0.8. Preferably, the polypropylene matrix has an intrinsic viscosity (IV) of 1.8
to 4.0 dl/g, more preferably of 2.0 to 3.5 dl/g.
As stated above the intrinsic viscosity (IV) is of particular relevance in this
application, as it influences the orientation effect needed. On the other hand the
intrinsic viscosity (IV) is an indicator of the molecular weight. A high intrinsic
viscosity (IV) results from a high molecular weight. Another way to express
the molecular weight of a polymer is by way of its melt flow rate (MFR). The
melt flow rate mainly depends on the average molecular weight. This is due to
the fact that long molecules render the material a lower flow-tendency than
short molecules. An increase in molecular weight means a decrease in the
MFR-value. The melrflow rate (RFR) is measured in g/10 min of the polymer
discharged through a defined dye under specified temperature and pressure
conditions and the measure of viscosity of the polymer which, in turn, for each
type of polymer is mainly influenced by its molecular weight but also by its
degree of branching. The melt flow rate measured under a load of 2.16 kg (ISO
1133) is denoted as MFR2. Hence as both measuring methods are interlinked
by the molecular weight of the polymer, also the melt flow rate (MFR) has to
be carefully considered.
Therefore it is required, that the polypropylene matrix shall have a specific
melt flow rate (MFR). If the melt flow rate MFR2 is too low (high molecular
weight polymer matrix), i.e. lower than 1 g/10min, then, the easy tear features
are far from target due to the high ductility of the matrix which promotes
plastic deformation. Hence, the polypropylene matrix shall have an MFR2 of
not lower than 1 g/lOmin, more preferably not lower than 1.5 g/lOmin. On the
other hand, if the MFR2 is too high, i.e. higher than 30 g/lOmin, then the
polypropylene matrix has inferior transparency and can not easily been
processed. Moreover a too high melt flow rate (MFR2) of the polypropylene
matrix boosts the particle size of the ethylene-propylene rubber (EPR) which is

also detrimental for the orientation effect as well as for the transparency of the
film. It is in particular preferred, that the MFR2 of the polypropylene matrix is
not higher than 20 g/10 min, more preferably not higher than 10 g/10min.
In addition it is preferred, that the composition has a MFR2 of at least 1.5 g/10
min, more preferably of at least 2 g/lOmin.
The type of polypropylene matrix is not restricted to a specific one, as long as
the matrix fulfills the above mentioned requirements. Hence, each
homopolymer or copolymer can be used. In case a copolymer is used, the
comonomer content, however, shall be less than 3 wt%, otherwise the film gets
too ductile affecting negatively the easy tear features. Preferably, the
comonomer is ethylene.
The choice of ethylene-propylene rubber (EPR) must conform with the
orientation requirement and the transparency targeted. Hence an ethylene-
propylene rubber (EPR) is needed having a high propylene amount, i.e. a
propylene amount of at least 55 wt% in the rubber. More preferably the amount
of propylene in the ethylene-propylene rubber (EPR) is at least 58 wt%, more
preferably at least 60 wt%.
Moreover to achieve good tear features the weight ratio of the polypropylene
matrix and the ethylene-propylene rubber (EPR) must be kept in a specific
range. Accordingly, the composition does not have more than 20 wt% of the
ethylene-propylene rubber (EPR), otherwise the film will be too soft and a
linear crack cannot be guaranteed anymore. Therefore the amount of
polypropylene matrix must range from 80 to 95 wt%, preferably in the range of
82 to 93 wt%. In turn, the ethylene-propylene rubber (EPR) must be in the
range of 5 to 20 wt%, preferably in the range of 7 to 18 wt%.
To achieve the desired properties of the present invention, it has been further
found out, that also the film must have a high cristallinity. A highly structured
(crystal) polymer has improved optical and mechanical properties, i.e. a good
tear performance expressed by a low tear energy.

