Patent Application
20110245446
The present invention relates to a new catalyst system, in particular to a new catalyst system suitable for the manufacture of propylene copolymers.
It is known that propylene copolymers of commerce show improved impact strength and lower brittleness compared to the propylene homopolymer counterparts obtainable by processes in which Ziegler-Natta catalysts are involved. Such obtained propylene copolymers, in particular with the α-olefin comonomer being ethylene, have found widespread applications for example in the production of polymer films, of articles produced by blow moulding or injection moulding, of fibres and of pipes. Among these applications, the most important is the use for the production of films. Such films may be used for packaging such as food packaging.
In general, for the production of propylene copolymers propylene is copolymerised with an α-olefin in a slurry or gas phase polymerization reaction in the presence of a suitable Ziegler-Natta catalyst. The amount of comonomer, i.e. α-olefin, normally does not exceed 10 mol % of the total polymer.
Commercial propylene copolymers produced in the presence of known Ziegler-Natta catalysts usually have a predetermined comonomer distribution which can be slightly tuned to a limited extent by varying the temperature of the process.
In such propylene copolymers the α-olefin is randomly distributed, i.e. the α-olefin units do not form blocks comprising only such comonomer units but instead are evenly distributed as single units within the polypropylene blocks which essentially make up the polymer chains. Moreover in such propylene copolymers the α-olefin comonomers concentrate in short polymer chains.
It is known that important properties such as the transparency and the toughness, i.e. the impact strength, for instance of a film comprising said propylene copolymers are influenced by the comonomer distribution, which in turn is dependent on the used catalyst system. It is also known, that the impact strength can be increased with increasing the amount of the comonomer content. However such an improvement in impact strength is paid with a deterioration of the processing properties as the stickiness of material is highly increased leading to reactor fouling. Moreover also the transparency suffers from rather high amounts of comonomers, like ethylene. It also must considered that the melting point of known propylene copolymers are very sensitive to the increase of comonomer content, i.e. high levels of comonomer lowers the melting point and/or the crystallization point undesirably.
Thus up to now it was impossible to provide propylene copolymers with improved balance between mechanical properties, thermal properties and processing properties. It was in particular not possible to enhance the impact strength of propylene copolymers by keeping constant the melting properties of said propylene copolymers, the transparency of films based on said propylene copolymers and the processing properties of said propylene copolymer films simultaneously.
The selection of the catalyst system plays the decisive role when tailoring propylene copolymers for specific end use applications as those stated above. It is known for instance that the stereospecific form of a polymer is influenced by the catalyst system employed and that the stereospecifity can be improved by adding an external donor compound to the catalyst system. The settling of monomer molecules in the growing polymer molecule are sterically influenced by the structure of the external donor compound of the catalyst particle and thus give the polymer chain a certain stereoisomeric structure. It is also known that the external donors regulate the content of the mmmm-pentades in the polymer chain and thus having a strong influence on the microstructure of the produced polymer. Moreover also the insertion of the comonomers into the propylene copolymer chain is very affected by the used catalyst system.
Accordingly for the development of a new class of propylene copolymers normally one also has to create a new catalyst system enabling to aim the desired properties of said copolymer.
In the present case it is sought for a catalyst system which enables the manufacture of a propylene copolymer having an improved balance between mechanical properties, thermal properties and processing properties. It is in particular an object of the present invention to provide a new catalyst system which enables the production of materials based on a propylene copolymer with improved toughness by keeping the transparency at high level. More particularly it is sought for a new catalyst system which enables the manufacture of a propylene copolymer with improved toughness having excellent process properties, i.e. the copolymer is less sticky compared to the propylene copolymers being state of the art and causes no reactor fouling. Moreover the melting properties of the propylene copolymer produced in the presence of the new catalyst system shall be preferably only little influenced by the comonomer content.
The finding of the present invention is that the catalyst system must comprise an internal donor, preferably an ester of an phthalic acid, and an external donor being an ethoxy-substituted silane, preferably a bis-ethoxy-substituted silane.
Thus the present invention provides a catalyst system comprising
R′R″Si(OCH2CH3)2 (IV)
Preferably the inventive catalyst system as defined in the previous paragraph does not comprise
(a) external donors having the formula (V)
R′R″Si(OCH3)2 (V)
R″′Si(OCH2CH3)3 (VI)
Accordingly it in a preferred embodiment the catalyst system of the instant invention does not comprise propyltriethoxysilane, vinyltriethoxysilane and beta-phenylmethyldiethoxysilane.
It is in particular appreciated that the inventive catalyst system as defined in the instant invention comprises as an external donor only the external donor having the formula (IV) as defined above and in more detail below. Accordingly it is preferred that the catalyst system according to this invention is free of any further external donors and contains only an alkyl-diethoxysilane derivative, in particular the alkyl-diethoxysilane derivative of formula (IV) as defined in the instant invention.
Surprisingly it has been found that with the new catalyst system having the above defined properties propylene copolymers can be produced having superior impact resistance and brittle behaviour compared to commercially available propylene copolymers (see
The present invention will become more fully understood from the detailed description and the accompanying drawings, wherein:
In the following the invention is described in more detail.
As a first requirement the catalyst system must comprise a procatalyst composition comprising a transition metal compound of Group 4 to 6 of the Periodic table (IUPAC, Nomenclature of Inorganic Chemistry, 1989), magnesium chloride (MgCl2) and an internal donor.
The transition metal compound is preferably selected from the group consisting of titanium compound having an oxidation degree of 3 or 4, vanadium compound, chromium compound, zirconium compound, hafnium compound and rare earth metal compounds, more preferably selected from the group consisting of titanium compound, zirconium compound and hafnium compound, and most preferably the transition metal is titanium compound. Moreover the transition metal compounds are in particular transition metal halides, such as transition metal chlorides. The titanium trichloride and titanium tetrachloride are particularly preferred.
Moreover as stated above the procatalyst composition must comprise an internal donor, which is chemically different to the external donor of the catalytic system, i.e. the internal donor must comprise a dialkylphthalate of formula (II), wherein R1 and R2 can be independently selected from a C1 to C4 alkyl, preferably R1 and R2 are the same, i.e. define the same C1 to C4 alkyl residue. The internal donor is defined by the fact that it is included in the mixture of the transition metal compound of Group 4 to 6 of the Periodic table (IUPAC, Nomenclature of Inorganic Chemistry, 1989) and MgCl2 (preferably in the presence of an alcohol) thereby reacting to the procatalyst composition, whereas the external donor is added (optionally together with the cocatalyst) to the mixture of the monomers and the procatalyst composition in the polymerisation process. Preferably the internal donor comprises a n-dialkylphthalate of formula (II), wherein R1 and R2 can be independently selected from a C1 to C4 alkyl, preferably R1 and R2 are the same, i.e. define the same C1 to C4 alkyl residue. Still more preferably the internal donor comprises n-dialkylphthalate of formula (II), wherein R1 and R2 can be independently selected from a C1 and C2 alkyl, preferably R1 and R2 are the same, i.e. define the same C1 or C2 alkyl residue like methyl or ethyl. Still more preferably the internal donor comprises diethylphthalate.
Of course the above defined and further below defined procatalyst composition is a solid, supported procatalyst composition.
Moreover it is preferred that the procatalyst composition contains not more than 2.5 wt.-% of the transition metal, preferably titanium. Still more preferably the procatalyst composition contains 1.7 to 2.5 wt.-% of the transition metal, preferably titanium. Additionally it is appreciated that the molar ratio internal donor/Mg of the procatalyst composition is between 0.03 and 0.08, still more preferably between 0.04 and 0.06, and/or its donor content is between 4 and 15 wt.-%, still more preferably between 6 and 12 wt.-% and yet more preferably between 6 to 10 wt.-%.
Furthermore it is preferred that the internal donor is the result of a transesterification of a dialkylphthalate of formula (I) with an alcohol. It is in particular preferred that the procatalyst composition is a procatalyst composition as produced in the patent applications WO 92/196351 (FI 88047), WO 92/19658 (FI 88048) and EP 0 491 566 A2 (FI 86886). The content of these documents is herein included by reference.
Accordingly it is preferred that the procatalyst composition is prepared by bringing together
Among others the preferred dialkylphthalate of formula (I) for the above and further down described process for the manufacture of the procatalyst composition is selected from the group consisting of propylhexyphthalate (PrHP), dioctylphthalate (DOP), di-iso-decylphthalate (DIDP), diundecylphthalate, diethylhexylphthalate and ditridecylphthalate (DTDP). The most preferred dialkylphthalate is dioctylphthalate (DOP), like di-iso-octylphthalate or diethylhexylphthalate, in particular diethylhexylphthalate.
Preferably at least 80 wt.-%, more preferably at least 90 wt.-%, of the dialkylphthalate of formula (I) is transesterified to the dialkylphthalate of formula (II) as defined above.
It is particular preferred that the procatalyst composition is prepared by
As a further requirement the external donor must be carefully selected. It has been recognized that the improved propylene copolymer properties of the present invention can be only reached in case the procatalyst composition as defined above is treated with an ethoxy-substituted silane as external donor.
