Biaxially oriented polyproylene film having a high surface modulus

DESCRIPTION
Biaxially oriented polypropylene film having a high surface modulus
The invention relates to a biaxially oriented, at least single-ply polypropylene film having a high surface modulus of elasticity, to a process for its production and to its use.
Biaxially oriented polypropylene films are known. The films are generally multilayer films produced by coextrusion by the so-called stenter process.
In this process, the polymers are melted and homogenized in extruders. The melts are filtered and brought together in a slot die, where they are extruded to give the multilayer melt film. The melt film is cast onto a chill roll, where it solidifies to give an unoriented film.
The film is subsequently biaxially oriented by stretching in the longitudinal and transverse directions. After the transverse stretching, the film is cooled to room temperature and trimmed at both edges, the thickness profile is measured, and the film is, if desired, surface treated. The film is subsequently wound up and packaged to give the cut roll ready for the customer.
The properties of the boPP films which are relevant to use are determined principally by the biaxial orientation. boPP films have high mechanical strengths, good dimensional stability at elevated temperature, a sparkling appearance and excellent flat lying as a consequence of an excellent thickness profile.
On the basis of these good properties and excellent processing properties, boPP films are used in a wide variety of applications. The most important market segment is packaging, which accounts for about 70% of the amount produced. In addition, boPP films are used in technical applications. Emphasis should be made of metalization, lamination and use of the film for electrical insulation in the production of capacitors.
boPP films used in the packaging market are further processed principally on the following three processing machines:
on vertical form-fill-seal machines (vffs)
on horizontal form-fill-seal machines (hffs) and
on wrapping machines.
For cost and environmental reasons, the trend is toward higher processing speeds and everlower film thicknesses. In the processing of films on wrapping machines, for example cigarette packs, there is also a desire for the tightest possible wrap appearance without billowing, earing and folding.
The processing of films on hf fs and in particular on vffs machines generally does not give such a tight pack as processing of the film on wrapping machines. On vffs machines, the films are principally converted into tubular bags, into which the contents (foods such as noodles, chips and beans) are poured and the bag is subsequently heat-sealed.
Examples of the processing of films on hffs machines are the packing of snacks, such as chocolate bars and cookies. Here too, the contents are preferably packed loose.
For problem-free processing of the film in these applications, it is necessary that the films have adequate film rigidity S (S=E*d.sup.3, where E=modulus of elasticity of the film, and d=film thickness). In order to achieve stable enclosure of the contents, it is likewise necessary that the rigidity of the film is high. If the film rigidity is too low, the enclosure of the contents is rippled, folds form, the supporting and protecting action of the film is reduced and handling of the pack becomes more difficult.
For attractivity reasons, it is also desirable to find a pack which has adequate shape stability so that it can be transported and stacked without problems.
In the case of the packages mentioned, which result in a rather loose packing of the contents, the rigidity of the film in the machine direction (MD) and the rigidity of the film in the transverse direction (TD) are important. The aim in the production of films for such applications is therefore to produce films having the highest possible surface rigidity S.sub.F. For a constant film thickness, this means that the rigidity based on the thickness should be as high as possible. The high rigidity can only be achieved by improving the surface modulus of elasticity (E.sub.F1 or E.sub.F2) of the film if it is not desired to increase the thickness of the film.
S.sub.F /d.sup.3 =E.sub.MD *E.sub.TD =E.sub.F1 (1)
or
S.sub.F /d.sup.3 =(1/2*(E.sub.MD.sup.2 +*E.sub.TD.sup.2))**1/2=E.sub.F2(2)
Increasing the modulus of elasticity (E modulus) has long been the subject of intensive efforts, because this mechanical property as stated above is directly related to the suitability for use and hence directly determines the processing behavior.
As described in the product surveys from the companies Mobil Plastics Europe and Hoechst AG, for example, the modulus of elasticity in tension (DIN 53 457, ASTM 882) of conventional boPP films in the longitudinal direction is between 2,000 and 2,200 N/mm.sup.2 and that in the transverse direction is between 4,300 and 4,500 N/mm.sup.2, regardless of the thickness.
It is known that, in the case of boPP films, the modulus of elasticity can be increased either by means of process engineering or by means of raw material modifications or a combination of the two possibilities.
A possible method for the production of high-strength polypropylene films is a three-stage or multistage stretching process, as described, for example, in EP-B-0 116 457. However, such a production process has the disadvantage that it requires an additional apparatus for subsequent longitudinal stretching and is therefore very expensive. Moreover, it is very susceptible to breakdowns in the course of production, for example tears in the film.
Furthermore, such subsequently longitudinally stretched films exhibit longitudinal shrinkage which is substantially higher compared with only biaxially stretched films and which as a rule prevents the films from withstanding thermal drying, as is still usual in some cases, for example after application of adhesive materials, without undesirable shrink folds.
The modification of the raw materials used for the production of high-strength polypropylene films with various hydrocarbon resins is described, for example, in U.S. Pat. No. 3,937,762. Such modification of raw materials permits the production of polypropylene films whose mechanical strength in the longitudinal direction is substantially improved compared with films of unmodified raw materials but does not reach the values of subsequently longitudinally stretched films, and shrinkage in the longitudinal direction is likewise relatively high.
EP-A-0 406 642 describes a boPP film having high mechanical strength. The high modulus of elasticity in the longitudinal direction is achieved if the base ply contains 5 to 30% by weight of a hydrocarbon resin and 0.01 to 1.0% by weight of a nucleating agent.