Therefore the composition employed must comprise an alpha-nucleating agent
in the amount of 0.0001 to 1 wt%, preferably in the amount of 0.001 to 0.5
wt%.
Alpha-nucleating agents of polypropylene are substances with the ability to act
as substrates for crystal formation by epitaxy thus increasing the number of
nuclei of the system. Thereby the nucleating agents improve the crystallization
behavior in processing, i.e. decreasing the cycle time or increasing the line
speed, increase the crystallinity in the final product and, additionally, improve
the optical and mechanical properties in terms of improved stiffness and here of
lower tear energy.
Any suitable alpha-nucleating agent known in the art can be used. However, it
is preferred to use at least one alpha-nucleating agent selected from the group
consisting of sodium benzoate, l,3:2,4-bis-(3,4-dimethyl-benzylidene)-sorbitol,
sodium-2,2l-methylenebis-(4,6-di-tert-butyl-phenyl)-phosphate and
hydroxybis-(2,4,8,10-tetra-tert-butyl-6-hydroxy-12h-dibenzo-(d,g)( 1,3,2)-
dioxaphosphocin-6-oxidato)-aluminium. A further a-nucleation method, herein
referred to as "BNT", is a special reactor technique, where the catalyst is
prepolymerised with monomers like vinylcyclohexane (VCH). This method is
described in greater detail in e.g. EP 0 316 187 A2. For the purpose of this
invention "BNT" is referred to as a-nucleating agent.
Preferably, the thickness of the film should not be too high since otherwise a
significant loss in transparency will be the effect. Therefore, it is preferred that
the film has a thickness of 5 to 200 µm, more preferably of 10 to 150 µm.
Preferably, the film shall have only few C6-extractables measured according to
FDA-HHS 177.1520 where 2.5g of the sample are extracted at 50°C with 1 1
hexane in a Soxhlet apparatus for 24 h. It is in particular preferred that the
amount of C6-extractables shall be equal or lower than 2.6 wt%, more
preferably equal or lower than 2.4 wt%.

It is in particular preferred that the film of the present invention has a tear
resistance in machine direction (WMD) determined by ISO 6383-2 of lower than
20 N/rnm, more preferably of lower than 15 N/mm, most preferably of lower
than 12.5 N/mm when measured on 100 µm thick films.
More preferably, the inventive film has a WTD/WMD-ratio of more than 2, more
preferably of more than 2.3, whereby WTD is the tear-resistance of the film in a
transverse direction determined by ISO 6383-2 when measured on 100 um
thick films.
In addition, it is preferred that the film has a tear-angle (TA) in machine
direction of equal or less than 2.5°, more preferably equal or less than 2.2°,
most preferably equal or less than 2.0° when measured on 100 µm thick
samples after having performed a test according to ISO 6383-2. Moreover, it is
preferred that the film has tear angle (TA) in transverse direction of less than
4.5°, more preferably less than 4.0° when measured on 100 µm thick samples
after having performed a test according to ISO 6383-2.
Further, it is preferred that the film has a haze of lower than 21%, more
preferably lower than 18%, most preferably lower than 15%, determined
according to ASTM D 1003-92 when measured on 100 urn thick films.
Preferably, the film has a gloss of better than 42%, more preferably better than
48%, most preferably better than 52%, determined according to ISO 2813
when measured on 100 µm thick films.
Moreover, the present invention comprises the use of the composition as
defined above for producing a cast film or blown film. In particular, it is
preferred that the composition and the cast film or blown film as defined above
is used for producing a pouch, label film, twist film, form-fill-and-seal (FFS)
film and vertical-bag-form-fill-and-seal (VFFS) film.
Furthermore, the present invention is related to a process for producing a cast
film as defined above comprising the steps of

(i) pouring or spreading a solution, hot melt or dispersion of a material onto
a temporary carrier,
(ii) hardening the material, and
(iii) stripping the hardened film from the surface of the carrier, whereby the
material is a composition as described above, in particular a composition
comprising
a. 80 to 95 wt% of a polypropylene matrix with an MFR2 of 1 to 30
g/10min being a homopolymer or a copolymer, which has a comonomer
content of less than 3 wt%;
b. 5 to 20 wt% of an ethylene-propylene-rubber (EPR) with at least 55 wt%
propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and
c. 0.0001 to 1 wt% ot an a-nucieating agent.
Further, the present invention is related to a process for producing a blown film
as described above thereby comprising the steps of
(i) blowing up a tube of molten material with air perpendicularly to the
upwards direction from a side-fed blown film die;
(ii) cooling it down with air from the outside on a cooling ring;
(iii) folding it and guiding it over deflector rolls onto the winder
wherein the material is a composition as defined above, in particular a
composition comprising
a) 80 to 95 wt% of a polypropylene matrix with an MFR2 of 1 to 30 g/10
min being a homopolymer or a copolymer, which has a comonomer
content of less than 3 wt%;
b) 5 to 20 wt% of ethylene-propylene rubber (EPR) with at least 55 wt%
propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and
c) 0.0001 to 1 wt% of an alpha-nucleating agent.

