Bopp film with homogeneous structure

FIELD: chemistry.

SUBSTANCE: invention relates to polypropylene, a method for production thereof and a film capacitor made from said polypropylene. The polypropylene has a melting temperature (Tm) measured according to ISO 11357-3 of at least 151.0°C and xylene cold soluble fraction (XCS) of not more than 1.5 wt %. According to stepwise isothermal segregation technique (SIST) results, 45.0 to 67.0 wt % of the crystalline fraction has a lamella thickness in the range of 7.70 to 14.09 nm and 18.0 to 50.0 wt % of the crystalline fraction has a lamella thickness greater than 14.09 nm.

EFFECT: disclosed polypropylene has high heat resistance and enables to obtain biaxially oriented polypropylene (BOPP) and/or a film capacitor with high electrical breakdown strength and a high β parameter.

13 cl, 1 dwg, 9 tbl

 

The present invention relates to a new and polypropylene film capacitor from the specified polypropylene, as well as to obtain the specified polypropylene.

Film capacitors must withstand extreme conditions such as high temperature and high electrical breakdown strength. Additionally, it should be understood that film capacitors have good mechanical properties such as high rigidity. With regard to power electrical breakdown, you must take into account that all properties of the system or quality system (here: film capacitor) is dominated by very small private properties of such systems. Unfortunately, it is not the strongest indicator that has a value, this is the weakest indicator, which regulates the entire performance. Thus, it should be understood that if the sample film capacitor has a high electrical breakdown, it also ensures that different samples of the same film capacitor also on average demonstrate the stated figures electrical breakdown. Therefore, in other words, film capacitor must be continuously the same properties in each location specified film.

Accordingly, to assess whether film capacitor throughout high rates ELEH the electrical breakdown from the specified film is cut into ten samples and each sample is subjected to an independent measurement of the breakdown according to IEC 60243. Small samples when measuring gain irreversible damage. Because of the stochastic nature of the breakdown field breakdown, recorded for each of the 10 samples (from the same film), have a fairly large scatter, which is not a Gaussian distribution, and is known as the distribution Weibull. This so-called distribution of extreme values. Therefore, it is necessary to look at the scatter of results, not only on the breakdown voltage. The scatter of the data Weibull characterized β-parameter. The lower the β-parameter, the greater the difference in the results of electrical breakdown. With regard to reliability, the dispersion should be as low as possible, hence, β is a parameter should be as large as possible. This means that the task is not only to achieve high voltage electrical breakdown, but also high β-parameter. Only high β-option ensures that the film capacitor will actually withstand high voltage electrical breakdown.

Therefore, an object of the present invention relates to polypropylene, which ensures that a film capacitor obtained from Pego, withstands high strength electric field without failure, is this quality can be ensured sufficiently high β-parameter. Preferably such propylene additionally it has a high heat resistance.

The present invention is based on the discovery that improved behavior breakdown, whereas β is the parameter that can be achieved when using polypropylene for a film capacitor, characterized by a high amount of fat the leafs defined using the stepped isothermal stratification (SIST). Such polypropylene allows to obtain a biaxially oriented polypropylene (BOPP) and/or film capacitor with high electrical breakdown strength and high β-parameter.

Therefore, the present invention relates to a polypropylene

(a) melting temperature (Tm), measured according to ISO 11357-3, at least 151,0°C,

(b) a fraction, soluble in cold xylene (XCS), not more than 1.5 wt.% and

(c) at least 18.0 wt.%, more preferably at least 18.3 wt.%, even more preferably at least 18.6 wt.%, even more preferably at least 19.0 wt.% the crystalline fraction of the thickness of the leafs more than 14,09 nm, where this fraction is determined using the stepped isothermal stratification (SIST).

Therefore, the present invention in particular relates to polypropylene

(a) temperature is dependent on the melting point (T m), measured according to ISO 11357-3, at least 151,0°C,

(b) a fraction, soluble in cold xylene (XCS), not more than 1.5 wt.% and

(c) at least 18.0 wt.%, more preferably at least 18.3 wt.%, even more preferably at least 18.6 wt.%, even more preferably at least 19.0 wt.% the crystalline fraction of the thickness of the leafs more than 14,09 nm, where this fraction is determined using the stepped isothermal stratification (SIST), where

(i) the polypropylene is melted at a temperature of 225°C for 5 minutes,

(ii) then cooled with 80°C/min to 145°C,

(iii) was incubated for 2 hours at a temperature of 145°C,

(iv) then cooled with 80°C./min to 135°C

(v) was incubated for 2 hours at a temperature of 135°C

(vi) then cooled with 80°C/min to 125°C,

(vii) was incubated for 2 hours at a temperature of 125°C,

(viii) then cooled with 80°C./min to 115°C,

(ix) was incubated for 2 hours at a temperature of 115°C,

(x) then cooled with 80°C./min to 105°C,

(xi) was incubated for 2 hours at 105°C,

(xii) then cooled with 80°C./min to -10°C and

(xiii) then heated at 10°C/min until 200°C To produce the melting curve of the specified polypropylene at a temperature in the range from 50 to 200°C, are used to calculate the allocation of the value of the thickness of the leafs according to the equation Thomson-Gibbs (Equation 1)

Tm=T0(1-2σΔH0L)(1)

where

T0=457,

ΔN0=134×106J/m3,

σ=0,0496 j/m2,

Tmis the measured temperature (K) and

L represents the thickness of the leafs (nm).

Unexpectedly, the authors of the present invention have found that such a polypropylene allows to obtain a film capacitor with a high electrical breakdown, which also have high values of β parameter (see Table). In particular, it was found that such high rates of β-parameter is achievable only in the case of polypropylene, characterized by a significant amount of fat of the leafs, the leafs, the thickness is at least 14,09 nm.