High resin concentrations, as described in the previous examples, lead to problems in film production. In particular, deposits occur after a short time on the screw of the plasticating extruder and on the rolls of the longitudinal stretching unit. Furthermore, the addition of nucleating agents in the stated concentration leads to optical film defects in the form of so-called "specks" and "bubbles", which of course are extremely undesirable. In addition, the regenerated material from such films can no longer be used owing to the tendency to agglomerate in the film production process. Furthermore, the stretching ratios stated in Examples 3 to 6 cannot be realized on any production machine at the conventional speeds with the homopolymer described there. Film constantly tears, particularly during transverse stretching.
Outstanding mechanical properties can be achieved by the combination of the addition of a resin to the raw material used with a subsequent longitudinal stretching process. A corresponding procedure is described in EP-A-0 079 520; moduli of elasticity in the longitudinal direction of 4,000 to 6,000 N/mm.sup.2 are achieved. However, this process, too, has the disadvantage that an expensive subsequent longitudinal stretching process susceptible to faults is required.
U.S. Pat. No. 4,921,749 (=EP-A-0 247 898) describes a sealable boPP film having improved mechanical and optical properties. The sealability of the film and the water vapor and oxygen transmission are also improved. All improvements result from the addition of a low molecular weight resin to the base ply. The amount of resin is between 3 and 30% by weight. The resin has a molecular weight of substantially less than 5,000, preferably less than 1,000, and is, for example, 600. The softening point of the resin is 120 to 140.degree. C.
The object of the present invention was to provide a biaxially oriented polypropylene film which is distinguished by a high surface modulus of elasticity. The disadvantages of the subsequent longitudinal stretching process, such as technical conversions in the production machine, breakdowns due to frequent tearing of the film and high residual shrinkage of the boPP films, are to be avoided. Furthermore, it must be ensured that the regenerated material can be added again in a concentration of 20 to 50% by weight, based on the total weight of the film. Other physical film properties which are required with regard to the use thereof as packaging film must not be adversely affected. The film should have a high gloss, no optical defects in the form of specks or bubbles, good scratch resistance, trouble-free running even with low film thickness on high-speed packaging machines and, in the case of transparent film types, little haze of the film.
This object is achieved according to the invention by a biaxially oriented polypropylene film having at least one base ply which contains polypropylene, wherein the polypropylene used in the base ply is one whose characteristic features are that
the mean isotactic block length of the polypropylene molecule between two structural chain defects is, as a statistical average, greater than 40,
the n-heptane-insoluble fraction of the polypropylene has a chain isotactic index of at least 95%, measured by means of .sup.13 C-NMR spectroscopy,
the ratio of the weight average M.sub.W to the number average M.sub.n as a molecular weight distribution of less than 4 and
the n-heptane-soluble fraction of the polypropylene is less than 1%
and the modulus of elasticity of the base ply in the longitudinal direction is greater than 2,400 N/mm.sup.2 and the modulus of elasticity of the film in the transverse direction is greater than 4,800 N/mm.sup.2.
Preferred embodiments of the invention, are additionally explained below.
According to the invention, the film may be multilayer or single-ply and is then composed only of the base ply described below. For the purposes of the present invention, the base ply is that ply which has the greatest thickness of all plies present. In general, the base ply in multilayer embodiments accounts for at least 40%, preferably 50 to 98%, of the total film thickness. In the multilayer embodiment, the film has, on its base ply, at least one top ply or if required top plies on both sides, which form the outer plies of the film. In a further multilayer embodiment, the film has on its base ply at least one interlayer or if required interlayers on both sides.
The base ply of the film contains in general at least 85-100% by weight, preferably 90-99% by weight, in particular 90-95% by weight, based in each case on the base ply of a propylene polymer described below, which differs substantially in structure from the conventional isotactic propylene polymers which are usually used in the base ply of boPP films. These structural differences can be achieved by the preparation of the propylene polymers by means of novel metallocene catalysts.
A feature of this structural difference is a mean isotactic block length of propylene polymer between two structural chain defects of at least 40, preferably at least 60 and in particular at least 70 propylene units.
The polypropylene used according to the invention may be characterized by means of further parameters which are associated with the particular structure of the polymer.
In addition to a defined mean isotactic block length, the polypropylene is distinguished by a particularly low n-heptane-soluble fraction which is in general less than 1.0% by weight, preferably >0-0.6% by weight and in particular is in the range from 0.5 to 0.005% by weight, based in each case on the weight of the starting polymer.
The n-heptane-insoluble fraction of the propylene polymer is in general highly isotactic. The chain isotactic index, determined by means of .sup.13 C-NMR spectroscopy, of the n-heptane-insoluble fraction is at least 95%, preferably at least 96% and in particular at least 97 to 100%.
The molecular weight distribution is a further suitable parameter for characterizing the polymer structure. It is advantageously comparatively narrow. The ratio of the weight average M.sub.W to the number average M.sub.n is preferably less than 4, especially less than 3. It is in particular in the range from 1.5 to 2.7.
It was completely surprising that, in spite of the extremely low n-heptane-soluble fraction, the high chain isotactic index and the very narrow molecular weight distribution, these novel polypropylenes can readily be stretched to give biaxially oriented polypropylene films. Furthermore, it was very surprising that the films produced from the novel polymer have substantially improved mechanical properties, in particular a high surface modulus of elasticity.