Alternatively, the blown films may be produced by tubular quench technology
with water cooling.
The propylene polymer blends of the present invention are preferably produced
by combining the propylene polymer A in the form of powder or granules, the
elastomeric copolymer B, and the α-nucleating agent C in a melt mixing
device.
Melt mixing devices suited for this process are discontinuous and continuous
kneaders, twin screw extruders and single screw extruders with special mixing
sections and co-kneaders. The residence time must be chosen such that a
sufficiently high degree of homogenisation is achieved.
Production of polypropylene matrix A
The propylene polymer may be produced by single- or multistage process
polymerisation of propylene or propylene and α-olefin and/or ethylene such as
bulk polymerisation, gas phase polymerisation, slurry polymerisation, solution
polymerisation or combinations thereof using conventional catalysts. A homo-
or copolymer can be made either in loop reactors or in a combination of loop
and gas phase reactor. Those processes are well known to one skilled in the art.
A suitable catalyst for the polymerisation of the propylene polymer is any
stereospecific catalyst for propylene polymerisation which is capable of
polymerising and copolymerising propylene and comonomers at a temperature
of 40 to 110°C and at a pressure from 10 to 100 bar. Ziegler Natta catalysts as
well as metallocene catalysts are suitable catalysts.
One skilled in the art is aware of the various possibilities to produce propylene
homo- and copolymers and will simply find out a suitable procedure to produce
suitable polymers which are used in the present invention.

Production of ethylene-propylene rubber
An ethylene-propylene-rubber (B) may be produced by known polymerisation
processes such as solution, suspension and gas-phase polymerisation using
conventional catalysts. Ziegler Natta catalysts as well as metallocene catalysts
are suitable catalysts.
A widely used process is the solution polymerisation. Ethylene, propylene and
catalyst systems are polymerised in an excess of hydrocarbon solvent.
Stabilisers and oils, if used, are added directly after polymerisation. The solvent
and unreacted monomers are then flashed off with hot water or steam, or with
mechanical devolatilisation. The polymer, which is in crumb form, is dried
with dewatering in screens, mechanical presses or drying ovens. The crumb is
formed into wrapped bales or extruded into pellets.
The suspension polymerisation process is a modification of bulk
polymerisation. The monomers and catalyst system are injected into the reactor
filled with propylene. The polymerisation takes place immediately, forming
crumbs of polymer that are not soluble in the propylene. Flashing off the
propylene and comonomer completes the polymerisation process.
The gas-phase polymerisation technology consists of one or more vertical
fluidised beds. Monomers and nitrogen in gas form along with catalyst are fed
to the reactor and solid product is removed periodically. Heat of reaction is
removed through the use of the circulating gas that also serves to fluidise the
polymer bed. Solvents are not used, thereby eliminating the need for solvent
stripping, washing and drying.
The production of ethylene propylene rubber (B) is also described in detail in
e.g. US 3,300,459, US 5,919,877, EP 0 060 090 Al and in a company
publication by EniChem "DUTRAL, Ethylene-Propylene Elastomers" , pages
1-4(1991).
Alternatively, ethylene-propylene rubber (B), which are commercially
available and which fulfil the indicated requirements, can be used.