Hereinafter the present invention will be described in more detail.

The polypropylene of the present invention can represent any polypropylene, but preferably, it was a random copolymer of propylene homopolymer or propylene, the latter being preferred.

Used in the description of the present patent application, the term "random-copolyme is" preferably means according to IUPAC, that is, as the polymer, which can detect a given Monomeric unit at any given site in the polymer chain.

In the case when the polypropylene is a random copolymer of propylene, it includes monomers, copolymerisate with propylene, for example comonomers such as ethylene and/or C4-C20alpha-olefins, in particular ethylene and/or C4-C10alpha-olefins, such as 1-bution and/or 1-hexene. Preferably a random copolymer of propylene comprises, essentially consists of monomers, copolymerizing with propylene from the group consisting of ethylene, 1-Butana and 1-hexene. Namely, random copolymer of propylene comprises unlike propylene ethylene units and/or 1-butene. In a preferred variant embodiment of the present invention is a random copolymer of propylene comprises only ethylene and propylene units. The content of the co monomer in the random copolymer of propylene preferably relatively low, i.e. up to 6.0 wt.%, more preferably in the range of 0.5 to 6.0 wt.%, even more preferably in the range of 0.5 to 4.0 wt.%, even more preferably in the range from 0.5 to 2.0 wt.%.

Used in the description of the present patent application, the term " homopolymer refers to polypropylene, essentially consisting of propylene units, i.e. at least 99 wt.%, predpochtitel is but at least 99.5 wt.%, more preferably at least 99.8 wt.% propylene units. In a preferred variant embodiment of the present invention the propylene homopolymer composed only of propylene units.

Preferably the polypropylene is isotactic. Therefore, it is clear that the polypropylene has a rather high pentad concentration, i.e. more than 90%, more preferably more than 92%, more preferably more than 93% and even more preferably more than 95%, such as more than 99%.

Commercially available propylene usually used to obtain capacitors, characterized by a high content of fraction soluble in cold xylene (XCS). The polypropylene of the present invention is characterized by a rather low content of fraction soluble in cold xylene (XCS), amounting to less than 1.5 wt.%, more preferably less than 1.3 wt.%, even more preferably less than 1.0 wt.%, such as less than 0.8 wt.%. Therefore, it is clear that the polypropylene of the present invention has a content of fraction soluble in cold xylene (XCS), ranging from 0.3 to 1.5 wt.%, more preferably in the range from 0.3 to 1.3 wt.%, even more preferably in the range from 0.4 to 1.0 wt.%, such as in the range from 0.4 to 0.8 wt.%.

The fraction soluble in cold xylene (XCS), to omnitele indicates, the polypropylene is preferably free of any elastomeric component polymer, such as ethylene-propylene rubber. In other words, the polypropylene should not be heterophase polypropylene, i.e. a system consisting of a polypropylene matrix, in which the dispersed phase of elastomer. Such systems are characterized by a high content of fraction soluble in cold xylene.

The polypropylene of the present invention is preferably obtained using the catalytic system, as described in detail below. Accordingly, the polypropylene is not obtained in the presence of a catalyst of Ziegler-Natta. As a rule, polypropylene get when using the catalysts of various types, also essentially different <2,1> regiodirection. Therefore, it is clear that the polypropylene has a <2,1> recidivity defined using13With spectroscopy, equal to or more than 0.4 mol.%, more preferably equal to or more than 0.6 mol.%, such as in the range of 0.7 to 0.9 mol.%.

Additionally, an important aspect of the present invention is that the polypropylene has a relatively high melting point. Therefore, it is clear that the polypropylene of the present invention has a melting temperature (Tm), measured according to ISO 11357-3, at least 151,0°C, bol is e preferably at least 152°C. Therefore, in particular, it is clear that the melting temperature (Tm), measured according to ISO 11357-3, polypropylene is in the range of 151 to 160°C, more preferably in the range from 152 to 155°C, even more preferably in the range from 152 to 159°C. and even more preferably in the range from 152 to 155°C.

Additionally, it is clear that the polypropylene of the present invention has a high crystallization temperature (Tc). Therefore, it is preferable that the polypropylene had a crystallization temperature (Tc), measured according to ISO 11357-3, at least 110°C., more preferably at least 111°C. Accordingly, the polypropylene preferably has a crystallization temperature (Tc), measured according to ISO 11357-3, in the range of 110 to 120°C., more preferably in the range from 111 to 117°C.

Technology stepped isothermal stratification (stepwise isothermal segregation technique) (SIST) provides the ability to determine the distribution of the thickness of the leafs. The method of exact measurements in the following Examples (in particular, the determination of the thickness of the leafs of each fraction and its enthalpy of melting). Thus, a fairly large number (with relatively high enthalpy of fusion [j/g]) of the polymer fractions crystallized at high temperatures, indicates a fairly high number of Tolstikhina. Therefore, it is clear that the polypropylene comprises at least 18.0 wt.%, more preferably at least 18.3 wt.%, even more preferably at least 18.6 wt.%, even more preferably at least 19.0 wt.% the crystalline fraction having a thickness of leafs more than 14,09 nm, where the specified fraction is determined using the stepped isothermal stratification (SIST). In particular, it is preferable that the polypropylene included within from of 18.0 to 50.0 wt.%, more preferably in the range from of 18.0 to 45.0 wt.%, even more preferably in the range from 18.3 to 40.0 wt.%, even more preferably in the range from 19,0 to 35.0 wt.% the crystalline fraction having a thickness of leafs more than 14,09 nm, where the specified fraction is determined using the stepped isothermal stratification (SIST).