The propylene polymer having the structure described above contains in general at least 90% by weight, preferably 94 to 100% by weight, in particular 98 to 100% by weight, of propylene units. The corresponding comonomer content of not more than 10% by weight or 0 to 6% by weight or 0 to 2% by weight comprises, where present, in general ethylene. The data in % by weight are based in each case on the propylene polymer. The melting point is in general in the range from 140 to 175.degree. C., preferably from 150 to 165.degree. C. and in particular from 155 to 162.degree. C., and the melt flow index (measurement according to DIN 53 735 at 21.6 N load and 230.degree. C.) is 1.0 to 30 g/10 min, preferably from 1.5 to 20 g/10 min and in particular 2.0 to 16 g/10 min.
The polypropylene described above can advantageously be prepared by processes known per se in which metallocene catalysts are used. The preparation of these polyolefins is not the subject of the present invention. The corresponding processes have already been described in EP-A-0 302 424, EP-A-0 336 128 and EP-A-0 336 127 and EP-A-0 576 970, which are hereby incorporated by reference.
It has been found that the structural differences of the polypropylene which are due to the preparation by means of a metallocene catalyst are advantageous for the surface modulus of elasticity of the boPP films produced therefrom. The surface modulus of elasticity of the boPP films comprising metallocene polypropylene is substantially improved compared with boPP films comprising general purpose polypropylene.
The conventional Ziegler-Natta catalysts which are used for the preparation of general purpose PP have a plurality of different polymerization-active centers, each of which prepares a different polymer. This leads to chains having very different molecular weights. In practice, both waxy polymers having chain lengths M.sub.n of less than 10,000 and ultra high molecular weight polymers having an M.sub.n greater than 1,000,000 are obtained. At the same time, the active centers vary in their stereospecificity. The spectrum ranges from completely unspecific centers through syndiospecific centers to isospecific centers, the latter in turn having different isospecificity. This leads to a product mixture comprising atactic polypropylene, syndiotactic polypropylene and isotactic polypropylene having different crystallinities, i.e. having different melting points. Syndiotactic polypropylene leads to warping of the film, atactic polypropylene to exudation (migration) and a reduction in the film hardness and isotactic polypropylene is a material having different melting points, i.e. is not a uniform product.
Small fluctuations in the polymerization conditions lead to fluctuations in the composition of the three characteristic chain types, i.e. once again to a different product which cannot be uniquely characterized.
On the other hand, the metallocene catalysts which are used for the preparation of metallocene PP have a polymerization center which can be uniquely characterized to respective desirable polymer types by variation of the metallocene-ligand sphere. The distribution of the chain length is uniform. The M.sub.w /M.sub.n is small and between 1.7 and 4.0, preferably between 1.8 and 3.0 and very particularly between 2.0 and 2.7 (Schultz-Florey distribution). Furthermore, the active centers also have a uniform stereospecificity, which leads to chains having a uniform melting point or chains having uniform stereospecific structure. Thus, polymer chains which differ only slightly in their mean isotactic block lengths are formed. This is also reflected in a uniform melting point.
The base ply of the film according to the invention can, if required, contain conventional additives in respective effective amounts in addition to the metallocene propylene polymer described above. Conventional additives are antiblocking agents, neutralizing agents, stabilizers, antistatic agents and/or lubricants.
Preferred antistatic agents are alkali metal alkanesulfonates, polyether-modified, i.e. ethoxylated and/or propoxylated polydiorganosiloxanes (polydialkylsiloxanes, polyalkylphenylsiloxanes and the like) and/or the essentially straight-chain and saturated aliphatic, tertiary amines which have an aliphatic radical having 10 to 20 carbon atoms and are substituted by .omega.-hydroxy-(C.sub.1 -C.sub.4)-alkyl groups, N,N-bis-(2-hydroxyethyl)-alkylamines having 10 to 20 carbon atoms, preferably 12 to 18 carbon atoms, in the alkyl radical being particularly suitable. The effective amount of antistatic agent is in the range from 0.05 to 0.5% by weight. Furthermore, glyceryl monostearate is preferably used as an antistatic agent, in an amount of 0.03% to 0.5%.
Suitable antiblocking agents are inorganic additives, such as silica, calcium carbonate, magnesium silicate, aluminum silicate, calcium phosphate and the like, and/or incompatible organic polymers, such as polyamides, polyesters, polycarbonates and the like, preferably benzoguanamine/formaldehyde polymers, silica and calcium carbonate. The effective amount of antiblocking agent is in the range from 0.1 to 2% by weight, preferably 0.1 to 0.8% by weight. The mean particle size is between 1 and 6 .mu.m, in particular 2 and 5 .mu.m, particles having a spherical shape, as described in EP-A-0 236 945 and DE-A-38 01 535, being particularly suitable.
Lubricants are higher aliphatic amides, higher aliphatic esters, waxes and metal soaps as well as polydimethylsiloxanes. The effective amount of lubricant is in the range from 0.01 to 3% by weight, preferably 0.02 to 1% by weight. The addition of higher aliphatic amides in the range from 0.01 to 0.25% by weight to the base ply is particularly suitable. A particularly suitable aliphatic amide is erucamide. The addition of polydimethylsiloxanes in the range from 0.02 to 2.0% by weight is preferred, in particular polydimethylsiloxanes having a viscosity from 5,000 to 1,000,000 mm.sup.2 /s.
The stabilizers used can be the conventional compounds having a stabilizing action for ethylene polymers, propylene polymers and other .alpha.-olefin polymers. The added amount thereof is between 0.05 and 2% by weight. Phenolic stabilizers, alkali metal stearates/alkaline earth metal stearates and/or alkali metal carbonates/alkaline earth metal carbonates are particularly suitable. Phenolic stabilizers in an amount from 0.1 to 0.6% by weight, in particular 0.15 to 0.3% by weight, and with a molecular mass of more than 500 g/mol are preferred. Pentaerythrityl tetrakis-3-(3,5-di-tertiary-butyl-4-hydroxyphenyl)-propionate or 1,3,5-trimethyl-2,4,6-tris(3,5-di-tertiary-butyl-4-hydroxybenzyl)benzene are particularly advantageous.