Alternatively, polymers A and B may be produced in a series of reactors, i.e.
starting with the production of polymer A in a loop reactor and transferring the
product into a gas phase reactor, where copolymer B is polymerised.
It is additionally preferred that the films are oriented by monoaxial or biaxial
orientation processes. In this way the tearability can be enhanced even further,
especially beyond that of standard block-copolymers.
In another embodiment the polymer composition can be coextruded to afford a
multi-layered film. The main layer thereby preferably comprises the described
polymer composition, while one or more outside layers can be added. It is
preferred that the outside layers have the same or a lower tearability. Exploiting
this arrangement leads to highly tearable films. The outside layer can also be a
thin layer of an especially transparent RACO (random copolymer)film.
Description of measurement methods
MFR
The melt flow rates were measured under a load of 2.16 kg at 230°C. The melt
flow rate is that quantity of polymer in grams which the test apparatus
standardized to ISO 1133 extrudes within 10 minutes at a temperature of 230°C
under a load of 2.16 kg.
Intrinsic Viscosity
Intrinsic viscosity was measured according to DIN ISO 1628-1 (October 1999)
in Decalin at 135°C.
Gloss
Gloss was determined according to ISO 2813 on 100 urn thick films at an angle
of 20°.

Haze
Haze was determined according to ASTM D 1003-92 on 50 and 100 µm thick
films. C6-solubles
C6-solubles were determined according to FDA-HHS 177.1520 where 2.5 g of
the sample are extracted at 50°C with 11 n-hexane in a Soxhlet apparatus for
24h.
Tear Resistance
Tear resistance was determined at room temperature on 75*63*0.1 mm or
75*63*0.05 mm samples with a precut slit of 20 mm according to ISO 6383-2
(Elmendorf test). The force required to tear the specimen completely along its
length was used to calculate the tear resistance.
Tear whitening
Tear whitening was determined on the fractured samples used to measure the
tear resistance according to an internal Borealis method. It has been assessed
with a ruler and rationalized with marks: 0 corresponds to no tear whitening at
all, 1 to a tear whitening mm (0.5 mm excluded), 3 to a tear whitening in between 0.5-1.0 mm (1.0 mm
excluded), 4 to a tear whitening in between 1.0-2.0 mm (2.0 mm excluded), 5
to a tear whitening above 2.0 mm (2 mm included).
Tear Plasticity
Tear plasticity was determined on the fractured samples used to measure the
tear resistance according to an internal Borealis method. It has been assessed
with a ruler and rationalized with marks: 0 correspond to no plasticity at all, 1
to a localized damage near the crack which size is localized in a zone of 1-2 mm around the main crack (2 mm excluded), 3 to a
damage localized in a zone of 2-5 mm around the main crack (5 mm excluded),
4 to a damage localized in a zone of 5-10 mm around the main crack (10 mm
excluded), 5 to a damage localized in a zone of > 10 mm around the main crack

Tear Angle
Tear angle was determined on the fractured samples used to measure the tear
resistance according to an internal Borealis method. It corresponds to the
deviation of the crack towards a straight propagation. It has been measured
with a protractor.
Dart Drop Impact
Dart Drop Impact (DDI) was determined according to ISO 7765-1 at room
temperature. The energy (here expressed in form of weight in g) that causes films to
fail under specified conditions of impact of a free-falling dart from a height of 660
mm that would result in 50% failure of the specimen is determined (F50). 20
specimens were tested for each weight.
Production of films
Cast films were produced:
A) on a single screw extruder with a barrel diameter of 30 mm and a slot die of
200 x 0.5 mm in combination with a chill- and a take up-roll. Melt temperature
was 260 °C in the die; the chill-roll was kept at 15 °C and the take-up roll at
15 °C. The film thickness was adjusted through the ratio between extruder
output (4,5 kg/h) and takeoff speed (10,5 m/min),
B) on a single screw extruder with a barrel diameter of 60 mm and a slot die of
800 x 0.9 mm in combination with a chill- and a take up-roll. Melt temperature
was 250 °C in the die; the chill-roll was kept at 30 °C and the take-up roll at
22 °C. A film thickness of 50 urn was adjusted through the ratio between
extruder output (60 kg/h) and takeoff speed (30 m/min).
Blown films were produced on a single screw extruder with a barrel diameter
of 60 mm and a tubular die of 200 mm diameter x 1.2 mm die gap. Melt
temperature was 190 °C in the die; the cooling air was kept at 15°C internal
and external of the film bubble. A film thickness of 50 µm was adjusted
through the ratio between extruder output (60 kg/h), blow up ratio (2:1) takeoff
speed (20 m/min).