Additionally, it is clear that the polypropylene includes not more than 67,0 wt.%, more preferably not more than 66.0 wt.%, such as not more than 65.0 wt.% the crystalline fraction having a thickness of leafs in the range from 7,70 to 14,09 nm. On the other hand, crystalline fraction, having a thickness of leafs in the range from 7,70 to 14,09 nm, should not be too small. Therefore, in addition or alternatively, it is preferable that the upper limit of polypropylene included more than 45 wt is.%, more preferably more than 50 wt.%, even more preferably more than 55 wt.%, even more preferably more than 60 wt.% the crystalline fraction having a thickness of leafs in the range from 7,70 to 14,09 nm. Therefore, it is clear that the polypropylene obtained by the method according to the present invention includes a crystalline fraction having a thickness of leafs in the range from 7,70 to 14,09 nm, the number within 45.0 to 67.0 wt.%, more preferably in the range from 55,0 to 67.0 wt.%, even more preferably in the range from to 60,0 66,0 wt.%, even more preferably in the range from 61,0 up to 65,00 wt.%, such as in the range from 63,0 to 65.0 wt.%.

Additionally, it is desirable that the polypropylene had more than 12.0 wt.%, more preferably more than 14.0 wt.%, such as more than 15.0 wt.% the crystalline fraction having a thickness of leafs in the range from 2.52 to 7,69 nm. Therefore, it is clear that the polypropylene comprises a crystalline fraction having a thickness of leafs in the range from 2.52 to 7,69 nm, in quantities ranging from 12.0 to 22.0 wt.%, more preferably in the range from of 14.0 to 20.0 wt.%, such as in the range from 15.0 to 19.0 wt.%.

The molecular weight distribution (MWD) is the ratio of the number of molecules in the polymer to the individual length of the chain. The molecular weight distribution (MWD) is expressed as the ratio of the bulk molecule the Noah mass (Mw) and srednetsenovoj molecular weight (Mn). Brednikova molecular weight (Mn) represents the average molecular weight of the polymer, expressed as the number of molecules in a static time schedule in each limit molecular weight compared to the molecular weight. In fact it is the total molecular weight of all molecules divided by the number of molecules. In turn, the mass-average molecular mass (Mw) is the static moment of the graph of the weight of the polymer in each limit molecular weight compared to the molecular weight.

Srednecenovogo molecular weight (Mn) and the mass-average molecular weight (Mw) along with the molecular weight distribution (MWD) is determined using exclusion chromatography size (SEC) when the device is used Waters Alliance GPCV 2000 with online viscometer. The temperature of thermostat 140°C. the solvent used trichlorobenzene (ISO 16014).

Accordingly, it is preferable that the polypropylene of the present invention had a mass-average molecular weight (Mw) in the range of 100000 to 600000 g/mol, more preferably in the range from 200000 to 500000 g/mol.

Brednikova molecular weight (Mn) of the polypropylene is preferably in the range from 5000 to 400,000 g/mol, more preferably in the range from 10000 to 300000 g/mol.

A wide molecular weight distribution (MWD) increases the technological characteristics of the poly is ropylene. Therefore, it is clear that the molecular weight distribution (MWD)measured according to ISO 16014, polypropylene is at least 2.8, more preferably at least 3,0, such as 3.3V. On the other hand, a broad molecular weight distribution (MWD) indicates a fairly high number of fractions with low molecular weight, which contribute to the content of fraction soluble in xylene, without improving any dielectric characteristics. Thus, alternatively, in one embodiment, the embodiment of the present invention, the molecular weight distribution (MWD) of the polypropylene is preferably in the range from 2.8 to 8.0, more preferably in the range from 3.0 to 5.0, such as in the range from 3.0 to 3.4, more preferably in the range from 3.3 to 3.5.

Additionally, it is preferable that the polypropylene of the present invention had a speed of melt flow (MFR) in a specific range. The rate of flow of the melt, measured under a load of 2.16 kg at a temperature of 230°C. (ISO 1133), indicate how MFR2(230°C). Therefore, in a preferred variant embodiment of the present invention, the polypropylene has an MFR2(230°C) of more than 2.0 g/10 minutes, more preferably more than 3.0 g/10 minutes. Therefore, it is clear that the MFR2(230°C)measured according to ISO 1133, is within the Ah from 2.0 to 10.0 g/10 minutes, more preferably in the range from 2.0 to 6.0 g/10 minutes, such as in the range from 2.0 to 4.0 g/10 minutes, more preferably in the range from 3.0 to 6.0 g/10 minutes.

Additionally, the polymer may represent unimodal or multimodal, like bimodal, based on the distribution of molecular weight and/or distribution of the content of the co monomer.

Used in the description of the present patent application, the term "multimodal" or "bimodal" refers to the modality of the polymer, that is,

the shape of the distribution curve of molecular weight, which represents a graph of molecular weight fraction as a function of molecular weight,

or

- the shape of the curve of distribution of the content of the co monomer, which represents a graph of the content of the co monomer as a function of molecular weight fractions of the polymer.

In particular, it is preferable that the polypropylene, if it is not unimodal, was multimodal, like bimodal, based on the distribution of molecular weight and/or distribution of the content of the co monomer. Therefore, it is clear that the polypropylene of the present invention includes the first fraction with MFR2(230°C), component in the range from 0.3 to 3.0 g/10 minutes, and the second fraction with MFR2(230°C), component in the range from 1.0 to 50.0 g/10 minutes. Even more preferably, the first fraction has a more Nisku the MFR 2(230°C) compared with the second fraction. Preferably, the first fraction is obtained in the circulation reactor, a second fraction is obtained in the gas-phase reactor.