Preferably the external donor has the formula (III)
R′nR″mSi(OCH2CH3)z (III)
Preferably R′ and R″ are independently selected from the group consisting of linear aliphatic hydrocarbon group, branched aliphatic hydrocarbon group, cyclic aliphatic hydrocarbon group and aromatic group. It is in particular preferred that R′ and R″ are independently selected from the group consisting of methyl, ethyl, propyl, butyl, octyl, decanyl, iso-propyl, iso-butyl, iso-pentyl, tert.-butyl, tert.-amyl, neopentyl, cyclopentyl, cyclohexyl, methylcyclopentyl and cycloheptyl. In a preferred embodiment the external donor has the formula IV
R′R″Si(OCH2CH3)2 (IV)
Accordingly it is preferred that the external donor is selected from the group consisting of di-iso-propyldiethoxysilane (DIPDES), cyclohexylmethyldiethoxysilane (CHMDES) and dicyclopentadienyldiethoxysilane (DCPDES). The most preferred external donor is di-iso-propyldiethoxysilane (DIPDES).
Moreover the catalyst system may comprise a cocatalyst. Preferred cocatalysts are organoaluminum compounds. Accordingly it is preferred to select the cocatalyst from the group consisting of trialkylaluminium, like triethylaluminium (TEA), dialkyl aluminium chloride and alkyl aluminium sesquichloride.
Especially good results are achieved with a catalyst system comprising
Thus it is preferred that the catalyst system comprises
R′nR″mSi(OCH2CH3)z (III),
The catalyst system as defined in the previous paragraph comprises in particular as an external donor only the external donor as defined under item (b). Accordingly it is preferred that the catalyst system according to this invention is free of any further external donors and contains only an alkyl-diethoxysilane derivative, in particular the alkyl-diethoxysilane derivative as defined in item (b) of the previous paragraph.
The above defined catalyst system enables to produce propylene copolymers in particular propylene copolymers as further defined below. Accordingly the catalyst system is further defined by the fact that it is suitable to produce a propylene copolymer, in particular a propylene copolymer as further defined below.
Moreover the present invention is directed to the manufacture of the catalyst system wherein in first step the procatalyst composition is produced and subsequently in a second step the external donor and optionally the cocatalyst is added. The procatalyst composition is preferably produced as defined in the in the patent applications WO 92/196351 (FI 88047), WO 92/19658 (FI 88048) and EP 0 491 566 A2 (FI 86886). The content of these documents is herein included by reference. Accordingly it is in particular preferred that the procatalyst composition is produced as defined above.
Of course the present invention is also directed to the use of the catalyst system as defined in the instant invention for the manufacture of a polypropylene, preferably a propylene copolymer, more preferably a propylene copolymer as defined below.
In the following the propylene copolymer is defined for which the inventive catalyst system is in particular suitable. Accordingly the present invention is also directed to the following propylene copolymers.
In a first embodiment of the present invention a propylene copolymer is provided comprising monomer units of propylene and at least one other α-olefin as a comonomer, wherein
Accordingly the propylene copolymer according to the first embodiment can be also defined by a propylene copolymer comprising monomer units of propylene and at least one other α-olefin as a comonomer, wherein
The exact measuring method of the stepwise isothermal segregation technique (SIST), in particular the determination of the melt enthalpy [J/g], is given in the example section.
Surprisingly, it has been found that propylene copolymers with such characteristics have superior properties compared to the propylene copolymers known in the art. Especially the propylene copolymers of the instant invention have superior impact resistance and brittle behaviour compared to commercially available propylene copolymers (see
The first requirement according to the first embodiment of the present invention is that the propylene copolymer comprises beside propylene a certain amount of comonomer being an α-olefin. Preferred α-olefins are selected from the group consisting of ethylene, C4 α-olefin, C5 α-olefin, C6 α-olefin to C8 α-olefin, more preferably selected from the group consisting of ethylene, 1-butene, 1-hepten, 1-hexene and 1-octene, still more preferably selected from the group consisting of ethylene and C4 α-olefin, yet more preferably selected from the group consisting of ethylene and 1-butene, and most preferably ethylene. The propylene copolymer may comprise mixtures of the above mentioned comonomers, however it is preferred that the propylene copolymer comprises only one species of α-olefin as a comonomer. In the most preferred embodiment the propylene copolymer comprises only propylene and ethylene.
The amount of comonomer present in the propylene copolymer must be at least 2.0 wt.-% to obtain the desired properties in particular with regard to the mechanical properties, like superior impact resistance. More precisely the weight ratio of the comonomer (being a α-olefin as defined above) to the sum of monomers present in said polypropylene copolymer (comonomer/(comonomer+propylene)) is at least 2. 0 wt.-%, more preferably is at least 3.0 wt.-% and still more preferably is at least 5.0 wt.-%. On the other hand the comonomer should be preferably not to high otherwise the polymer might loose its rigidity. Accordingly the weight ratio of the comonomer to the sum of monomers present in said polypropylene copolymer (comonomer/(comonomer+propylene)) shall preferably not exceed 30.0 wt.-%, more preferably not exceed 15.0 wt.-%, still more preferably not exceed 10.0 wt.-% and yet more preferably shall not exceed 8.0 wt.-%. Preferred ranges are 2.0 to 20.0 wt.-%, more preferred 2.0 to 12.0 wt.-%, yet more preferred 2.0 to 10.0 wt.-%, still more preferred 3.00 to 10.0 wt.-%, still yet more preferred 3.0 to 8.0 wt.-%, and most preferred 5.0 to 7.0 wt.-%. Accordingly it is preferred that the propylene copolymer according to this invention is a random propylene copolymer. The comonomer content can be determined with FT infrared spectroscopy, as described below in the example section.
Furthermore the propylene copolymer according to this invention is further specified by its lamellar thickness distribution. The stepwise isothermal segregation technique (SIST) provides a possibility to determine the lamellar thickness distribution. The precise measuring method is specified in the example section (in particular the definition of the lamella thickness of each fraction and its melt enthalpy). Thereby rather high amounts (rather high melt enthalpy [J/g]) of polymer fractions crystallizing at high temperatures indicate a rather high amount of thick lamellae.
It has been recognized that the improved balance between the mechanical and process properties can be only achieved with a new class of propylene copolymer having a specific lamellar thickness distribution, i.e. a propylene copolymer comprising a fraction with a lamella thickness of more than 9.0 nm. More preferably the propylene copolymer comprises a fraction with a lamella thickness of more than 9.2 nm, still more preferably of more than 9.5 nm. Preferred ranges for said fraction are from 9.0 to 12.0 nm, more preferred from 9.2 to 11.0 nm.
A further requirement of the above defined fraction is that it represents the largest fraction of all fractions, in particular compared to the fractions with a lamella thickness below 9.0 nm, of the propylene copolymer. Accordingly the propylene copolymer comprises a fraction with a lamella thickness of more than 9.0 nm (the other preferred values for the lamella thickness are given above) having a higher melt enthalpy [J/g] as each lamella fraction with a lamella thickness below 9.0 nm. More preferably the fraction with a lamella thickness of more than 9.0 nm has melt enthalpy of more than 20.0 J/g, still more preferably of more than 21.0 J/g. Concerning the fractions below 9.0 nm it is preferred that the they have a melt enthalpy of not more than 30.0 J/g. It is in particular preferred that the fractions with a lamella thickness in the range of 6.5 to 9.0 nm have a melt enthalpy in the range of 15.0 to 30.0 J/g.
The propylene copolymer according to this invention is further preferably defined by its isotactic sequence length distribution.
The measurement of isotactic sequence length distribution is performed in the instant invention by using the temperature rising elution fraction (TREF) technique (the exact description is given in the experimental part), which fractionates propylene copolymers according to the solubility differences. It has been clearly demonstrated for propylene polymers that the temperature rising elution fraction (TREF) technique fractionates the propylene polymer according to the longest crystallisable sequences in the chain, which increases almost linearly with the elution temperature (P. Ville et al., Polymer 42 (2001) 1953-1967). Hence the higher the maximum temperature the longer are the isotactic sequences. The results further showed that the temperature rising elution fraction (TREF) technique does not strictly fractionate polypropylene according to tacticity but according to the longest crystallisable sequences in the chain. The solubility of a polypropylene polymer chain hence is influenced only by the concentration and distribution of sterical defects. Insofar the temperature rising elution fraction (TREF) technique is an appropriate method to characterize the inventive propylene copolymer further.
Thus it is preferred that the propylene copolymer posses a distribution curve of the average isotactic chain length featured by at least two distinct maxima, i.e. the comonomer units are not equally distributed among the individual chains of the propylene copolymer. Accordingly it is preferred that the temperature rising elution fractionation (TREF) curve of the inventive propylene copolymer comprises at least two local maxima
More preferably the area below the absolute maximum of that the temperature rising elution fractionation (TREF) function is in the range of 50 to 85 wt-%, more preferably in the range of 50 to 80 wt.-% and yet more preferably in the range of 55 to 80 wt.-%. With regard to the area below the relative maximum of the temperature rising elution fractionation (TREF) function as defined above it is preferred that it is in the range of 10 to 30 wt.-%, more preferably in the range of 10 to 25 wt.-%.