Examples
Preparation of polymers A
The propylene polymers A1-A4 and A6 used for the present invention were
prepared according to the following procedure:
Raw Materials:
Hexane dried over molecular sieve (3/10A)
TEAL: 93 % from Sigma-Aldrich
Donor: Dicyclopentyldimethoxysilane: ex Wacker Chemie (99%).
N2: supplier AGA, quality 5.0; purification with catalyst BASF R0311, catalyst
G132 (CuO/ZNO/C), molecular sieves (3/10A) and P2O5.
Propylene: polymerisation grade
Hydrogen: supplier AGA, quality 6.0
The catalyst ZN104 is commercially available from Basell.
Sandostab P-EPQ is commercially available from Clariant.
A 5 1 autoclave reactor has been purified by mechanical cleaning,
washing with hexane and heating under vacuum/N2 cycles at 160 °C. After
testing for leaks with 30 bar N2 over night reactor has been vacuumed and
filled with 1110 g propylene by weighing and 8 nl H2 by pressure monitoring
from a 50 1 steel cylinder.
10 mg of ZN104-catalyst are activated for 10 minutes with a mixture of
Triethylaluminium (TEA1; solution in hexane lmol/1) and
Dicyclopentyldimethoxysilane as donor (0.3 mol/1 in hexane) - in a molar ratio
of 5 after a contact time of 5 min - and 10 ml hexane in a catalyst feeder. The
molar ratio of TEA1 and Ti of catalyst is 250. After activation the catalyst is
spilled with 300 g propylene into the stirred reactor with a temperature of
23 °C. Stirring speed is hold at 250 rpm. After 6 min prepolymerisation at
23 °C temperature is increased to 70 °C in about 14 min. After holding that

temperature for 1 hour polymerisation is stopped by flashing propylene and
cooling to room temperature.
After spilling the reactor with N2 the homopolymer powder is transferred to a
steel container and stabilized with 0.1 wt% of Sandostab P-EPQ and 0.2 wt%
of Ionol in acetone and dried over night in a hood and additionally for 2 hours
at 50 °C under vacuum.
The amount of polymer powder (A3) was 113 g and the MFR (230 °C, 2.16 kg)
of the powder was 5 g/10 min.
Procedure for random copolymer
The propylene copolymer A5 used for the present invention was prepared
according to the following procedure:
Raw Materials:
Hexane dried over molecular sieve (3/10A)
TEAL: 93 % from Sigma-Aldrich
Donor: Dicyclopentyldimethoxysilane: ex Wacker Chemie (99%).
N2: supplier AGA, quality 5.0; purification with catalyst BASF R0311, catalyst
G132 (CuO/ZNO/C), molecular sieves (3/10A) and P2O5.
Propylene: polymerisation grade
Ethylene: polymerisation grade
Hydrogen: supplier AGA, quality 6.0
Sandostab P-EPQ is commercially available from Clariant.
A 5 1 autoclave reactor has been purified by mechanical cleaning,
washing with hexane and heating under vacuum/N2 cycles at 160°C. After
testing for leaks with 30 bar N2 over night reactor has been vacuumed and
filled with 1110 g propylene by weighing and 5 nl H2 by pressure monitoring
from a 50 1 steel cylinder.

8 mg of ZN104-catalyst are activated for 10 minutes with a mixture of
Triethylaluminiurn (TEA1; solution in hexane lmol/1) and
Dicyclopentyldimethoxysilane as donor (0.3 mol/1 in hexane) - in a molar ratio
of 25 after a contact time of 5 min - and 10 ml hexane in a catalyst feeder. The
molar ratio of TEA1 and Ti of catalyst is 250. After activation the catalyst is
spilled with 300 g propylene into the stirred reactor with a temperature of
23 °C. Stirring speed is hold at 350 rpm. After 6 min prepolymerisation at
23 °C temperature is increased to 70 °C in about 14 min. While heating the
ethylene flow has been raised continuously up to the final flow of 340 ml/min
during the prepolymerisation. After holding a polymerisation temperature of
70°C for 60 min at constant temperature, constant ethylene flow and constant
stirrer rotation polymerisation is stopped by stopping the ethylene flow, by
flashing propylene and cooling down the reactor to room temperature.
After spilling the reactor with N2 the homopolymer powder is transferred to a
steel container and stabilized with 0.1 wt% of Sandostab P-EPQ and 0.2 wt%
of Ionol in acetone and dried over night in a hood and additionally for 2 hours
at 50 °C under vacuum.
The amount of polymer powder (A5) was 98 g, the MFR (230 °C, 2.16 kg) of
the powder was 3 g/10 min and its C2-content was 4.5 wt%.