Additionally, it is clear that the polypropylene has a linear structure and, therefore, has not (or not close) branching. Accordingly, it is clear that the polypropylene of the present invention preferably has a branching index g' of not less than 0.90, preferably more than 0.90, such as at least 0,95. In other words, if the polypropylene has a branching, it is quite moderate. Accordingly, the branching index g' of the polypropylene is preferably in the range from 0.9 to 1.0, more preferably in the range from more than 0.9 to 1.0, such as in the range from 0.96 to 1.0. The branching index g' is defined as g'=[IV]br/[IV]linwhere g' is the branching index, [IVbr] represents the intrinsic viscosity of the branched polypropylene and [IV]linrepresents the intrinsic viscosity of a linear polypropylene with the same mass-average molecular weight (±3%)as the branched polypropylene. Thus, the low index g' is an indicator of highly branched polymer. In other words, if the metric g' decreases, the branching of polypropylene increases. Accurately identify the bookmark index g' is given in the Examples.

Because the polypropylene of the present invention preferably has a non-branched structure, it also contains significant amounts of gel. Gels are a typical phenomenon of crosslinking polypropylene. Therefore, the gel content is a good indicator of chemical modification of polypropylene. Accordingly, the polypropylene of the present invention is characterized by a relatively moderate amounts of gel, that is not more than 0.50 wt.%, more preferably not more than 0.25 wt.%, even more preferably not more than 0.15 wt.%, such as less than 0.15 wt.%, even more preferably not more than 0.10 wt.%, defined as the relative amount of polymer insoluble in boiling xylene (fraction insoluble in boiling xylene XHI). Essentially, in a preferred variant embodiment of the present invention, the gel content is undetectable.

As will be described in detail below, the polypropylene of the present invention obtained using a specific metallocene catalyst system. Accordingly, the polypropylene of the present invention are obtained without the use of a catalyst of Ziegler-Natta. Consequently, additionally it is preferable that the content of residual titanium (Ti) in the polypropylene preferably comprised less than 10 parts per million, sales is more preferably titanium (Ti) is not defined.

Additionally, since the catalyst used in the method according to the present invention is not applied on any carrier, preferably a residue of silicon (Si), measured according to ISO 3451-1 (1997), the polypropylene is less than 10 parts per million, more preferably less than 5 ppm, such as less than 1 part per million. In a particular variant embodiment of the present invention, the silicon (Si) is not defined in the polypropylene.

The present invention not only relates to polypropylene per se, but also refers to its use. Accordingly, the polypropylene is preferably used as a biaxially oriented film and/or film of the capacitor. Additionally, the polypropylene of the present invention has the β-parameter (parameter Weibull) electrical breakdown, measured in accordance with IEC 60243, more than 8, preferably more than 10, even more preferably more than 13, even more preferably more than 15, such as more than 18.

The polypropylene may include additives known from the prior art, such as antioxidants. However, you should avoid any supplements that have a negative impact on the behavior of electrical breakdown.

Additionally, the present invention also relates to a biaxially oriented polypropylene the new film, where polypropylene is polypropylene of the present invention. Preferably biaxially oriented polypropylene film has a score of drawing at least 5 times in the longitudinal direction and 5 times in the transverse direction, more preferably has a hood at least 9 times in the longitudinal direction and 5 times in the transverse direction.

Additionally, the polypropylene of the present invention can be used as film capacitors. In such cases, film capacitor includes at least 80 wt.%, more preferably at least 90 wt.%, even more preferably at least 99 wt.% polypropylene of the present invention. In essentially preferred variant of embodiment of the present invention film capacitor consists of polypropylene according to the present invention. Additionally, it is preferable film capacitor is biaxially oriented polypropylene film of the present invention.

Next will be described in more detail obtaining the polypropylene of the present invention.

The polypropylene of the present invention, in particular, the benefits of using new catalytic systems with a surface area, measured according to ASTM D of 3,663 (N2), less than 20 m2/g and including the catalysis of the torus, representing the transition metal compounds with formula (I):

(Cp)2RZrX2(I),

where

X is independently a monovalent anionic ligand, such as σ-ligand,

Cf is an organic ligand selected from the group consisting of unsubstituted cyclopentadienyl, unsubstituted indenyl, unsubstituted tetrahydroindene, unsubstituted fluorenyl, substituted cyclopentadienyl, substituted indenyl, substituted tetrahydroindene and substituted fluorenyl,

provided that both SR-a ligand selected from the above group and both the CP-ligand is chemically the same, i.e. identical,

R represents a bridging group linking two CP-ligand, where R has the formula (II):

-Y(R')2-(2),

where

Y is C, Si or Ge, preferably Si,

R' - C1-C20alkyl, C4-C10cycloalkyl,6-C12aryl, C7-C12arylalkyl or trimethylsilyl,

provided that both R'is a residue selected and the above groups, and both R'-residue chemically different.

Through the use of catalytic systems with a very small surface area, including the specific catalyst, it is possible to obtain the above-mentioned polypropylene.

Additionally, it is preferable that the catalytic system had a surface area of less than 15 m2/g, more preferably less than 10 m2/g and most preferably less than 5 m2/g surface Area in the present invention is measured according to ASTM D of 3,663 (N2).

Additionally, it is clear that the catalyst system has a porosity less than that of 1.30 ml/g and more preferably less than 1.00 ml/g, the Porosity is measured in accordance with ASTM 4641 (N2). In another preferred variant of embodiment of the present invention, the porosity is not determinable by using the method applied according to ASTM 4641 (N2).