Moreover it is preferred that the propylene copolymer has xylene solubles of some extent, i.e. of at least 2.0 wt.-%. Xylene solubles are the part of the polymer soluble in cold xylene determined by dissolution in boiling xylene and letting the insoluble part crystallize from the cooling solution (for the method see below in the experimental part). The xylene solubles fraction contains polymer chains of low stereo-regularity and is an indication for the amount of non-crystalline areas.
Preferably, the propylene copolymer has xylene solubles of more than 6.0 wt.-%. On the other hand, the amount of xylene solubles should not be too high since they represent a potential contamination risk. Accordingly it is preferred that the xylene solubles are not more than 40.0 wt.-%, still more preferably not more than 35.0 wt.-% and yet more preferably not more than 20.0 wt.-%. In preferred embodiments the xylene solubles are in the range of 5.0 to 40.0 wt.-%, more preferably in the range of 6.0 to 30.0 wt.-% and still more preferably in the range of 6.0 to 20.0 wt.-%.
Additionally it is appreciated that the xylene soluble fraction of the inventive propylene copolymer is characterized by a rather high intrinsic viscosity. Common propylene copolymers have normally xylene soluble fractions with a rather low intrinsic viscosity, which is reflected in increased stickiness leading to reactor fouling.
The intrinsic viscosity is a measure of the capability of a polymer in solution to enhance the viscosity of said solution. The viscosity behavior of macromolecular substances in solution is one of the most frequently used approaches for characterization. The intrinsic viscosity number 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 molecule as well as the solvent. In general, the intrinsic viscosity of linear macromolecular substances is related to the molecular weight or degree of polymerization. With macromolecules, viscosity number measurements provide a method for the rapid determination of molecular weight when the relationship between viscosity and molecular weight has been established. The intrinsic viscosity in the instant invention is measured according to DIN ISO 1628/1, October 1999 (in Decalin at 135° C.).
Accordingly the propylene copolymer according to this invention preferably fulfils the equation (2), more preferably the equation (2a), yet more preferably the equation (2b), still more preferably the equation (2c), still yet more preferably the equation (2d), like the equation (2e)
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.1143 (2)
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.1101 (2a)
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.0501 (2b)
IV(XS)[dl/g]−0.31·IV[dl/g]>−0.05 (2c)
IV(XS)[dl/g]−0.3·IV[dl/g]>−0.2 (2d)
IV(XS)[dl/g]−0.3·IV[dl/g]>−0.1 (2e)
wherein
IV (XS) is the intrinsic viscosity of the xylene soluble fraction of the polypropylene copolymer measured according DIN ISO 1628/1 and
IV is the intrinsic viscosity of the total polypropylene copolymer measured according DIN ISO 1628/1.
As can be seen from
Moreover the high intrinsic viscosity values of the xylene soluble fraction of the inventive propylene copolymers are also reached in broad range of melt flow rate. This can be easily learned from
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.601 (3)
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.621 (3a)
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.641 (3b)
IV(XS)[dl/g]+0.01MFR[g/10min]>0.64 (3c)
wherein
IV (XS) is the intrinsic viscosity of the xylene soluble fraction of said polypropylene copolymer measured according DIN ISO 1628/1, and
MFR is the melt flow rate measured according to ISO 1133 at 230° C. and 2.16 kg load.
Additionally it is preferred that the xylene soluble fraction of the inventive propylene copolymer as defined herein has a intrinsic viscosity of at least 0.4 dl/g, more preferably of at least 0.5 dl/g. Moreover it is appreciated that the intrinsic viscosity of the total propylene copolymer reaches a certain value. Thus it is preferred that the intrinsic viscosity of the total propylene copolymer is at least 1.0 dl/g, more preferably at least 1.2 dl/g.
In a second embodiment of the present invention a propylene copolymer is provided comprising monomer units of propylene and at least one other α-olefin as a comonomer, wherein
Surprisingly, it has been found that propylene copolymers with such characteristics have superior properties compared to the propylene copolymers known in the art. Especially the propylene copolymers of the instant invention have superior impact resistance and brittle behaviour compared to commercially available propylene copolymers (see
The first requirement according to the second embodiment of the present invention is that the propylene copolymer comprises beside propylene a certain amount of comonomer being an α-olefin. Preferred α-olefins are selected from the group consisting of ethylene, C4 α-olefin, C5 α-olefin and C6 α-olefin to C8 α-olefin, more preferably selected from the group consisting of ethylene, 1-butene, 1-heptene, 1-hexene and 1-octene, still more preferably selected from the group consisting of ethylene and C4 α-olefin, yet more preferably selected from the group consisting of ethylene and 1-butene, and most preferably ethylene. The propylene copolymer may comprise mixtures of the above mentioned comonomers, however it is preferred that the propylene copolymer comprises only one species of α-olefin as a comonomer. In the most preferred embodiment the propylene copolymer comprises only propylene and ethylene.
The amount of comonomer present in the propylene copolymer must be at least 2.0 wt.-% to obtain the desired properties in particular with regard to the mechanical properties, like superior impact resistance. More precisely the weight ratio of the comonomer (being a α-olefin as defined above) to the sum of monomers present in said polypropylene copolymer (comonomer/(comonomer+propylene)) is at least 2.0 wt.-%, more preferably is at least 3.0 wt.-% and still more preferably is at least 5.0 wt.-%. On the other hand the comonomer should be preferably not to high otherwise the polymer might loose its rigidity. Accordingly the weight ratio of the comonomer to the sum of monomers present in said polypropylene copolymer (comonomer/(comonomer+propylene)) shall preferably not exceed 30.0 wt.-%, more preferably not exceed 15.0 wt.-%, still more preferably not exceed 10.0 wt.-% and yet more preferably shall not exceed 8.0 wt.-%. Preferred ranges are 2.0 to 20.0 wt.-%, more preferred 2.0 to 12.0 wt.-%, yet more preferred 2.0 to 10.0 wt.-%, still more preferred 3.0 to 10.0 wt.-%, still yet more preferred 3.0 to 8.0 wt.-%, and most preferred 5.0 to 7.0 wt.-%. Accordingly it is preferred that the propylene copolymer according to this invention is a random propylene copolymer. The comonomer content can be determined with FT infrared spectroscopy, as described below in the example section.
The propylene copolymer according to this invention is further defined by its isotactic sequence length distribution.
The measurement of isotactic sequence length distribution is performed in the instant invention by using the temperature rising elution fraction (TREF) technique (the exact description is given in the experimental part), which fractionates propylene copolymers according to the solubility differences. It has been clearly demonstrated for propylene polymers that the temperature rising elution fraction (TREF) technique fractionates the propylene polymer according to the longest crystallisable sequences in the chain, which increases almost linearly with the elution temperature (P. Ville et al., Polymer 42 (2001) 1953-1967). Hence the higher the maximum temperature the longer are the isotactic sequences. The results further showed that the temperature rising elution fraction (TREF) technique does not strictly fractionate polypropylene according to tacticity but according to the longest crystallisable sequences in the chain. The solubility of a polypropylene polymer chain hence is influenced only by the concentration and distribution of sterical defects. Insofar the temperature rising elution fraction (TREF) technique is an appropriate method to characterize the inventive propylene copolymer further.
The propylene copolymer according to the instant invention differs from known propylene copolymers in its temperature rising elution fractionation (TREF) function (see
More preferably the area below the absolute maximum of that the temperature rising elution fractionation (TREF) function is in the range of 50 to 85 wt.-%, more preferably in the range of 50 to 80 wt.-% and yet more preferably in the range of 55 to 80 wt.-%. With regard to the area below the relative maximum of the temperature rising elution fractionation (TREF) function as defined above it is preferred that it is in the range of 10 to 30 wt.-%, more preferably in the range of 10 to 25 wt.-%.
Furthermore the propylene copolymer according to this invention is preferably further specified by its lamellar thickness distribution. The stepwise isothermal segregation technique (SIST) provides a possibility to determine the lamellar thickness distribution. The precise measuring method is specified in the example section (in particular the definition of the lamella thickness of each fraction and its melt enthalpy). Thereby rather high amounts (rather high melt enthalpy [J/g]) of polymer fractions crystallizing at high temperatures indicate a rather high amount of thick lamellae.
has been recognized that the improved balance between the mechanical and process properties can be achieved with a propylene copolymer having a specific lamellar thickness distribution, i.e. a propylene copolymer comprising a fraction with a lamella thickness of more than 9.0 nm. More preferably the propylene copolymer comprises a fraction with a lamella thickness of more than 9.2 nm, still more preferably of more than 9.5 nm. Preferred ranges for said fraction are from 9.0 to 12.0 nm, more preferred from 9.2 to 11.0 nm.