Neutralizing agents are preferably dihydrotalcite, calcium stearate and/or calcium carbonate having a mean particle size of at most 0.7 .mu.m, an absolute particle size of less than 10 .mu.m and a specific surface area of at least 40 m.sup.2 /g.
In a preferred multilayer embodiment, the polypropylene film according to the invention comprises at least one top ply or if necessary top plies on both sides, composed of polymers of .alpha.-olefins having 2 to 10 carbon atoms. In general, the top ply contains at least 70% by weight, preferably 80 to 100% by weight, in particular 90 to 98% by weight, of the .alpha.-olefinic polymers, based in each case on the weight of the top ply and any additives described above in effective amounts in each case.
Examples of such .alpha.-olefinic polymers are
a propylene homopolymer or
a copolymer of
ethylene and propylene or
ethylene and 1-butylene or
propylene and 1-butylene or
a terpolymer of
ethylene and propylene and 1-butylene or
a mixture of two or more of the stated homo-, co- and terpolymers or
a blend of two or more of the stated homo-, co- and terpolymers, if necessary mixed with one or more of the stated homo-, co- and terpolymers,
in particular a propylene homopolymer or
a random ethylene/propylene copolymer having
an ethylene content of 1 to 10% by weight, preferably 2.5 to 8% by weight, or
a random propylene/1-butylene copolymer having
a butylene content of 2 to 25% by weight, preferably 4 to 20% by weight,
based in each case on the total weight of the copolymer, or
a random ethylene/propylene/1-butylene terpolymer having
an ethylene content of 1 to 10% by weight, preferably 2 to 6% by weight, and
a 1-butylene content of 2 to 20% by weight, preferably 4 to 20% by weight,
based in each case on the total weight of the terpolymer, or
a blend of an ethylene/propylene/1-butylene terpolymer and a propylene/1-butylene copolymer
having an ethylene content of 0.1 to 7% by weight
and a propylene content of 50 to 90% by weight
and a 1-butylene content of 10 to 40% by weight,
based in each case on the total weight of the polymer blend,
being preferred.
The propylene homopolymer used in the top ply has a melting point of 140.degree. C. or higher, preferably 150 to 165.degree. C. Isotactic homopolypropylene having an n-heptanesoluble fraction of 6% by weight or less, based on the isotactic homopolypropylene, is preferred. The homopolymer has in general a melt flow index of 1.0 g/10 min to 20 g/10 min.
The copolymers and terpolymers preferably used in the top ply and described above have in general a melt flow index of 1.5 to 30 g/10 min. The melting point is preferably in the range from 120 to 140.degree. C. The blend of copolymer and terpolymer, described above, has a melt flow index of 5 to 9 g/10 min and a melting point of 120 to 150.degree. C. All melt flow indices stated above are measured at 230.degree. C. and under a force of 21.6 N (DIN 53 735).
In a dull embodiment, the top ply additionally contains a high density polyethylene (HDPE) which is mixed or blended with the top ply polymers described above. The composition and details of the dull top plies are described, for example, in EP 0 563 796 or EP 0 622, which are incorporated herein by reference.
The top ply or plies may also contain the metallocene-catalyzed propylene polymer described above for the base ply.
If required, the additives described above for the base ply, such as antistatic agents, antiblocking agents, lubricants, neutralizing agents and stabilizers, may be added to the top ply or top plies. The stated amounts in these above embodiments are based on the corresponding weight of the top ply. In a preferred embodiment, the top ply or plies contains or contain a combination of antiblocking agent, preferably SiO.sub.2, and lubricant, preferably polydimethylsiloxane.
The film according to the invention comprises at least the base ply described above, preferably at least one top ply. Depending on its intended use, the film may have a further top ply on the opposite side. If required, an interlayer or interlayers can be applied on one or both sides between the base ply and the top ply or plies.
Preferred embodiments of the polypropylene film according to the invention are three-ply. The structure, thickness and composition of a second top ply can be chosen independently of the top ply already present, and the second top ply may likewise contain one of the polymers or polymer mixtures which are described above but which need not be identical to that of the first top ply. The second top ply may, however, also contain other conventional top ply polymers.
The thickness of the top ply or plies is generally greater than 0.1 .mu.m and is preferably in the range from 0.1 to 10 .mu.m, preferably in the range from 0.3 to 3 .mu.m, in particular 0.4 to 1.5 .mu.m, and top plies on both sides may be of equal or different thickness.
The interlayer or interlayers may comprise the .alpha.-olefinic polymers described for the top plies. In a preferred embodiment, the interlayer or interlayers comprises or comprise the propylene polymer described for the base ply. The interlayer or interlayers may contain the conventional additives described for the individual plies. The thickness of the interlayer or interlayers is generally greater than 0.3 .mu.m and is preferably in the range from 1.0 to 15 .mu.m, in particular 1.5-10 .mu.m.
The total thickness of the polypropylene film according to the invention may vary within wide limits and depends on the intended use. It is preferably 4 to 100 .mu.m, in particular 5-60 .mu.m, preferably 6-30 .mu.m. the base ply accounting for about 40 to 100% of the total film thickness.
The invention furthermore relates to a process for producing the polypropylene film according to the invention by the coextrusion process known per se.