In a particular preferred variant of embodiment of the present invention, the porosity is not defined when using the method according to ASTM 4641 (N2) and has a surface area, measured according to ASTM D of 3,663 (N2), less than 5 m2/year

Used in the description of the present patent application the term "δ-ligand" is a common value, that is the group that is associated with the metal in one or more position Sigma-bond. Preferably monovalent anionic ligand represents halogen, in an hour the particular chlorine (Cl).

Preferably the catalyst has the formula (I)above,

where each X represents a chlorine (Cl) and/or both identical Cf-substituted ligand.

Optional one or more substituent(s) relationship(s) with cyclopentadienyl, indenolol, tetrahydroindene or fluorenyl and can be selected from the group comprising halogen, acyclic carbon residue (for example, C1-C20alkyl, C2-C20alkenyl,2-C20quinil,3-C12cycloalkyl,6-C20aryl or7-C20arylalkyl)3-C12-cycloalkyl containing 1, 2, 3 or 4 heteroatom(s) in the ring, With6-C20-heteroaryl,1-C20-haloalkyl, -SiR"3, -OsiR"3, -SR", -PR"2and-NR2,

where each R" is independently hydrogen or an acyclic carbon residue, for example, C1-C20alkyl, C2-C20alkenyl,2-C20quinil,3-C12cycloalkyl or6-C20aryl.

More preferably, both identical to Cf-ligand are indenolol group, where each angenlina group bears one or more Deputy, as mentioned above. More preferably, each of the identical CP-ligands is indenolol group bearing two Deputy, as described above, provided that the substituents are chosen so the way, both Cf-ligand have the same chemical structure, i.e. both the CP-ligand have the same substituents that are associated chemically with the same indenolol group.

Even more preferably, both identical to Cf-ligand are indenolol group, where angenlina group includes at least five-membered ring indenyl, more preferably in position 2, the Deputy is chosen from the group consisting of alkyl, such as C1-C6alkyl, for example methyl, ethyl, isopropyl, trialkylborane, where each alkyl is independently selected from C1-C6of alkyl, such as methyl or ethyl, provided that angenlina group both CP-ligands have the same chemical structure, i.e. both the CP-ligand have the same substituents that are associated chemically with the same indenolol group.

Even more preferably, both identical to Cf-ligand are indenolol group, where angenlina group includes at least six-membered ring indenyl, more preferably in position 4, Deputy chosen from the group consisting of C6-C20aromatic ring, such as phenyl or naphthyl, preferably phenyl, which is optionally substituted by one or more Deputy, such as C1-C6alkyl, and a heteroaromatic ring, provided that the Indus is safe group both CP-ligands have the same chemical structure, that is, both the CP-ligand have the same substituents that are associated chemically with the same indenolol group.

Even more preferably, both identical to Cf-ligand are indenolol group, where angenlina group includes the five-membered ring indenyl, more preferably in position 2, the Deputy and six-membered ring indenyl more preferably in position 4, additional Deputy where the Deputy five-membered ring selected from the group consisting of alkyl, such as C1-C6alkyl, for example methyl, ethyl, isopropyl, trialkylborane, preferably methyl, and additional Deputy six-membered ring selected from the group consisting of C6-C20aromatic ring, such as phenyl or naphthyl, preferably phenyl, which is optionally substituted by one or more Deputy, such as C1-C6alkyl, such as tert-butylmethyl, and heteroatomic ring, provided that angenlina group both CP-ligands have the same chemical structure, i.e. both the CP-ligand have the same substituents that are associated chemically with the same indenolol group.

Essentially it is clear that the two are identical Cf-ligand are indenolol group, where angenlina group includes the five-membered ring indenyl in position 2, the Deputy and sixth is ichinoe ring indenyl in position 4, additional Deputy where the Deputy five-membered ring selected from the group consisting of ethyl, methyl and isopropyl, and additional Deputy six-membered ring selected from the group consisting of phenyl, C1-C6of alkyl, substituted phenyl such as 4-tert-butyl-phenyl, naphthyl and C1-C6of alkyl, substituted naphthyl, provided that indenyl both CP-ligands have the same chemical structure, i.e. both the CP-ligand have the same substituents that are associated chemically with the same indenolol group.

For the linking group R of formula (II):

-Y(R')2-(II)

preferably

Y represents Si

R' represents a C1-C10alkyl, C4-C10cycloalkyl or C6-C12aryl,

provided that both R'is a residue selected from the above group, and both R'-residue chemically different.

Therefore, in a particular variant embodiment of the present invention, the catalyst has the formula (III)

(Cp)2RZrCl2(I/mi> II),

where

Cp is indenyl substituted by the substituent in position 2 of the five-membered ring and in position 4 Deputy six-membered ring, where the Deputy of the five-membered ring represents methyl or ethyl and Deputy six-membered ring represents a C1-C6alkyl substituted by phenyl, such as 4-methyl-phenyl or 4-tert-butyl-phenyl (the latter being preferred),

provided that both CP-ligand is chemically the same, i.e. identical,

R represents a bridging group linking two Cp-ligand, where R has the formula (IV)

-Si(R')-2(IV),

where

R' is chosen from the group consisting of methyl, ethyl, isopropyl, cyclohexyl, 4-C1-C10alkyl-cyclo-hexyl, such as 4-methyl-cyclo-hexyl,

provided that both R'is a residue selected from the above group, and both R'-residue chemically different.

Accordingly, in a particular preferred variant of embodiment of the present invention the catalyst is razmer(cyclohexyl)silanediol bis(2-methyl-4-(4-tert-butylphenyl)the Indus is Il)zirconiated.

More preferably, the catalyst of the present invention do not cause any external inorganic or organic media, such as silicon, aluminum or porous polymer carrier material.

The above catalytic system obtained by methods described in WO 01/48034.