A further requirement of the above defined fraction is that it represents the largest fraction of all fractions, in particular compared to the fractions with a lamella thickness below 9.0 nm, of the propylene copolymer. Accordingly the propylene copolymer comprises a fraction with a lamella thickness of more than 9.0 nm (the other preferred values for the lamella thickness are given above) having a higher melt enthalpy [J/g] as each lamella fraction with a lamella thickness below 9.0 nm. More preferably the fraction with a lamella thickness of more than 9.0 nm has melt enthalpy of more than 20.0 J/g, still more preferably of more than 21.0 J/g. Concerning the fractions below 9.0 nm it is preferred that the they have a melt enthalpy of not more than 30.0 J/g. It is in particular preferred that the fractions with a lamella thickness in the range of 6.5 to 9.0 nm have a melt enthalpy in the range of 15.0 to 30.0 J/g.
Moreover it is preferred that the propylene copolymer has xylene solubles of some extent, i.e. of at least 2.0 wt.-%. Xylene solubles are the part of the polymer soluble in cold xylene determined by dissolution in boiling xylene and letting the insoluble part crystallize from the cooling solution (for the method see below in the experimental part). The xylene solubles fraction contains polymer chains of low stereo-regularity and is an indication for the amount of non-crystalline areas. Preferably, the propylene copolymer has xylene solubles of more than 6.0 wt.-%. On the other hand, the amount of xylene solubles should not be too high since they represent a potential contamination risk. Accordingly it is preferred that the xylene solubles are not more than 40.0 wt.-%, still more preferably not more than 35.0 wt.-% and yet more preferably not more than 20.0 wt.-%. In preferred embodiments the xylene solubles are in the range of 5.0 to 40.0 wt.-%, more preferably in the range of 6.0 to 30.0 wt.-% and still more preferably in the range of 6.0 to 20.0 wt.-%.
Additionally it is appreciated that the xylene soluble fraction of the inventive propylene copolymer is characterized by a rather high intrinsic viscosity. Common propylene copolymer have normally xylene soluble fractions with a rather low intrinsic viscosity, which is reflected in increased stickiness leading to reactor fouling.
The intrinsic viscosity is a measure of the capability of a polymer in solution to enhance the viscosity of said solution. The viscosity behavior of macromolecular substances in solution is one of the most frequently used approaches for characterization. The intrinsic viscosity number 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 molecule as well as the solvent. In general, the intrinsic viscosity of linear macromolecular substances is related to the molecular weight or degree of polymerization. With macromolecules, viscosity number measurements provide a method for the rapid determination of molecular weight when the relationship between viscosity and molecular weight has been established. The intrinsic viscosity in the instant invention is measured according to DIN ISO 1628/1, October 1999 (in Decalin at 135° C.).
Accordingly the propylene copolymer according to this invention preferably fulfils the equation (2), more preferably the equation (2a), yet more preferably the equation (2b), still more preferably the equation (2c), still yet more preferably the equation (2d), like the equation (2e)
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.1143 (2)
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.1101 (2a)
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.0501 (2b)
IV(XS)[dl/g]−0.31·IV[dl/g]>−0.05 (2c)
IV(XS)[dl/g]−0.3·IV[dl/g]>−0.2 (2d)
IV(XS)[dl/g]−0.3·IV[dl/g]>−0.1 (2e)
wherein
IV (XS) is the intrinsic viscosity of the xylene soluble fraction of the polypropylene copolymer measured according DIN ISO 1628/1 and
IV is the intrinsic viscosity of the total polypropylene copolymer measured according DIN ISO 1628/1.
As can be seen from
Moreover the high intrinsic viscosity values of the xylene soluble fraction of the inventive propylene copolymers are also reached in broad range of melt flow rate. This can be easily learned from
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.601 (3)
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.621 (3a)
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.641 (3b)
IV(XS)[dl/g]+0.01MFR[g/10min]>0.64 (3c)
wherein
IV (XS) is the intrinsic viscosity of the xylene soluble fraction of said polypropylene copolymer measured according DIN ISO 1628/1, and
MFR is the melt flow rate measured according to ISO 1133 at 230° C. and 2.16 kg load.
Additionally it is preferred that the xylene soluble fraction of the inventive propylene copolymer as defined herein has a intrinsic viscosity of at least 0.4 dl/g, more preferably of at least 0.5 dl/g. Moreover it is appreciated that the intrinsic viscosity of the total propylene copolymer reaches a certain value. Thus it is preferred that the intrinsic viscosity of the total propylene copolymer is at least 1.0 dl/g, more preferably at least 1.2 dl/g.
In a third embodiment of the present invention a propylene copolymer is provided comprising monomer units of propylene and at least one other α-olefin as a comonomer, wherein
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.1143 (2)
Surprisingly, it has been found that propylene copolymers with such characteristics have superior properties compared to the propylene copolymers known in the art. Especially the propylene copolymers of the instant invention have superior impact resistance and brittle behaviour compared to commercially available propylene copolymers (see
The first requirement according to the third embodiment of the present invention is that the propylene copolymer comprises beside propylene a certain amount of comonomer being an α-olefin. Preferred α-olefins are selected from the group consisting of ethylene, C4 α-olefin, C5 α-olefin and C6 α-olefin to C8 α-olefin, more preferably selected from the group consisting of ethylene, 1-butene, 1-heptene, 1-hexene and 1-octene, still more preferably selected from the group consisting of ethylene and C4 α-olefin, yet more preferably selected from the group consisting of ethylene and 1-butene, and most preferably ethylene. The propylene copolymer may comprise mixtures of the above mentioned comonomers, however it is preferred that the propylene copolymer comprises only one species of α-olefin as a comonomer. In the most preferred embodiment the propylene copolymer comprises only propylene and ethylene.
The amount of comonomer present in the propylene copolymer must be at least 2.0 wt.-% to obtain the desired properties in particular with regard to the mechanical properties, like superior impact resistance. More precisely the weight ratio of the comonomer (being a α-olefin as defined above) to the sum of monomers present in said polypropylene copolymer (comonomer/(comonomer+propylene)) is at least 2.0 wt.-%, more preferably is at least 3.0 wt.-% and still more preferably is at least 5.0 wt.-%. On the other hand the comonomer should be preferably not to high otherwise the polymer might loose its rigidity. Accordingly the weight ratio of the comonomer to the sum of monomers present in said polypropylene copolymer (comonomer/(comonomer+propylene)) shall preferably not exceed 30.0 wt.-%, more preferably not exceed 15.0 wt.-%, still more preferably not exceed 10.0 wt.-% and yet more preferably shall not exceed 8.0 wt.-%. Preferred ranges are 2.0 to 20.0 wt.-%, more preferred 2.0 to 12.0 wt.-%, yet more preferred 2.0 to 10.0 wt.-%, still more preferred 3.0 to 10.0 wt.-%, still yet more preferred 3.0 to 8.0 wt.-%, and most preferred 5.0 to 7.0 wt.-%. Accordingly it is preferred that the propylene copolymer according to this invention is a random propylene copolymer. The comonomer content can be determined with FT infrared spectroscopy, as described below in the example section.
Moreover it is required that the propylene copolymer has xylene solubles of some extent, i.e. of at least 2.0 wt.-%. Xylene solubles are the part of the polymer soluble in cold xylene determined by dissolution in boiling xylene and letting the insoluble part crystallize from the cooling solution (for the method see below in the experimental part). The xylene solubles fraction contains polymer chains of low stereo-regularity and is an indication for the amount of non-crystalline areas.
Preferably, the propylene copolymer has xylene solubles of more than 6.0 wt.-%. On the other hand, the amount of xylene solubles should not be too high since they represent a potential contamination risk. Accordingly it is preferred that the xylene solubles are not more than 40.0 wt.-%, still more preferably not more than 35.0 wt.-% and yet more preferably not more than 20.0 wt.-%. In preferred embodiments the xylene solubles are in the range of 5.0 to 40.0 wt.-%, more preferably in the range of 6.0 to 30.0 wt.-% and still more preferably in the range of 6.0 to 20.0 wt.-%.
As stated above it is required that the xylene soluble fraction of the inventive propylene copolymer is characterized by a rather high intrinsic viscosity. Common propylene copolymer have normally xylene soluble fractions with a rather low intrinsic viscosity, which is reflected in increased stickiness leading to reactor fouling.
The intrinsic viscosity is a measure of the capability of a polymer in solution to enhance the viscosity of said solution. The viscosity behavior of macromolecular substances in solution is one of the most frequently used approaches for characterization. The intrinsic viscosity number 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 molecule as well as the solvent. In general, the intrinsic viscosity of linear macromolecular substances is related to the molecular weight or degree of polymerization. With macromolecules, viscosity number measurements provide a method for the rapid determination of molecular weight when the relationship between viscosity and molecular weight has been established. The intrinsic viscosity in the instant invention is measured according to DIN ISO 1628/1, October 1999 (in Decalin at 135° C.).
Accordingly the propylene copolymer according to this invention fulfils the equation (2), preferably the equation (2a), yet more preferably the equation (2b), still more preferably the equation (2c), still yet more preferably the equation (2d), like the equation (2e)
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.1143 (2)
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.1101 (2a)
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.0501 (2b)
IV(XS)[dl/g]−0.31·IV[dl/g]>−0.05 (2c)
IV(XS)[dl/g]−0.3·IV[dl/g]>−0.2 (2d)
IV(XS)[dl/g]−0.3·IV[dl/g]>−0.1 (2e)
wherein
IV (XS) is the intrinsic viscosity of the xylene soluble fraction of the polypropylene copolymer measured according DIN ISO 1628/1 and
IV is the intrinsic viscosity of the total polypropylene copolymer measured according DIN ISO 1628/1.