In this process, the melt or melts corresponding to the ply or to the individual plies of the film is or are coextruded through a flat die, the film thus obtained is drawn off on one or more rollers for solidification, the film is then biaxially stretched (oriented) and the biaxially stretched film is heat-set and, if required, corona-treated or flame-treated on the surface ply intended for treatment.
The biaxial stretching (orientation) is generally carried out successively, the successive biaxial stretching, in which stretching is first carried out longitudinally (in the machine direction) and then transversely (perpendicular to the machine direction), being preferred.
Firstly, the polymer or the polymer mixture of the individual plies is compressed and liquefied in an extruder, as is usual in the coextrusion process, and the additives added if required may already be present in the polymer or in the polymer mixture. The melts are then simultaneously forced through a slot die (flat film die), and the extruded multilayer film is drawn off on one or more draw-off rollers, during which it cools and solidifies.
The film thus obtained is then stretched longitudinally and transversely relative to the extrusion direction, which leads to orientation of the molecular chains. The longitudinal stretching is expediently carried out with the aid of two rollers running at different speeds corresponding to the desired stretching ratio, and the transverse stretching is carried out with the aid of an appropriate tenter frame. The longitudinal stretching ratios are in the range from 3 to 9, preferably 4.5-8.5. The transverse stretching ratios are in the range from 4 to 12, preferably 5-11, in particular 7 to 10.
The biaxial stretching of the film is followed by its heat setting (heat treatment), the film being kept for about 0.1 to 10 s at a temperature of 100 to 160.degree. C. The film is then wound up in the usual manner by means of a winding device.
It has proved to be particularly advantageous to keep the draw-off roller or rollers, by means of which the extruded film is cooled and solidified, at a temperature of 10 to 100.degree. C., preferably 20-70.degree. C., by a heating and cooling circulation.
The temperatures at which longitudinal and transverse stretching are carried out may be varied within a relatively wide range and depend on the desired properties of the film. In general, longitudinal stretching is preferably carried out at 80 to 170.degree. C., preferably 80-150.degree. C. and transverse stretching preferably at 100 to 200.degree. C., preferably 120-170.degree. C.
After the biaxial stretching, one or both surfaces of the film are preferably corona-treated or flame-treated by one of the known methods. The intensity of treatment is in general in the range from 37 to 50 mN/m, preferably 39 to 45 mN/m.
In an expedient corona treatment, the film is passed between two conductor elements serving as electrodes, such a high voltage, in most cases alternating voltage (about 5 to 20 kV and 5 to 30 kHz), being applied between the electrodes that spray discharges or corona discharges can take place. Due to the spray discharge or corona discharge, the air above the film surface is ionized and reacts with the molecules of the film surface so that polar spots are formed in the essentially nonpolar polymer matrix.
For a flame treatment with a polarized flame (cf. U.S. Pat. No. 4,622,237), a direct electric voltage is applied between a burner (negative pole) and a cooling roller. The level of the applied voltage is between 400 and 3,000 V, preferably in the range from 500 to 2,000 V. Owing to the applied voltage, the ionized atoms experience increased acceleration and impinge at higher kinetic energy on the polymer surface. The chemical bonds within the polymer molecule are more readily broken, and the formation of free radicals proceeds more rapidly. The thermal stress on the polymer is in this case far less than in the standard flame treatment, and films can be obtained in which the sealing properties of the treated side are even better than those of the untreated side.
The film according to the invention is distinguished by outstanding mechanical properties, in particular by a very large surface modulus.
The modulus of elasticity of the base ply, which contains the polypropylene polymer prepared by means of a metallocene catalyst, in the longitudinal direction is greater than 2,400 N/mm.sup.2, preferably greater than 2,500 N/mm.sup.2, and the modulus of elasticity of the base ply in the transverse direction is greater than 4,800 N/mm.sup.2, preferably greater than 5,000 N/mm.sup.2. The surface modulus E.sub.F1 of the film is at least 12*10.sup.6 (N/mm.sup.2).sup.2, referring to formula (1), and at least 3,800 N/mm.sup.2 (E.sub.F2), referring to formula (2).
Surprisingly, the moduli of elasticity of the film can be substantially improved by using polypropylene prepared by means of a metallocene catalyst. The improved moduli of elasticity of the base ply contribute to the improved mechanical properties of the film.
Surprisingly, even with a thickness of less than 20 .mu.m, the films according to the invention are sufficiently rigid to permit processing on the modern high-speed packaging machines. The increased film rigidity may be due to the fact that spatially differently arranged CH.sub.3 groups of this boPP film act as retaining points which prevent sliding of the crystal planes under corresponding load.
The following methods of measurement were used for characterizing the raw materials and the films:
Melt Flow Index
The melt flow index was measured according to DIN 53 735 at 21.6 N load and 230.degree. C.
Melting Point
DSC measurement, maximum of the melting curve, heating rate 20.degree. C./min.
Water Vapor and Oxygen Transmission
The water vapor transmission is determined according to DIN 53 122 Part 2. The oxygen barrier effect is determined according to Draft DIN 53 380 Part 3 at an atmospheric humidity of 53%.
Haze
The haze of the film was measured according to ASTM-D 1003-52.
Gloss
The gloss was determined according to DIN 67 530. The reflector value was measured as an optical characteristic of the surface of a film. Analogously to the standards ASTM-D 523-78 and ISO 2813, the angle of incidence was set at 60 or 85. At the set angle of incidence, a light beam strikes the planar test surface and is reflected or scattered by the latter. The light beams incident on the photoelectronic receiver are indicated as a proportional electric value. The measured value is dimensionless and must be quoted with the angle of incidence.