The following homopolymers and random copolymers were prepared
analogously according to the above procedure (Table 1):

Preparation of ethylene-propylene rubber (B)
The elastomeric copolymers of the present invention were prepared according
to the following procedure:
A 5 1-reactor (autoclave) filled with about 0.2 barg propylene (polymerisation
grade) is pressured up with the required amount of H2 in order to achieve the
targeted intrinsic viscosity of the elastomeric copolymer. Then 300 g of
propylene are added.
5 mg of a ZN101 (supplied by Basell) catalyst is contacted with 0.3 ml white
oil for about 16 hours and then activated for 5 minutes with a mixture of
Triethylaluminium (TEA1; solution in hexane 1 mol/1) and an alkoxysilane
(Dicyclopentyldimethoxysilan in the examples) as donor (0.3 mol/1 in hexane) -
in a molar ratio of 16 using a contact time of 5 min. The molar ratio of TEA1
and Ti of catalyst was 380 and TEA1 concentration in TEAl/donor mixture
12.6 mg/ml hexane. After activation the catalyst is transferred to the reactor by

spilling in with 500 g propylene. After 12 min pre-polymerisation at 30 °C a
specified amount of ethylene is added to the reactor and the temperature is
increased to the target polymerisation temperature (55 °C in the examples).
During heating up additional ethylene dosing is started to achieve the target
total pressure at the target polymerisation temperature. Total pressure is hold
constantly via continuously dosing of ethylene during polymerisation. 30 min
after end of prepolymerisation the reaction is stopped by flashing of monomers
and cooling.
The polymer is stabilized with 0.1 wt% of Sandostab P-EPQ and 0.2 wt% of
Ionol in acetone and dried over night in a hood and additionally for 2 hours at
50 °C under vacuum.

The following elastomeric ethylene-propylene copolymers were prepared
according to the above procedure(s), except that H2 and ethylene amounts were
varied to achieve different intrinsic viscosities and comonomer concentrations.
They are reported in Table 3.

The amounts of each component and the results of the measurements are shown
in Tables 4 and 5. Tests were performed on 100 µm thick cast films obtained
according to method A.

In addition, cast and blown films of 50 µm thickness of E1 and CE1 were
tested to assess the difference of the different technologies. Results are listed in
Table 6. A remarkable DDI performance for blown films can be seen with E1.

WE CLAIM:
1. A cast film or blown film having a composition comprising:
a. 80 to 95 wt% of a polypropylene matrix (A) with an MFR2 of 1 to 30
g/10min being a homopolymer or a copolymer, which has a comonomer content of less
than 3 wt%;
b. 5 to 20 wt% of an ethylene-propylene-rubber (EPR) (B) with at least 55 wt%
propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and
c. 0.0001 to 1 wt% of an α-nucleating agent.
2. A film as claimed in claim 1, wherein the comonomer is ethylene.
3. A film as claimed in claim 1 or 2, wherein at least one α-nucleating agent is selected
from the group consisting of sodium benzoate, 1;3;2,4-bis-(3,4-dimethyl-benzylidene)-
sorbitol, sodium-2,2'-methylenebis-]4,6-di-tert-butyl-phenyl)-phosphate and hydroxybis-(2,
4,8, 10-tetra-tert-butyl-6-hydroxy-12h-dibenzo-(d, g) (1 ,3,2)-dioxaphosphocin-6-oxidato)-
aluminium, or those based on prepolymerisation of the catalyst with monomers like
vinylcyclohexane (VCH).
4. A film as claimed in any one of the preceding claims 1 to 3, wherein the
polypropylene matrix has a higher intrinsic viscosity (IV) than the ethylene-propylene-
rubber (EPR).
5. A film as claimed in any one of the preceding claims,wherein the polypropylene
matrix has an intrinsic viscosity (IV) of 1.8 to 4.0 dl/g.
6. A film as claimed in any one of the preceding claims, wherein the ratio (IVEPR
/IVmatrix) of the intrinsic viscosity (IV) of the ethylene-propylene rubber (EPR) to the
polypropylene matrix is not higher than 0.85.