As can be seen from
Moreover the high intrinsic viscosity values of the xylene soluble fraction of the inventive propylene copolymers are also reached in broad range of melt flow rate. This can be easily learned from
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.601 (3)
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.621 (3a)
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.641 (3b)
IV(XS)[dl/g]+0.01MFR[g/10min]>0.64 (3c)
wherein
IV (XS) is the intrinsic viscosity of the xylene soluble fraction of said polypropylene copolymer measured according DIN ISO 1628/1, and
MFR is the melt flow rate measured according to ISO 1133 at 230° C. and 2.16 kg load.
Additionally it is preferred that the xylene soluble fraction of the inventive propylene copolymer as defined herein has a intrinsic viscosity of at least 0.4 dl/g, more preferably of at least 0.5 dl/g. Moreover it is appreciated that the intrinsic viscosity of the total propylene copolymer reaches a certain value. Thus it is preferred that the intrinsic viscosity of the total propylene copolymer is at least 1.0 dl/g, more preferably at least 1.2 dl/g.
Furthermore the propylene copolymer according to this invention is preferably further specified by its lamellar thickness distribution. The stepwise isothermal segregation technique (SIST) provides a possibility to determine the lamellar thickness distribution. The precise measuring method is specified in the example section (in particular the definition of the lamella thickness of each fraction and its melt enthalpy). Thereby rather high amounts (rather high melt enthalpy [J/g]) of polymer fractions crystallizing at high temperatures indicate a rather high amount of thick lamellae.
It has been recognized that the improved balance between the mechanical and process properties can be achieved with a propylene copolymer having a specific lamellar thickness distribution, i.e. a propylene copolymer comprising a fraction with a lamella thickness of more than 9.0 nm. More preferably the propylene copolymer comprises a fraction with a lamella thickness of more than 9.2 nm, still more preferably of more than 9.5 nm. Preferred ranges for said fraction are from 9.0 to 12.0 nm, more preferred from 9.2 to 11.0 nm.
A further requirement of the above defined fraction is that it represents the largest fraction of all fractions, in particular compared to the fractions with a lamella thickness below 9.0 nm, of the propylene copolymer. Accordingly the propylene copolymer comprises a fraction with a lamella thickness of more than 9.0 nm (the other preferred values for the lamella thickness are given above) having a higher melt enthalpy [J/g] as each lamella fraction with a lamella thickness below 9.0 nm. More preferably the fraction with a lamella thickness of more than 9.0 nm has melt enthalpy of more than 20.0 J/g, still more preferably of more than 21.0 J/g.
Concerning the fractions below 9.0 nm it is preferred that the they have a melt enthalpy of not more than 30.0 J/g. It is in particular preferred that the fractions with a lamella thickness in the range of 6.5 to 9.0 nm have a melt enthalpy in the range of 15.0 to 30.0 J/g.
The propylene copolymer according to this invention is further preferably defined by its isotactic sequence length distribution.
The measurement of isotactic sequence length distribution is performed in the instant invention by using the temperature rising elution fraction (TREF) technique (the exact description is given in the experimental part), which fractionates propylene copolymers according to the solubility differences. It has been clearly demonstrated for propylene polymers that the temperature rising elution fraction (TREF) technique fractionates the propylene polymer according to the longest crystallisable sequences in the chain, which increases almost linearly with the elution temperature (P. Ville et al., Polymer 42 (2001) 1953-1967). Hence the higher the maximum temperature the longer are the isotactic sequences. The results further showed that the temperature rising elution fraction (TREF) technique does not strictly fractionate polypropylene according to tacticity but according to the longest crystallisable sequences in the chain. The solubility of a polypropylene polymer chain hence is influenced only by the concentration and distribution of sterical defects. Insofar the temperature rising elution fraction (TREF) technique is an appropriate method to characterize the inventive propylene copolymer further.
Thus it is preferred that the propylene copolymer posses a distribution curve of the average isotactic chain length featured by at least two distinct maxima, i.e. the comonomer units are not equally distributed among the individual chains of the propylene copolymer. Accordingly it is preferred that the temperature rising elution fractionation (TREF) curve of the inventive propylene copolymer comprises at least two local maxima
More preferably the area below the absolute maximum of that the temperature rising elution fractionation (TREF) function is in the range of 50 to 85 wt.-%, more preferably in the range of 50 to 80 wt.-% and yet more preferably in the range of 55 to 80 wt.-%. With regard to the area below the relative maximum of the temperature rising elution fractionation (TREF) function as defined above it is preferred that it is in the range of 10 to 30 wt.-%, more preferably in the range of 10 to 25 wt.-%.
In a fourth embodiment of the present invention a propylene copolymer is provided comprising monomer units of propylene and at least one other α-olefin as a comonomer, wherein
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.601 (3)
Surprisingly, it has been found that propylene copolymers with such characteristics have superior properties compared to the propylene copolymers known in the art. Especially the propylene copolymers of the instant invention have superior impact resistance and brittle behaviour compared to commercially available propylene copolymers (see
The first requirement according to the fourth embodiment of the present invention is that the propylene copolymer comprises beside propylene a certain amount of comonomer being an α-olefin. Preferred α-olefins are selected from the group consisting of ethylene, C4 α-olefin, C5 α-olefin and C6 α-olefin to C8 α-olefin, more preferably selected from the group consisting of ethylene, 1-butene, 1-heptene, 1-hexene and 1-octene, still more preferably selected from the group consisting of ethylene and C4 α-olefin, yet more preferably selected from the group consisting of ethylene and 1-butene, and most preferably ethylene. The propylene copolymer may comprise mixtures of the above mentioned comonomers, however it is preferred that the propylene copolymer comprises only one species of α-olefin as a comonomer. In the most preferred embodiment the propylene copolymer comprises only propylene and ethylene.
The amount of comonomer present in the propylene copolymer must be at least 2.0 wt.-% to obtain the desired properties in particular with regard to the mechanical properties, like superior impact resistance. More precisely the weight ratio of the comonomer (being a α-olefin as defined above) to the sum of monomers present in said polypropylene copolymer (comonomer/(comonomer+propylene)) is at least 2.0 wt.-%, more preferably is at least 3.0 wt.-% and still more preferably is at least 5.0 wt.-%. On the other hand the comonomer should be preferably not to high otherwise the polymer might loose its rigidity. Accordingly the weight ratio of the comonomer to the sum of monomers present in said polypropylene copolymer (comonomer/(comonomer+propylene)) shall preferably not exceed 30.0 wt.-%, more preferably not exceed 15.0 wt.-%, still more preferably not exceed 10.0 wt.-% and yet more preferably shall not exceed 8.0 wt.-%. Preferred ranges are 2.0 to 20.0 wt.-%, more preferred 2.0 to 12.0 wt.-%, yet more preferred 2.0 to 10.0 wt.-%, still more preferred 3.0 to 10.0 wt.-%, still yet more preferred 3.0 to 8.0 wt.-%, and most preferred 5.0 to 7.0 wt.-%. Accordingly it is preferred that the propylene copolymer according to this invention is a random propylene copolymer. The comonomer content can be determined with FT infrared spectroscopy, as described below in the example section.
Moreover it is required that the propylene copolymer has xylene solubles of some extent, i.e. of at least 2.0 wt.-%. Xylene solubles are the part of the polymer soluble in cold xylene determined by dissolution in boiling xylene and letting the insoluble part crystallize from the cooling solution (for the method see below in the experimental part). The xylene solubles fraction contains polymer chains of low stereo-regularity and is an indication for the amount of non-crystalline areas.
Preferably, the propylene copolymer has xylene solubles of more than 6.0 wt.-%. On the other hand, the amount of xylene solubles should not be too high since they represent a potential contamination risk. Accordingly it is preferred that the xylene solubles are not more than 40.0 wt.-%, still more preferably not more than 35.0 wt.-% and yet more preferably not more than 20.0 wt.-%. In preferred embodiments the xylene solubles are in the range of 5.0 to 40.0 wt.-%, more preferably in the range of 6.0 to 30.0 wt.-% and still more preferably in the range of 6.0 to 20.0 wt.-%.
As stated above it is required that the xylene soluble fraction of the inventive propylene copolymer is characterized by a rather high intrinsic viscosity. Common propylene copolymer have normally xylene soluble fractions with a rather low intrinsic viscosity, which is reflected in increased stickiness leading to reactor fouling.
The intrinsic viscosity is a measure of the capability of a polymer in solution to enhance the viscosity of said solution. The viscosity behavior of macromolecular substances in solution is one of the most frequently used approaches for characterization. The intrinsic viscosity number 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 molecule as well as the solvent. In general, the intrinsic viscosity of linear macromolecular substances is related to the molecular weight or degree of polymerization. With macromolecules, viscosity number measurements provide a method for the rapid determination of molecular weight when the relationship between viscosity and molecular weight has been established. The intrinsic viscosity in the instant invention is measured according to DIN ISO 1628/1, October 1999 (in Decalin at 135° C.).