Specific preferred catalytic system obtained using the hardening of the emulsion is described in WO 03/051934. The document is entered here by reference in full. Therefore, the solid catalytic system preferably has the form of a solid catalytic particles obtained by the process comprising the stages:

a) obtaining a solution of one or more catalytic components;

b) dispersing the specified solution in immiscible solvent to obtain an emulsion in which the specified one or more catalytic component is present in the form of droplets dispersed phase,

(C) the approval of this dispersed phase with the conversion of these droplets to solid particles and optionally removing these particles with obtaining the specified catalyst.

It is preferable to obtain the solution using the first solvent, more preferably the first organic solvent. Even more preferably the organic solvent is selected from groups who, consisting of a linear alkane, a cyclic alkane, linear alkene, cyclic alkene, aromatic hydrocarbons and halogenated hydrocarbons.

Preferably immiscible solvent to form a continuous phase, representing an inert solvent, preferably immiscible solvent comprises a fluorinated organic solvent and/or their functionalityand derivatives, more preferably immiscible solvent comprises a semi-, highly - or perfluorinated carbon and/or functionalized derivative. Most preferably specified immiscible solvent includes perfluorocarbons or functionalized derivative, preferably3-C30perftoran, -alkenes or-cycloalkanes, more preferably4-C10perftoran, -alkenes or-cycloalkanes, preferably essentially perference, perforated, perfluorooctane or PERFLUORO(methylcyclohexane) or their mixture.

Additionally, it is preferable that the emulsion comprising the specified continuous phase and the specified dispergirovannoyj phase was represented by bi - or multiphase system, known from the prior art. For the formation of the emulsion can be used emulsifier. After the formation of the emulsion system indicated in the data the solution of the catalyst components in situ formed the specified catalyst.

In principle, the emulsifying agent may represent any suitable agent involved in the formation and/or stabilization of the emulsion and not having any negative influence on the catalytic activity of the catalyst. Emulsifying agent may represent, for example, surfactant-based hydrocarbons, optionally open the heteroatom(s), preferably halogenated hydrocarbons, optionally having a functional group, preferably a semi-, highly - or perfluorinated carbon, as is known from the prior art. Alternatively, the emulsifying agent can be obtained in the process of obtaining the emulsion, for example, by passing the reaction of the precursor surfactant with the connection of a solution of the catalyst. The specified predecessor surfactants may represent halogenated hydrocarbon with at least one functional group, such as highly fluorinated C1-30the alcohol which reacts, for example, with socialisticheskom component, such as alumoxane.

In principle, to obtain from the dispersed droplets of solid particles can be used with any method of curing. In one preferred variant of the embodiment of the present invention, the curing etc which lead temperature change. The emulsion is subjected to a gradual temperature change of up to 10°C/minute, preferably in the range from 0.5 to 6°C./minute, and more preferably in the range from 1 to 5°C/minute. Even more preferably the emulsion is subjected to a gradual change in temperature more than 40°C, preferably more than 50°C in less than 10 seconds, preferably in less than 6 seconds.

Preferably extracted particles have an average size in the range of 5 to 200 μm, more preferably in the range from 10 to 100 μm.

Additionally, preferably solidified particles have a spherical shape, a predetermined distribution of particle size and surface area, as defined above, preferably less than 25 m2/g, more preferably less than 20 m2/g, even more preferably less than 15 m2/g, even more preferably less than 10 m2/g and most preferably less than 5 m2/g, where these particles get in the manner specified above.

More detailed options embodiments and examples of systems with continuous and dispersed phase, method of producing the emulsion, emulsifying agent and methods of curing are shown, for example, the reference in the present patent application of international patent application WO 03/051934.

The above symmetrical components kata is Isadora obtained according to the methods described in WO 01/48034.

As indicated above, the catalyst system may further include an activator, such as socialization, as described in WO 03/051934 entered here by reference.

The preferred socialization are metallocene if you alumoxane, in particular, C1-C10-alkylalkoxy, most preferably methylalumoxane (MAO). Such alumoxane can be used as the sole catalyst or together with another acetalization(AMI). Therefore, in addition to or in addition to alumoxanes can be used other exciting complexes forming the catalyst activators. These activators are commercially available or can be obtained according to the literature of the prior art.

Additional alumoxane socializaton described in WO 94/28034 entered here by reference in full. This linear or cyclic oligomers with up to 40, preferably in the range from 3 to 20, -(Al(R'")O)- repeating units (where R'" represents hydrogen, C1-C10-alkyl (preferably methyl) or (C6-C18-aryl or mixtures thereof).

The use and number of such activators are well-known specialist in the field of engineering that applies the present invention. For example, using boron as the activator can b the th used the ratio of the transition metal to the Bor as an activator, component in the range from 5:1 to 1:5, preferably in the range from 2:1 to 1:2, such as 1:1. In the case of the preferred alumoxanes, such as methylalumoxane (MAO), the amount of Al, provided by alumoxanes may be selected so as to provide a molar ratio of Al: transition metal, for example, in the range from 1 to 10 000, preferably in the range from 5 to 8000, preferably in the range from 10 to 7000, for example in the range from 100 to 4000, such as in the range from 1000 to 3000. As a rule, in the case of solid (heterogeneous) catalyst ratio is preferably less than 500.

Therefore, the choice of the number of socializaton used in the catalyst of the present invention, varies and depends on the conditions and the specific compound of the transition metal that is well-known specialist in the field of technology to which the present invention relates.

The solution can contain additional components, including ORGANOMETALLIC compounds of transition metals that can be added to the above solution before or alternatively after the stage of dispersion.

Additionally, the present invention relates to the use of the above catalyst system to obtain a polypropylene according to the present invention.