7. A film as claimed in any one of the preceding claims, wherein the film has C6-
extractables equal or lower than 2.6 wt%.
8. A film as claimed in any one of the preceding claims, wherein the composition has
an MFR2 of at least 2.0 g/10min.
9. A film as claimed in any one of the preceding claims, wherein the film has a
thickness of 5 to 200 µm.
10. A film as claimed in any one of the preceding claims, wherein the film has a tear
resistance in the machine direction (WMD) determined by ISO 6383-2 of lower than 20
N/mm when measured on 100 µm thick samples.
11. A film as claimed in any one of the preceding claims, wherein the film has a WTD/
WMD-ratio of more than 2, whereby WTD is the tear resistance of the film in the transverse
direction determined by ISO 6383-2 when measured on 100 µm thick samples.
12. A film as claimed in any one of the preceding claims, wherein the film has a tear
angle (TA) in machine direction equal or less than 2.5° so and a tear angle (TA) in
transverse direction of less than 4.5° when measured on 100 µm thick samples after having
performed a test according to ISO 6383-2.
13. A film as claimed in any one of the preceding claims, wherein the film has a haze of
lower than 21 % determined according to ASTM D 1003-92 when measured on 100 µm
thick samples.

14. A film as claimed in any one of the preceding claims, wherein the film has a gloss
of better than 42 % determined according to ISO 2813 when measured on 100 µm thick
samples.
15. Process for producing a cast film as claimed in any one of the preceding claims 1 to
14, comprising the steps of:
i) pouring or spreading a solution, hot-melt or dispersion of a material onto a
temporary carrier
ii) hardening the material, and
iii) stripping the hardenedfilm from the surface of the carrier whereby the
material is a composition comprising
a. 80 to 95 wt% of a polypropylene matrix with an MFR2 of 1 to 30 g/10min
being a homopolymer or a copolymer, which has a comonomer content of less than 3 wt%;
b. 5 to 20 wt% of an ethylene-propylene-rubber (EPR) with at least 55 wt%
propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and
c. 0.0001 to 1 wt% of an α-nucleating agent.
16. Process for producing a blown film as claimed in any one of the preceding claims 1
to 14, comprising the steps of:
(i) blowing up a tube of molten material with air perpendicularly to the upwards
direction from a side-fed blown film die;
(ii) cooling it down with air from the outside on a cooling ring;
(iii) folding it and guiding it over deflector roils onto the winder wherein the
material is a composition comprising:
a. 80 to 95 wt% of a polypropylene matrix with an MFR2 of 1 to 30 g/10min
being a homopolymer or a copolymer, which has a comonomer content of less than 3 wt%;
b. 5 to 20 wt% of an ethylene-propylene-rubber (EPR) with at least 55 wt%
propylene having an intrinsic viscosity (IV) of 1 to 2.5 dl/g; and

c. 0.0001 10 1 wt% of an a-nucleating agent.
17. Process as claimed in claim 15 or 16, wherein the composition is further defined by
anyone of the claims 2 to 8.

ABSTRACT

A CAST OR BLOWN TRANSPARENT EASY TEARABLE
FILM AND PROCESS OF MANUFACTURE THEREOF
A cast or blown transparent easy tearable film and process of manufacture thereof
are disclosed. The cast film or blown film has a composition comprising 80 to 95 wt% of a
polypropylene matrix (A) with an MFR2 of 1 to 30 g/10min being a homopolymer or a
copolymer, which has a comonomer content of less than 3 wt%, 5 to 20 wt% of an
ethylene-propylene-rubber (EPR) (B) with at least 55 wt% propylene having an intrinsic
viscosity (IV) of 1 to 2.5 dl/g; and 0.0001 to 1 wt% of an α-nucleating agent.