Moreover the inventive propylene copolymers shall not only have a xylene soluble fraction with rather high intrinsic viscosity values but said inventive propylene copolymers shall also obtainable in broad range of melt flow rate. Thus as stated above the propylene copolymer of the instant invention fulfils the equation (3), more preferably the equation (3a) still more preferably the equation (3b), yet more preferably the equation (3c)
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.601 (3)
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.621 (3a)
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.641 (3b)
IV(XS)[dl/g]+0.01MFR[g/10min]>0.64 (3c)
wherein
IV (XS) is the intrinsic viscosity of the xylene soluble fraction of said polypropylene copolymer measured according DIN ISO 1628/1, and
MFR is the melt flow rate measured according to ISO 1133 at 230° C. and 2.16 kg load.
Additionally it is appreciated that the propylene copolymer according to this invention preferably fulfils the equation (2), more preferably the equation (2a), yet more preferably the equation (2b), still more preferably the equation (2c), still yet more preferably the equation (2d), like the equation (2e)
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.1143 (2)
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.1101 (2a)
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.0501 (2b)
IV(XS)[dl/g]−0.31·IV[dl/g]>−0.05 (2c)
IV(XS)[dl/g]−0.3·IV[dl/g]>−0.2 (2d)
IV(XS)[dl/g]−0.3·IV[dl/g]>−0.1 (2e)
wherein
IV (XS) is the intrinsic viscosity of the xylene soluble fraction of the polypropylene copolymer measured according DIN ISO 1628/1 and
IV is the intrinsic viscosity of the total polypropylene copolymer measured according DIN ISO 1628/1.
As can be seen from
Additionally it is preferred that the xylene soluble fraction of the inventive propylene copolymer as defined herein has a intrinsic viscosity of at least 0.4 dl/g, more preferably of at least 0.5 dl/g. Moreover it is appreciated that the intrinsic viscosity of the total propylene copolymer reaches a certain value. Thus it is preferred that the intrinsic viscosity of the total propylene copolymer is at least 1.0 dl/g, more preferably at least 1.2 dl/g.
Furthermore the propylene copolymer according to this invention is preferably further specified by its lamellar thickness distribution. The stepwise isothermal segregation technique (SIST) provides a possibility to determine the lamellar thickness distribution. The precise measuring method is specified in the example section (in particular the definition of the lamella thickness of each fraction and its melt enthalpy). Thereby rather high amounts (rather high melt enthalpy [J/g]) of polymer fractions crystallizing at high temperatures indicate a rather high amount of thick lamellae.
It has been recognized that the improved balance between the mechanical and process properties can be achieved with a propylene copolymer having a specific lamellar thickness distribution, i.e. a propylene copolymer comprising a fraction with a lamella thickness of more than 9.0 nm. More preferably the propylene copolymer comprises a fraction with a lamella thickness of more than 9.2 nm, still more preferably of more than 9.5 nm. Preferred ranges for said fraction are from 9.0 to 12.0 nm, more preferred from 9.2 to 11.0 nm.
A further requirement of the above defined fraction is that it represents the largest fraction of all fractions, in particular compared to the fractions with a lamella thickness below 9.0 nm, of the propylene copolymer. Accordingly the propylene copolymer comprises a fraction with a lamella thickness of more than 9.0 nm (the other preferred values for the lamella thickness are given above) having a higher melt enthalpy [J/g] as each lamella fraction with a lamella thickness below 9.0 nm. More preferably the fraction with a lamella thickness of more than 9.0 nm has melt enthalpy of more than 20.0 J/g, still more preferably of more than 21.0 J/g. Concerning the fractions below 9.0 nm it is preferred that the they have a melt enthalpy of not more than 30.0 J/g. It is in particular preferred that the fractions with a lamella thickness in the range of 6.5 to 9.0 nm have a melt enthalpy in the range of 15.0 to 30.0 J/g.
The propylene copolymer according to this invention is further preferably defined by its isotactic sequence length distribution.
The measurement of isotactic sequence length distribution is performed in the instant invention by using the temperature rising elution fraction (TREF) technique (the exact description is given in the experimental part), which fractionates propylene copolymers according to the solubility differences. It has been clearly demonstrated for propylene polymers that the temperature rising elution fraction (TREF) technique fractionates the propylene polymer according to the longest crystallisable sequences in the chain, which increases almost linearly with the elution temperature (P. Ville et al., Polymer 42 (2001) 1953-1967). Hence the higher the maximum temperature the longer are the isotactic sequences. The results further showed that the temperature rising elution fraction (TREF) technique does not strictly fractionate polypropylene according to tacticity but according to the longest crystallisable sequences in the chain. The solubility of a polypropylene polymer chain hence is influenced only by the concentration and distribution of sterical defects. Insofar the temperature rising elution fraction (TREF) technique is an appropriate method to characterize the inventive propylene copolymer further.
Thus it is preferred that the propylene copolymer posses a distribution curve of the average isotactic chain length featured by at least two distinct maxima, i.e. the comonomer units are not equally distributed among the individual chains of the propylene copolymer. Accordingly it is preferred that the temperature rising elution fractionation (TREF) curve of the inventive propylene copolymer comprises at least two local maxima
More preferably the area below the absolute maximum of that the temperature rising elution fractionation (TREF) function is in the range of 50 to 85 wt.-%, more preferably in the range of 50 to 80 and yet more preferably in the range of 55 to 80 wt.-%. With regard to the area below the relative maximum of the temperature rising elution fractionation (TREF) function as defined above it is preferred that it is in the range of 10 to 30 wt.-%, more preferably in the range of 10 to 25 wt.-%.
The further features mentioned below apply to all embodiments described above, i.e. the first, second, third and the forth embodiment as defined above.
As stated above, the benefit of the present invention can be reached over a broad range of the molecular weight. Accordingly the melt flow rate (MFR) of propylene copolymer can vary over a broad spectrum. The melt flow rate (MFR) 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 melt flow rate (MFR) 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 at 230° C. (ISO 1133) is denoted as MFR2. Accordingly, it is preferred that in the present invention the terpolymer has an MFR2 in a range of 0.1 to 500.0 g/10 min, more preferably of 0.5 to 100.0 g/10 min, still more preferred of 1.0 to 80.0 g/10 min.
The molecular weight distribution (MWD) is expressed as the ratio of weight average molecular weight (Mw) and number average molecular weight (Mn). The number average molecular weight (Mn) is an average molecular weight of a polymer expressed as the first moment of a plot of the number of molecules in each molecular weight range against the molecular weight. In effect, this is the total molecular weight of all molecules divided by the number of molecules. In turn, the weight average molecular weight (Mw) is the first moment of a plot of the weight of polymer in each molecular weight range against molecular weight.
The number average molecular weight (Mn) and the weight average molecular weight (Mw) as well as the molecular weight distribution (MWD) are determined by size exclusion chromatography (SEC) using Waters Alliance GPCV 2000 instrument with online viscometer. The oven temperature is 140° C. Trichlorobenzene is used as a solvent (ISO 16014).
It is preferred that the propylene copolymer of the present invention has a weight average molecular weight (Mw) from 10,000 to 2,000,000 g/mol, more preferably from 20,000 to 1,500,000 g/mol.
The number average molecular weight (Mn) of the propylene copolymer is preferably in the range of 5,000 to 750,000 g/mol, more preferably from 10,000 to 750,000 g/mol.
As a broad molecular weight distribution (MWD) improves the processability of the polypropylene the molecular weight distribution (MWD) is preferably up to 20.0, more preferably up to 10.0, still more preferably up to 8.0.
Moreover it is preferably desired that the propylene copolymer has a rather high melting point (Tm) and crystallization temperature (Tcryst).
Thus the propylene copolymer preferably fulfils the equation (4), more preferably the equation (4a), still more preferably the equation (4b), yet more preferably the equation (4c)
Tm[° C.]+5.29·comonomer[wt.-%]<178.5 (4)
Tm[° C.]+5.00·comonomer[wt.-%]<178.5 (4a)
Tm[° C.]+4.50·comonomer[wt.-%]<178.5 (4b)
Tm[° C.]+4.5·comonomer[wt.-%]<178.5 (4c)
in case the comonomer content is equal or below 5.09 wt.-% (5.1 wt.-% for equation (4c)), or
the propylene copolymer preferably fulfils the equation (5), more preferably the equation (5a), still more preferably the equation (5b), yet more preferably the equation (5c)
Tm[° C.]+5.29·comonomer[wt.-%]>178.5 (5)
Tm[° C.]+5.00·comonomer[wt.-%]>178.5 (5a)
Tm[° C.]+4.50·comonomer[wt.-%]>178.5 (5b)
Tm[° C.]+4.5·comonomer[wt.-%]>178.5 (5c)
in case the comonomer content is more than 5.09 wt.-% (5.1 wt.-% for equation (5c)),
wherein
Tm is the melting temperature and
comonomer is the weight ratio of the comonomer to the sum of monomers present in said polypropylene copolymer (comonomer/(comonomer+propylene)).