Surface Tension
The surface tension was determined by means of the so-called ink method (DIN 53 364).
Printability
The corona-treated films were printed on 14 days after their production (short-term evaluation) or 6 months after their production (long-term evaluation). The ink adhesion was evaluated by means of the self-adhesive tape test. The ink adhesion was rated as moderate if little ink could be removed by means of self-adhesive tape and was rated as poor if a substantial amount of ink could be removed.
Tensile Strength, Elongation at Break
The tensile strength and the elongation at break are determined according to DIN 53455.
Modulus of Elasticity
The modulus of elasticity is determined in the longitudinal and transverse direction according to DIN 53 457 or ASTM 882. The surface modulus of elasticity is determined according to formula (1) or formula (2).
Determination of the High-temperature Blocking Characteristics
To measure the high-temperature blocking characteristics, two wooden blocks adhesively bonded to felt on one side and having the dimensions 72 mm.times.41 mm.times.13 mm are wrapped and sealed in the film to be measured. A weight of 200 g is placed on the wooden blocks positioned so that the felt coverings face one another, and this set-up is introduced into a heating oven preheated to 70.degree. C. and is left there for 2 hours. Thereafter, cooling is effected for 30 minutes to room temperature (21.degree. C.), the weight is removed from the wooden blocks and the upper block is pulled off the lower block by means of a mechanical apparatus. The evaluation is effected over 4 individual measurements, from which a maximum pull-off force (measured in N) is then determined. The specification is met if none of the individual measurements is above 5 N.
Molecular Weight Determination
The average molecular weight M.sub.w and M.sub.N (average weight M.sub.w and average number M.sub.n) and the mean inhomogeneity of the molecular mass were determined analogously to DIN 55 672, Part 1, by means of gel permeation chromatography. Instead of THF, ortho-dichlorobenzene was used as the eluant. Since the olefinic polymers to be investigated are not soluble at room temperature, the entire measurement is carried out at an elevated temperature (135.degree. C.).
Isotactic Content
The isotactic content of the homopolymer and also the isotactic content of the film can be characterized approximately by means of the insoluble fraction of the raw material or of the film in a suitable solvent. It has proven expedient to use n-heptane. Usually, a Soxhlet extraction with boiling n-heptane is carried out. In order to obtain good reproducibility, it is expedient to fill the Soxhlet apparatus with a compact instead of granules. The thickness of the compact should not exceed 500 micrometers. For the quantitative determination of the atactic content of the polymer, it is of decisive importance to ensure sufficient extraction time. As a rule, the extraction time is in the range from 8 to 24 hours.
The operational definition of the isotactic content PP.sub.iso in percent is given by the ratio of the weights of the dried n-heptane-insoluble fraction to the sample weight:
PP.sub.iso =100.times.(n-heptane-insoluble fraction/sample weight)
An analysis of the dried n-heptane extract shows that, as a rule, it does not comprise pure atactic propylene polymer. In the extraction, aliphatic and olefinic oligomers, in particular isotactic oligomers, and also possible additives, such as, for example, hydrogenated hydrocarbon resins, are also measured.
Chain Isotactic Index
The isotactic content PP.sub.iso defined above is not sufficient for characterizing the chain isotacticity of the polymer. It proves to be useful to determine the chain isotactic index II of the propylene polymer by means of high-resolution .sup.13 C-NMR spectroscopy, the NMR sample chosen being not the original raw material but its n-heptane-insoluble fraction. To characterize the isotacticity of polymer chains, .sup.13 C-NMR spectroscopic triad isotactic index II (triads) is used in practice.
Determination of the Triad-related Chain Isotactic Index II (triads)
The chain isotactic index II (triads) of the n-heptaneinsoluble content of the polymer and of the film is determined from the .sup.13 C-NMR spectrum of said homopolymer or of said film. The intensities of triad signals which result from the methyl groups with different local environments are compared.
With regard to the evaluation of the .sup.13 C-NMR spectrum, a distinction must be made between two cases:
A) The raw material investigated is a pure propylene homopolymer without a random C.sub.2 content.
B) The raw material investigated is a propylene polymer having a low random C.sub.2 content, referred to below as C.sub.2 -C.sub.3 -copolymer.
Case A:
The chain isotactic index of the homopolymer is determined from its .sup.13 C-NMR spectrum. The intensities of the signals which result from the methyl groups with different environments are compared. In the .sup.13 C-NMR spectrum of a homopolymer, essentially three groups of signals, so-called triads, occur.
1. At a chemical shift of about 21 to 22 ppm, the "mm-triad" occurs and is assigned to the methyl groups having methyl groups directly adjacent on the left and right.
2. At a chemical shift of about 20.2 to 21 ppm, the "mr-triad" occurs and is assigned to the methyl groups having methyl groups directly adjacent on the left or right.
3. At a chemical shift of about 19.3 to 20 ppm, the "rr-triad" occurs and is assigned to the methyl groups without directly adjacent methyl groups.
The intensities of the signal groups assigned are determined as the integral of the signals. The chain isotactic index is defined as follows: ##EQU1## where J.sub.mm, J.sub.mr and J.sub.rr are the integrals of the signal groups assigned.