Documents:

03764-kolnp-2007-abstract.pdf

03764-kolnp-2007-claims.pdf

03764-kolnp-2007-correspondence others.pdf

03764-kolnp-2007-description complete.pdf

03764-kolnp-2007-form 1.pdf

03764-kolnp-2007-form 3.pdf

03764-kolnp-2007-form 5.pdf

03764-kolnp-2007-gpa.pdf

03764-kolnp-2007-international exm report.pdf

03764-kolnp-2007-international search report.pdf

03764-kolnp-2007-pct priority document notification.pdf

03764-kolnp-2007-pct request form.pdf

03764-kolnp-2007-translated copy of priority document.pdf

3764-KOLNP-2007-(13-02-2012)-CORRESPONDENCE.pdf

3764-KOLNP-2007-(23-11-2011)-CORRESPONDENCE.pdf

3764-KOLNP-2007-ABSTRACT 1.1.pdf

3764-KOLNP-2007-AMANDED CLAIMS.pdf

3764-KOLNP-2007-AMANDED PAGES OF SPECIFICATION.pdf

3764-KOLNP-2007-ASSIGNMENT.pdf

3764-KOLNP-2007-ASSIGNMENT1.1.pdf

3764-KOLNP-2007-CORRESPONDENCE OTHERS 1.1.pdf

3764-KOLNP-2007-CORRESPONDENCE.pdf

3764-KOLNP-2007-DESCRIPTION (COMPLETE) 1.1.pdf

3764-KOLNP-2007-EXAMINATION REPORT REPLY RECIEVED.pdf

3764-KOLNP-2007-EXAMINATION REPORT.pdf

3764-KOLNP-2007-FORM 1-1.1.pdf

3764-KOLNP-2007-FORM 18.pdf

3764-KOLNP-2007-FORM 2.pdf

3764-KOLNP-2007-FORM 3-1.1.pdf

3764-KOLNP-2007-FORM 3.pdf

3764-KOLNP-2007-FORM 5.pdf

3764-KOLNP-2007-GPA.pdf

3764-KOLNP-2007-GRANTED-ABSTRACT.pdf

3764-KOLNP-2007-GRANTED-CLAIMS.pdf

3764-KOLNP-2007-GRANTED-DESCRIPTION (COMPLETE).pdf

3764-KOLNP-2007-GRANTED-FORM 1.pdf

3764-KOLNP-2007-GRANTED-FORM 2.pdf

3764-KOLNP-2007-GRANTED-SPECIFICATION.pdf

3764-KOLNP-2007-OTHERS 1.1.pdf

3764-KOLNP-2007-OTHERS.pdf

3764-KOLNP-2007-PA.pdf

3764-KOLNP-2007-PETITION UNDER RULE 137.pdf

3764-KOLNP-2007-REPLY TO EXAMINATION REPORT.pdf

3764-KOLNP-2007-TRANSLATED COPY OF PRIORITY DOCUMENT.pdf

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Patent Number

255725

Indian Patent Application Number

3764/KOLNP/2007

PG Journal Number

12/2013

Publication Date

22-Mar-2013

Grant Date

19-Mar-2013

Date of Filing

04-Oct-2007

Name of Patentee

BOREALIS TECHNOLOGY OY

Applicant Address

P.O. BOX 330, FIN-06101, PORVOO

Inventors:

#	Inventor's Name	Inventor's Address
1	GREIN CHRISTELLE	HARRACHSTRASSE 28, A-4020 LINZ
2	NIEDERSUSS PETER	BLINDENDORF 221, A-4312 RIED/RIEDMARK
3	WOLFSBERGER ANTON	ESCHENWEG 2, A-4210, GALLNEUKIRCHEN

PCT International Classification Number

C08J 5/18,B29C 47/00

PCT International Application Number

PCT/EP2006/004129

PCT International Filing date

2006-05-03

PCT Conventions:

#	PCT Application Number	Date of Convention	Priority Country
1	05 010 360.5	2005-05-12	EUROPEAN UNION