It is in particular preferred, that the melting point of the propylene copolymer is at least 147° C. (Tm).
Alternatively or additionally it is preferred that the propylene copolymer preferably fulfils the equation (6), more preferably the equation (6a), still more preferably the equation (6b), yet more preferably the equation (6c)
Tcryst[° C.]+7.29·comonomer[wt.-%]<139.5 (6)
Tcryst[° C.]+7.00·comonomer[wt.-%]<139.5 (6a)
Tcryst[° C.]+6.50·comonomer[wt.-%]<139.5 (6b)
Tcryst[° C.]+6.5·comonomer[wt.-%]<139.5 (6c)
in case the comonomer content is equal or below 5.03 wt.-% (5.0 wt.-% for equation (6c)), or
the propylene copolymer preferably fulfils the equation 7, more preferably the equation (7a), still more preferably the equation (7b), yet more preferably the equation (7c)
Tcryst[° C.]+7.2857·comonomer[wt.-%]>139.5 (7)
Tcryst[° C.]+7.00 comonomer[wt.-%]>139.5 (7a)
Tcryst[° C.]+6.50·comonomer[wt.-%]>139.5 (7b)
Tcryst[° C.]+6.5·comonomer[wt.-%]>139.5 (7c)
in case the comonomer content is more than 5.03 wt.-% (5.0 wt.-% for equation (7c)),
wherein
Tcryst is the crystallization temperature and
comonomer is the weight ratio of the comonomer to the sum of monomers present in said polypropylene copolymer (comonomer/(comonomer+propylene)).
It is in particular preferred, that the crystallization temperature (Tcryst) is at least 95° C.
In addition it is appreciated that the inventive propylene copolymer has good optical properties. Thus it is preferred that propylene copolymer has a haze of not more than 40, still more preferred not more than 35 measured according to ASTM D 1003-92.
The propylene copolymer as defined in the four embodiments above is preferably produced in the presence of a catalyst system as defined in the instant invention above. Thereby the polymerization may a single- or multistage process polymerization of propylene and comonomer such as bulk polymerization, gas phase polymerization, slurry polymerization, solution polymerization or combinations thereof using the above defined catalyst system. Preferably the process comprises also a prepolymerization with catalyst system of the instant invention. More preferably the propylene copolymer is produced 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 slurry reactor designates any reactor, such as a continuous or simple batch stirred tank reactor or loop reactor, operating in bulk or slurry and in which the polymer forms in particulate form. “Bulk” means a polymerization in reaction medium that comprises at least 60 wt-% monomer. According to a preferred embodiment the slurry reactor comprises a bulk loop reactor. This alternative is particularly suitable for producing bimodal propylene copolymer. By carrying out the polymerization in the different polymerization reactors in the presence of different amounts of hydrogen, the MWD of the product can be broadened and its mechanical properties and processability improved. It is also possible to use several reactors of each type, e.g. one loop reactor and two or three gas phase reactors or two loops and one gas phase reactor, in series.
“Gas phase reactor” means any mechanically mixed or fluid bed reactor. Preferably the gas phase reactor comprises a mechanically agitated fluid bed reactor with gas velocities of at least 0.2 msec.
The particularly preferred embodiment of the invention comprises carrying out the polymerization in a process comprising loop and gas phase reactors in a cascade where the loop reactor operates in liquid propylene and at high polymerization temperatures. The second polymerization step is made in gas phase reactor(s) in order to broaden the molar mass distribution of the propylene copolymer.
Considering the detailed information in this description, the following embodiments are especially preferred:
[0001] A catalyst system comprising
R′R″Si(OCH2CH3)2 (IV)
IV(XS)[dl/g]−0.3085·IV[dl/g]>−0.1143 (2)
IV(XS)[dl/g]+0.0083MFR[g/10min]>0.601 (3)
The present invention will now be described in further detail by the examples provided below.
The following definitions of terms and determination methods apply for the above general description of the invention as well as to the below examples unless otherwise defined.
Number average molecular weight (Mn), weight average molecular weight (Mw) and molecular weight distribution (MWD) are determined by size exclusion chromatography (SEC) using Waters Alliance GPCV 2000 instrument with online viscometer. The oven temperature is 140° C. Trichlorobenzene is used as a solvent (ISO 16014).
MFR2 is measured according to ISO 1133 (230° C., 2.16 kg load).
Comonomer content is measured with Fourier transform infrared spectroscopy (FTIR) calibrated with 13C-NMR. When measuring the ethylene content in polypropylene, a thin film of the sample (thickness about 250 mm) was prepared by hot-pressing. The area of —CH2— absorption peak (800-650 cm−1) was measured with Perkin Elmer FTIR 1600 spectrometer. The method was calibrated by ethylene content data measured by 13C-NMR.
Melting temperature Tm, crystallization temperature Tc, and the degree of crystallinity is measured with Mettler TA820 differential scanning calorimetry (DSC) on 5-10 mg samples. Both crystallization and melting curves were obtained during 10° C./min cooling and heating scans between 30° C. and 225° C. Melting and crystallization temperatures were taken as the peaks of endotherms and exotherms. Also the melt- and crystallization enthalpy (Hm and Hc) were measured by the DSC method according to ISO 11357-3.
Haze is determined by ASTM D1003-92.
Intrinsic viscosity is measured according to DIN ISO 1628/1, October 1999 (in Decalin at 135° C.).
The xylene solubles (XS, wt.-%): Analysis according to the known method: 2.0 g of polymer is dissolved in 250 ml p-xylene at 135° C. under agitation. After 30±2 minutes the solution is allowed to cool for 15 minutes at ambient temperature (21° C.) and then allowed to settle for 30 minutes at 25±0.5° C. The solution is filtered and evaporated in nitrogen flow and the residue dried under vacuum at 90° C. until constant weight is reached.
XS %=(100×m1×v0)/(m0×v1), wherein
m0=initial polymer amount (g)
m1=weight of residue (g)
v0=initial volume (ml)
V1=volume of analyzed sample (ml)
Stepwise Isothermal Segregation Technique (SIST): The isothermal crystallisation for SIST analysis was performed in a Mettler TA820 DSC on 3±0.5 mg samples at decreasing temperatures between 200° C. and 105° C.
The samples were melted at 225° C. for 5 min,
The melting curve is obtained by heating the cooled sample at a heating rate of 10° C./min up to 200° C. All measurements were performed in a nitrogen atmosphere.
The minima of the melting curve (see
wherein T0=457 K, ΔH0=184×106 J/m3, σ=0.0496 J/m2, L is the lamella thickness and Tm is the measured temperature (K). Such obtained lamella thicknesses define the fractions of each polymer sample (compare table 4).
The melt enthalpy [J/g] of each fraction of the polymer sample as defined above is obtained as follows:
In general the melt enthalpy is calculated from the quotient of the heat flow volume and initial weight of the sample. The heat flow volume is recorded as function of temperature, i.e. the melting curve (heat flow (endo) downwards as a function of temperature; see
Accordingly the relative maxima may be mathematically understood, i.e. a point x* is a relative maximum of a function ƒ if there exists some ε>0 such that ƒ(x*)≧ƒ(x) for all x with |x-x*|<ε. Furthermore, in case of shoulders, the first derivative of the function (the measured melting curve) must lead to a relative maximum at the relative maximum of said function. Excluded are those inflection points that are located between two relative extrema.
Flexural modulus is measured according to ISO 178
Charpy impact strength is measured according ISO 179 at 23° C. and ISO 179-2 in the temperature range of 0-20° C.
The chemical composition distribution was determined by analytical Temperature Rising Elution Fractionation (a-TREF) as described in J. B. P. Soares, A. E. Hamielec; Temperature rising elution fractionation of linear polyolefins; Polymer 1995, 36 (8), 1639-1654 and Soares, J. B. P., Fractionation, In: Encyclopedia Of Polymer Science and Technology, John Wiley & Sons, New York, pp. 75-131, Vol. 10, 2001. The separation of the polymer in a-TREF is according to crystallinity. The TREF profiles were generated using a CRYSTAF-TREF 200+ instrument manufactured by PolymerChar S.A. (Valencia, Spain). The experimental procedure, as described in N. Aust, M. Gahleitner, K. Reichelt, B. Raninger; Optimization of run parameters of temperature-rising elution fractionation with the aid of a factorial design experiment; Polymer Testing 2006, 25 (7), 896-903 was as follows:
In the dissolution step, the polymer sample was dissolved in 1,2,4-trichlorobenzene (TCB, 2 to 4 mg/mL, stabilized with 300 mg/L 2,6-Di tert butyl-4-methyl-phenol) in one of the vessels at a concentration of 4 mg/mL at 160° C. for 90 min. The sample was then loaded into the TREF column (7.8 mm inner diameter, 15 cm length, packed with stainless steal shots as inert support), and held at 110° C. for 30 min for stabilization. The polymer sample was crystallized and precipitated onto the support inside the TREF column by a slow reduction of the temperature to 30° C. under a constant cooling rate (0.1° C./min). The column temperature was kept at 30° C. for 25 min for stabilization before the elution step started. In the elution step, a solvent (TCB) flowed through the column at a constant flow rate of 0.5 mL/min while the temperature in the column was first held for 10 min at 30° C. to measure the remaining soluble fraction followed by slowly increasing the temperature to 130° C. at a constant heating rate (0.5° C./min). The concentration of the polymer being eluted was measured during the whole elution step with an infrared detector (measuring the C—H absorption at 3.5 microns wavelength) and recorded together with the temperature in the column oven as a function of time. The concentration signal was plotted as a function of the elution temperature (TREF profile). For convenience the under isothermal conditions (30° C., 10 min) measured soluble fraction was added to this plot by converting the time into temperature using the constant heating rate of 0.5° C./min. In the TREF calculation software (by Polymer Char, version 07a) the concentration plot (TREF profile) was normalized including the soluble fraction.