Case B:
FIG. 1 is a schematically enlarged representation of a .sup.13 C-NMR spectrum of an ethylene/propylene copolymer. The chemical shift of the methyl groups of interest is in the range from 19 to 22 ppm. As can be seen in FIG. 1, the spectrum of the methyl groups can be divided into three blocks. In these blocks, the CH.sub.3 groups appear in triad sequences, whose assignment to the local environments is explained in detail below:
Block 1:
CH.sub.3 groups in the PPP sequence (mm-triad) ##STR1## Block 2: CH.sub.3 groups in the PPP sequence (mr- or rm-triads) ##STR2## and CH.sub.3 groups in the EPP sequence (m-chain): ##STR3## Block 3 CH.sub.3 groups in the PPP sequence (rr-triads): ##STR4## CH.sub.3 groups in an EPP sequence (r-chain): ##STR5## CH3 groups in an EPE sequence: ##STR6##
In the determination of the triad-related chain isotactic index II (triads) of the n-heptane-insoluble content of an ethylene/propylene copolymer, only PPP triads were considered, i.e. only those propylene units which are present between two adjacent propylene units (cf. also EP-B-0 115 940, page 3, lines 48 and 49).
The definition of the triad isotactic index of an ethylene/propylene copolymer is:
II (triads)=100.times.(J.sub.mm /J.sub.ppp)
Calculation of the chain isotactic index of an ethylene/propylene copolymer:
1. J.sub.mm is given by the peak integral of block 1.
2. Calculate the integral (J.sub.total) of all methyl group peaks in blocks 1, 2 and 3.
3. By simple considerations, it is possible to show that J.sub.ppp =J.sub.total -J.sub.EPP -J.sub.EPE.
Sample Preparation and Measurement:
60 to 100 mg of polypropylene are weighed into a 10 mm NMR tube, and hexachlorobutadiene and tetrachloroethane in a ratio of about 1.5:1 are added until a fill height of about 45 mm is reached. The suspension is stored at about 140.degree. C. until (as a rule about one hour) a homogeneous solution has formed. In order to accelerate the dissolution process, the sample is stirred from time to time with a glass rod.
The .sup.13 C-NMR spectrum is recorded at an elevated temperature (as a rule 365 K) under standard measuring conditions (semiquantitatively).
Mean Isotactic Block Length n.sub.iso
The mean isotactic block length n.sub.iso is determined from the .sup.13 C-NMR spectrum according to the formula
n.sub.iso =1+2J.sub.mm /J.sub.mr.
Preparation of the Propylene Polymers

The propylene polymers were prepared with the aid of metallocene catalysts by the polymerization reactions described by way of example below:
EXAMPLE 1
A dry reactor having the capacity of 150 dm.sup.3 was flushed with nitrogen and filled, at 20.degree. C., with 80 dm.sup.3 of a naptha cut having a boiling range of from 100 to 120.degree. C. The gas space was then flushed free from nitrogen by 5 flushing operations with propylene under a pressure of 2 bar and decompression.
After the addition of 50 l of liquid propylene, 64 cm.sup.3 of solution of methylaluminoxane in toluene (corresponding to 100 mmol of Al, molecular weight according to cryoscopic determination 1,000 g/mol) were added and the reactor content was heated to 50.degree. C. Hydrogen content in the gas space of the reactor of 1.2% was established by metering in hydrogen and was subsequently kept constant by further metering during the entire polymerization time (checking on-line by gas chromatography.
20 mg of the metallocene rac-dimethylsilanediylbis-(2-methyl-4,6-diisopropyl-1-indenyl)zirconiumdichloride were dissolved in 16 ml of a solution of methylaluminoxane in toluene (corresponding to 25 mmol of Al) and were added to the reactor.
The reactor was kept at 50.degree. C. for 10 hours by cooling, after which the polymerization was stopped by adding 50 dm.sup.3 (S.T.P.) of CO.sub.2 gas and the polymer formed was separated off from the suspension medium and was dried.
21.9 kg of polymer powder, corresponding to a metallocene activity of 109.5 kg PP/g metallocene*h were obtained. The polymer is characterized by the following further data:
Viscosity VN: 228 cm.sup.3 /g
Average molecular weight M.sub.w : 225 000 g/mol
M.sub.w /M.sub.n : 2.5
Melting point T.sub.m : 150.degree. C.
Melt flow index MFI: 7.0 g/10 min
Mean isotactic block length n.sub.iso : about 80
Isotactic index: about 97.5%
EXAMPLE 2
The polymerization of Example 1 was repeated, but the metallocene rac-dimethylsilanediylbis(2-methyl-4,5-benzo-1-indenyl)zirconium dichloride was used. The polymerization temperature was 60.degree. C., and polymerization was carried out for 6.5 hours. The metallocene activity in this case was 173 kg PP/g metallocene*h. The polymer is characterized by the further data as follows:
Viscosity VN: 258 cm.sup.3 /g
Average molecular weight M.sub.w : 302 000 g/mol
M.sub.w /M.sub.n : 2.3
Melting point T.sub.m : 147.degree. C.
Melt flow index MFI: 4.3 g/10 min
Mean isotactic block length n.sub.iso : about 80
Isotactic index: about 97.5%
EXAMPLE 3
The polymerization of Example 1 was repeated, but 10 mg of the metallocene rac-dimethylsilanediylbis(2-methyl-4-phenyl-1-indenyl)zirconium dichloride were used. The hydrogen concentration in the gas space of the reactor was 1.8% by volume. The metallocene activity was 227 kg PP/g metallocene*h. The polymer is characterized by the further data as follows:
Viscosity VN: 230 cm.sup.3 /g
Average molecular weight M.sub.w : 274 500 g/mol
M.sub.w /M.sub.n : 2.0
Melting point T.sub.m : 160.degree. C.