Additionally, the present invention relates to a method for polyp is cut according to the present invention using the above catalyst system. Additionally, preferably, the process temperature is more than 60°C. Preferably the process is a multistage process that allows to obtain multimodal propylene, as mentioned above.

Multistage methods include the use of reactors, polymerization in bulk/gas phase reactors, known as multi-zone gas-phase reactors for the production of multimodal propylene polymer.

The preferred multi-stage method is the way of the circulating-gas-phase", such as the proposed Borealis A/S, Denmark (known as BORSTAR® technology, described for example in patent literature, such as EP 0887379 or in WO 92/12182.

Multimodal polymers can be obtained according to several methods, for example described in WO 92/12182, EP 0887379 and WO 98/58976.

Multimodal polypropylene of the present invention preferably receive a multi-stage method with multi-stage reaction sequence described in WO 92/12182. The contents of this document are entered here by reference.

From the prior art known to produce multimodal, in particular bimodal, polypropylene in two or more series-connected reactors, i.e. at different stages (a) and (b).

According to the present invention the main stage polymerization predpochtitel is but carried out as a combination of polymerization in mass/polymerization in a gas phase reactor.

The polymerization mass is preferably carried out in the so-called circulation reactor.

To obtain a multimodal polypropylene of the present invention, the preferred flexible way. For this reason, it is preferable that the composition was obtained in two main stages of polymerization in combination circulating reactor/gas-phase reactor.

Optionally and preferably the method also may include preliminary polymerization method known from the prior art, which may be preceded by a stage of polymerization (a).

Preferably the method is a continuous method.

Preferably in a method of producing a polypropylene polymer of the present invention, as was mentioned above, the conditions for a reactor for polymerization in bulk at the stage (a) can be the following:

the temperature is in the range from 40°C to 110°C, preferably is in the range from 60°C to 100°C, in the range from 70°C to 90°C,

- the pressure is in the range from 20 bar to 80 bar, preferably in the range from 40 bar to 70 bar,

- to control the molar mass can be added hydrogen when using the known method.

Then the reaction mixture from the polymerization reactor in the mass from step (a) is moved in a gas-phase reactor, i.e. at stage (b), and the service is via the stage (b) is preferably the following:

the temperature is in the range from 50°C to 130°C, preferably in the range from 60°C to 100°C,

- the pressure is in the range from 5 bar to 50 bar, preferably between 15 bar up to 40 bar,

- to control the molar mass can be added hydrogen when using the known method.

The exposure time can vary in both zones of the reactor. In one variant embodiment of the method of producing a polypropylene polymer of the present invention, the dwell time in the reactor, polymerization in bulk, for example in the circulation is in the range from 0.5 to 5 hours, for example in the range from 0.5 to 2 hours, and the time in the gas-phase reactor, typically is in the range from 1 to 8 hours.

If necessary, the polymerization can be carried out in a known manner at supercritical conditions in the first reactor polymerization in mass, preferably in the circulation reactor and/or condensation in the gas-phase reactor.

The method according to the present invention or any variants of its embodiment allows to obtain easily feasible means, and to further adapt the composition of the polypropylene polymer of the present invention, for example, the properties of the polymer composition can be adjusted or controlled way, for example, by one or more of the following parameterspec: temperature, the supply of hydrogen, the supply of co monomer, the supply of propylene, for example, in gas-phase reactor, the catalyst, the type and number of external donor (if used), the separation between the components.

The above method allows you to get in the reactor above the polypropylene is easily feasible means.

Film capacitor can be obtained by using the traditional extraction methods of preparation, are known from the prior art. Accordingly, a method of obtaining a film capacitor according to the present invention includes the use of the polypropylene described in this patent application, and getting it is preferably in the form of a film using a method using the frame for drawing and orientation films known from the prior art.

The method using the frame for drawing and orienting the film is, in particular, the way in which the polypropylene according to the present invention is melted and extruded through a slit, such as T-die, a cooling drum to obtain newiterator sheet. The specified sheet is subjected to a preliminary heat when using, for example, hot metal shaft and then pulled in the longitudinal direction between a set of shafts with different peripheral speeds and ZAT the both edges of the sheet engaged by the grippers, pull the sheet in the transverse direction in a heating Cabinet when using the frame for stretching and orienting the film obtained by biaxially oriented film. The temperature of the specified past a stretching sheet during the stretching in the longitudinal direction is preferably controlled so that it was within the melting point of the polypropylene, as specified in the description of the present patent application (-15 or +5°C). The uniformity of the film thickness when drawing in the transverse direction of the appreciate when using the way in which the area of the fixing film after stretching in the longitudinal direction of the mask and measure the actual factor extraction by measuring the size of the specified masking after stretching in the transverse direction.

Then the film is treated by corona discharge in air, nitrogen, gaseous carbon dioxide or any mixtures thereof for subsequent metallization of the surface to improve the adhesion strength with the applied metal and reel tape device for winding.

The resulting film is placed in the device for vacuum metallization and film preferably cause the oil pattern for the formation of the insulating grooves for specified purposes when using the device for applying oil patterns using a special application grids and things under the tion. Then metal, suitable for specified purposes, is applied to achieve a predetermined layer resistance. Additionally, if you want, metallization carried out using a safety comb-like plates for continuous changes in the rate of resistance in the transverse direction of the film. Metallized film is cut to obtain two tapes as a couple to obtain a capacitor. Then the tape is wound with the receiving device and the device gives a flat shape when using thermo-press, then on the ends of the sprayed metal, attaching findings, impregnated with insulating oil and the link with the receipt of the capacitor.

Additionally, the present invention relates to the use of film capacitor specified in the description of the present patent application as a capacitor.