DIPDES; MFR 10 g/10 min; C2 content 6.5 wt.-% (Inventive) The propylene polymers used for the present invention were prepared according to the following procedure:
The monomers used were additionally purified via BASF catalyst R3-11 (Cu), GIRDLER catalyst (CuO/ZnO) and molecular sieves 4 and 10 Å.
A 20 l 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 the reactor has been vacuumed and filled with 5350 g propylene by weighing and 18 nl H2 by pressure monitoring from a 50 l steel cylinder. 35 mg of Polytrack 8502-catalyst are activated for 10 minutes with a mixture of Triethylaluminium (TEAL solution in hexane 1 mol/l) and Di-iso-propyldiethoxysilane as donor (0.3 mol/l in hexane)—in a molar ratio of 10 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 250 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 16 min. After holding that temperature for 1 hour and feeding constantly 1968 mln/min ethylene into the reactor polymerisation is stopped by flashing propylene and cooling to room temperature.
The amount of polymer powder was 1654 g and the MFR (230° C., 2.16 kg) of the powder was 10 g/10 min, C2 content was 6.5 wt.-%. After spilling the reactor with N2 the polymer powder is transferred to a steel container.
100 g powder, used for characterization, was stabilized with 0.1 wt.-% of Sandostab P-EPQ and 0.2 wt.-% of Ionol CP in acetone and dried over night in a hood and additionally for 2 hours at 50° C. under vacuum.
For mechanical testing reactor product was pelletised via TSE16 extruder (PRISM) and additivated with 0.15 wt.-% Irganox B225 and 0.05 wt.-% Ca-stearate. All samples have been nucleated with 0.2% 1,3:2,4-bis(3,4-dimethylbenzylidene)sorbitol.
DCPDMS; MFR 9 g/10 min; C2 content 6.5 wt.-% (Inventive) The propylene polymers used for the present invention were prepared according to the following procedure:
The monomers used were additionally purified via BASF catalyst R3-11 (Cu), GIRDLER catalyst (CuO/ZnO) and molecular sieves 4 and 10 Å.
A 20 l 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 the reactor has been vacuumed and filled with 5350 g propylene by weighing and 88 nl H2 by pressure monitoring from a 50 l steel cylinder. 35 mg of Polytrack 8502-catalyst are activated for 10 minutes with a mixture of Triethylaluminium (TEAl; solution in hexane 1 mol/l) and Dicyclopentyldimethoxysilane as donor (0.3 mol/l in hexane)—in a molar ratio of 10 after a contact time of 5 min—and 10 ml hexane in a catalyst feeder. The molar ratio of TEAl and Ti of catalyst is 250. After activation the catalyst is spilled with 250 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 16 min. After holding that temperature for 1 hour and feeding constantly 3668 mln/min ethylene into the reactor polymerisation is stopped by flashing propylene and cooling to room temperature.
The amount of polymer powder was 2884 g and the MFR (230° C., 2.16 kg) of the powder was 9 g/10 min, C2 content was 6.5 wt.-%. After spilling the reactor with N2 the polymer powder is transferred to a steel container.
100 g powder, used for characterization, was stabilized with 0.1 wt.-% of Sandostab P-EPQ and 0.2 wt.-% of Ionol CP in acetone and dried over night in a hood and additionally for 2 hours at 50° C. under vacuum.
For mechanical testing reactor product was pelletised via TSE16 extruder (PRISM) and additivated with 0.15 wt.-% Irganox B225 and 0.05 wt.-% Ca-stearate. All samples have been nucleated with 0.2% 1,3:2,4-bis(3,4-dimethylbenzylidene)sorbitol.
DIPDES; MFR 11 g/10 min; C2 content 4.5 wt.-% (Inventive) The propylene polymers used for the present invention were prepared according to the following procedure:
The monomers used were additionally purified via BASF catalyst R3-11 (Cu), GIRDLER catalyst (CuO/ZnO) and molecular sieves 4 and 10 Å.
A 20 l autoclave reactor has been purified by mechanical cleaning, washing with hexane and heating under vacuum/N/cycles at 160° C. After testing for leaks with 30 bar N2 over night the reactor has been vacuumed and filled with 5350 g propylene by weighing and 16 nl H2 by pressure monitoring from a 50 l steel cylinder. 35 mg of Polytrack 8502-catalyst are activated for 10 minutes with a mixture of Triethylaluminium (TEAl; solution in hexane 1 mol/l) and Di-iso-propyldiethoxysilane as donor (0.3 mol/l in hexane)—in a molar ratio of 10 after a contact time of 5 min—and 10 ml hexane in a catalyst feeder. The molar ratio of TEAL and Ti of catalyst is 250. After activation the catalyst is spilled with 250 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 16 min. After holding that temperature for 1 hour and feeding constantly 880 mln/min ethylene into the reactor polymerisation is stopped by flashing propylene and cooling to room temperature.
The amount of polymer powder was 1474 g and the MFR (230° C., 2.16 kg) of the powder was 11 g/10 min, C2 content was 4.5 wt.-%. After spilling the reactor with N2 the polymer powder is transferred to a steel container.
100 g powder, used for characterization, was stabilized with 0.1 wt.-% of Sandostab P-EPQ and 0.2 wt.-% of Ionol CP in acetone and dried over night in a hood and additionally for 2 hours at 50° C. under vacuum.
For mechanical testing reactor product was pelletised via TSE16 extruder (PRISM) and additivated with 0.15 wt.-% Irganox B225 and 0.05 wt.-% Ca-stearate. All samples have been nucleated with 0.2% 1,3:2,4-bis(3,4-dimethylbenzylidene)sorbitol.
DCPDMS; MFR 11 g/10 min; C2 content 4.5 wt.-% (Comparison) The propylene polymers used for the present invention were prepared according to the following procedure:
The monomers used were additionally purified via BASF catalyst R3-11 (Cu), GIRDLER catalyst (CuO/ZnO) and molecular sieves 4 and 10 Å.
A 20 l 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 the reactor has been vacuumed and filled with 5350 g propylene by weighing and 80 nl H2 by pressure monitoring from a 50 l steel cylinder. 35 mg of Polytrack 8502-catalyst are activated for 10 minutes with a mixture of Triethylaluminium (TEAl; solution in hexane 1 mol/l) and Dicyclopentyldimethoxysilane as donor (0.3 mol/l in hexane)—in a molar ratio of 10 after a contact time of 5 min—and 10 ml hexane in a catalyst feeder. The molar ratio of TEAl and Ti of catalyst is 250. After activation the catalyst is spilled with 250 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 16 min. After holding that temperature for 1 hour and feeding constantly 1612 mln/min ethylene into the reactor polymerisation is stopped by flashing propylene and cooling to room temperature.
The amount of polymer powder was 2313 g and the MFR (230° C., 2.16 kg) of the powder was 11 g/10 min, C2 content was 4.5 wt.-%. After spilling the reactor with N2 the polymer powder is transferred to a steel container.
100 g powder, used for characterization, was stabilized with 0.1 wt.-% of Sandostab P-EPQ and 0.2 wt.-% of Ionol CP in acetone and dried over night in a hood and additionally for 2 hours at 50° C. under vacuum.
For mechanical testing reactor product was pelletised via TSE16 extruder (PRISM) and additivated with 0.15 wt.-% Irganox B225 and 0.05 wt.-% Ca-stearate. All samples have been nucleated with 0.2% 1,3:2,4-bis(3,4-dimethylbenzylidene)sorbitol.
All other examples given in the tables (inventive and comparison examples) can be analogous obtained by changing the hydrogen content and the ethylene feed as well as the external donor in known manner.
The donors used have the following abrevations:
| Number | Date | Country | Kind |
|---|---|---|---|
| EP 07010182.9 | May 2007 | EP | regional |
This application is a divisional of U.S. patent application Ser. No. 12/451,583 filed on Nov. 19, 2009, which is a National Stage of International Application No. PCT/EP2008/056300 filed May 21, 2008. This application claims priority to European Patent Application No. 07010182.9 filed on May 22, 2007. The disclosures of the above applications are incorporated herein by reference.
| Number | Date | Country | |
|---|---|---|---|
| Parent | 12451583 | Nov 2009 | US |
| Child | 12927882 | US |