Melt flow index MFI: 4.0 g/10 min
Mean isotactic block length n.sub.iso : about 100
Isotactic index: about 98%
EXAMPLE 4
The procedure was as in Example 1, but two different hydrogen concentrations were used during the polymerization. First, a hydrogen content of 10% by volume was established in the gas space of the reactor and was kept constant by subsequent metering until the propylene pressure in the reactor had fallen to 6 bar as a result of polymerization of propylene. The hydrogen was then reduced to 1.0% by volume by briefly releasing gas, and the polymerization was continued at this hydrogen concentration.
10 mg of the metallocene rac-dimethylsilanediylbis(2-ethyl-4-phenyl-1-indenyl)zirconium dichloride were dissolved in 16 ml of solution of methylalumoxane in toluene (corresponding to 25 mmol of Al) and were added to the reactor.
16.2 kg of polymer powder, corresponding to a metallocene activity of 162 kg PP/g metallocene*h, were obtained. The polymer is characterized by the following further data:
Viscosity VN: 245 cm.sup.3 /g
Average molecular weight M.sub.w : 358 000 g/mol
M.sub.w /M.sub.n : 3.0
Melting point T.sub.m : 161.degree. C.
Melt flow index MFI: 4.6 g/10 min
Mean isotactic block length n.sub.iso : about 100
Isotactic index: about 98%
Production of the Films
EXAMPLE 5
A transparent, single-ply film having a total thickness of 5 .mu.m was produced by extrusion and subsequent stepwise orientation in the longitudinal and transverse directions. The raw material used for the film was:
99.85% of highly isotactic propylene homopolymer from Hoechst AG
0.15% of stabilizer
The propylene homopolymer was prepared according to Example 3. The production conditions in the individual process steps were:
Extrusion: Temperatures 280.degree. C.
Longitudinal stretching: Temperature: 115.degree. C.
Transverse stretching: Temperature: 160.degree. C. Transverse stretching ratio: 11
Setting: Temperature: 150.degree. C. Convergence: 15%
The film produced in this manner had the properties listed in the table (first line: Example 5).
EXAMPLE 6
A transparent three-ply film having a symmetrical structure and a total thickness of 16 .mu.m was produced by coextrusion and subsequent stepwise orientation in the longitudinal and transverse direction. The top plies each had a thickness of 0.6 .mu.m.
A-base ply:
99.85% by weight of highly isotactic polypropylene from Hoechst AG
0.15% by weight of antistatic agent
The polypropylene of the base raw material was prepared according to Example 3.
B-top plies:
98.77% by weight of a random ethylene/propylene copolymer having a C.sub.2 content of 4.5% by weight
0.33% by weight of an antiblocking agent, having a mean particle size of 2 .mu.m
0.90% by weight of a lubricant
The production conditions in the individual process steps were:
______________________________________Extrusion: Temperatures A-ply: 280.degree. C. B-ply: 280.degree. C.Longitudinal Temperature: 115.degree. C.stretching: Longitudinal stretching ratio: 3.5Transverse Temperature: 160.degree. C.stretching: Transverse stretching ratio: 11Setting: Temperature: 150.degree. C. Convergence: 15%______________________________________
The film produced in this manner had the properties listed in the Table (Example 6).
COMPARATIVE EXAMPLE 1
In comparison with Example 6, a commercial polypropylene, produced by means of a Ziegler-Natta catalyst, from Hoechst AG was used. The n-heptane-soluble fraction of the film had a chain isotactic index of 93%, measured by means of .sup.13 C-NMR spectroscopy. The M.sub.w /M.sub.n was 4.5 and the n-heptane-soluble fraction was 4% by weight.
TABLE__________________________________________________________________________ High- Modulus of Tensile Elongation Friction tempera- elasticity strength at break Shrinkage 14 days tureFilm DIN 532 457 surface DIN 53 455 DIN 53 455 DIN 67 530 Haze after Scratch blockingthick- longitudinal/ modulus longitudinal/ longitudinal/ longitudinal/ ASTM D production resis- character-ness transverse (formula 2) transverse transverse Gloss transverse 100352 B side/ tance istics.mu.m N/mm.sup.2 N/mm.sup.2 N/mm.sup.2 % DIN 67530 % % B' side .DELTA. haze N__________________________________________________________________________E5 5 2600/5400 4240 160/320 125/70 100 1.5/1.2 2.0 0.4/0.4 8 0.5E6 16 2400/4900 3860 145/310 120/65 120 1.6/3.0 1.9 0.22/0.23 23 1.5CE1 16 2200/4100 3290 140/300 160/60 100 5.7/5.5 2.5 0.24/0.27 28 1.8__________________________________________________________________________ E = Example; CE = Comparative Example B side: roll side B' side: corona or flame treatment side, if this treatment has been carried out

Number	Date	Country	Kind
195 19 260	May 1995	DEX
195 48 796	Dec 1995	DEX

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4348457	Rosenthal et al.	Sep 1982
4622237	Lori	Nov 1986
4668753	Kashiwa et al.	May 1987
4701369	Duncan	Oct 1987
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5236680	Nakazawa et al.	Aug 1993
5468440	McAlpin et al.	Nov 1995
5474820	Murschall et al.	Dec 1995
5529843	Dries et al.	Jun 1996
5534606	Bennett et al.	Jul 1996

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27586	Apr 1981	EPX
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367613	May 1990	EPX
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2 572 709	May 1986	FRX
3801535	Jul 1988	DEX
741906	Dec 1955	GBX
2 156 268	Oct 1985	GBX

Biaxially oriented polyproylene film having a high surface modulus

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