Additionally, the present invention relates to a capacitor comprising at least a layer comprising a film capacitor according to the present invention. Additionally, preferably the capacitor includes a metal layer, in particular a metal layer receive the above method.

Hereinafter the present invention will be described with reference to the following Examples.

EXAMPLES.

A. measurement Methods.

For the above description of the present invention, if not explicitly specified otherwise, the long with the following Examples use the following definitions and methods of determination.

Quantitative analysis of the microstructure using NMR spectroscopy.

Quantitative spectroscopy nuclear magnetic resonance (NMR) is used to assess isotacticity, regioregularity and content of the co monomer in polymers.

Quantitative analysis13C{1H} NMR spectrum recorded in a state of solution using NMR spectrometer Bruker Advance III 400 operating at frequencies in the range from 400,15 to 100,62 MHz to1H and13S, respectively. The entire range of record when using13With optimized 10 mm sensor measurement of linear variables in the extended temperature range to 125°C for use in all pneumatic nitrogen gas.

For homopolymers of polypropylene approximately 200 mg of material was dissolved in 1,2-tetrachloroethane-d2 (TCE-d2). To ensure homogeneity of the solution after receipt of the initial sample in the fuser, ampoule for NMR spectroscopy additionally heated in a furnace with a round rotating hearth for at least 1 hour. When installed in the magnet vials exposed to 10 Hz. This scheme was chosen, primarily due to the need high-resolution quantitative analysis of the regularity of distribution of molecular structure (Busico, V., Cipullo, R., Prog. Polym. Sci. 26 (2001) 443; Busico, V.; Cipullo, R., Monaco, G., Vacatello, M., Segre, A.L., Macromoleucles 30 (1997) 6251). Creating the standard single-pulse excitation using NOE and duplex WALTZ 16 diagram interchange (Zhou, Z., Kuemmerle, R., Qiu, X., Redwine, D., Cong, R., Taha, A., Baugh, D. Winniford, Century, J.Mag. Reson. 187 (2007) 225; Busico, V., Carbonniere, P., Cipullo, R., Pellecchia, R., Severn, J., Talarico, G., Macromol. Rapid Commun. 2007, 28, 11289). Just for the spectrum needed 8192 (8k) pulses.

For copolymers of propylene approximately 200 mg of material was dissolved in 3 ml of 1,2-tetrachlorethane-d2 (TCE-d2) with chromium(III)acetylacetonate (Cr(ASAS)3with results in 65 mm solution of the relaxation agent in a solvent (Singh, G., Kothari, A., Gupta, V., Polymer Testing 28 5 (2009), 475). To ensure homogeneity of the solution after receipt of the initial sample in the fuser ampoule for NMR spectroscopy additionally heated in a furnace with a round rotating hearth for at least 1 hour. When installed in the magnet vials exposed to 10 Hz. This scheme was chosen, primarily due to the need high-resolution quantitative analysis for accurate quantitative determination of ethylene content. Create a standard single-pulse excitation without the use of NOE, when the optimized angle of inclination with 1-second delay repeat cycle and duplex WALTZ16 diagram interchange (Zhou, Z., Kuemmerle, R., Qiu, X., Redwine, D., Cong, R., Taha, A., Baugh, D. Winniford, Century, J.Mag. Reson. 187 (2007) 225; Busico, V., Carbonniere, P., Cipullo, R., Pellecchia, R., Severn, J., Talarico, G., Macromol. Rapid Commun. 2007,28,11289). Just for the spectrum needed 6144 (6k) pulses.

Conduct quantitative analysis on the basis of the13C{1 H} NMR spectrum with a certain mean value and determine appropriate quantitative values when using integral using special computer programs.

For copolymers of propylene all chemical shifts indirectly indicate the Central methylene group, ethylene block (EEE) when 30,00 parts per million when using the chemical shift of the solvent. This approach allows for a comparison with the standard even in the absence of structural units.

For polypropylene homopolymers all chemical shifts are internally tied to methyl the isotactic pentad (mmmm) when 21,85 parts per million.

Characteristic signals corresponding to regiodirection or co monomer shown (Resconi, L., Cavallo, L., Fait, A., Piemontesi, F., Chem. Rev. 2000, 100, 1253;; Wang, W-J., Zhu, S., Macromolecules 33 (2000), 1157; Cheng, H.N., Macromolecules 17 (1984), 1950).

The regularity of the distribution of the molecular structure quantitatively determined through integration of the methyl region within the 23.6-19.7 parts per million, adjusted for any parcels that are not associated with interest striopallidodentate (Busico, V., Cipullo, R., Prog. Polym. Sci. 26 (2001) 443; Busico, V., Cipullo, R., Monaco, G., Vacatello, M., Segre, A.L., Macromoleucles 30 (1997) 6251).

In particular, the impact of regiodirection and co monomer to the quantitative analysis of the frequency distribution of the molecular structure correct subtracting integrally representative regiogaranti and co monomer of a specific area integral striopallidodentate.

Isotacticity determine the level of the pentad and indicate as a percentage of the sequences of the isotactic pentad (mmmm) from the sequences of all the pentad:

[mmmm]%=100·(mmmm/the sum of all the pentad).

The presence of 2.1 retroreective indicate two methyl plot of 17.7 and 17.2 parts per million, which is confirmed by other typical areas.

Not given characteristic signals corresponding to other types of regiodirection (Resconi, L., Cavallo, L., Fait, A., Piemontesi, F., Chem. Rev. 2000, 100, 1253).

Quantitative analysis 2.1 retroreective carried out using the average of two integral characteristic methyl parcel of 17.7 and 17.2 ppm:

PE=(Ie6+Ie8)/2.

Quantitative analysis of 1,2 initially inserted propene carried out on the basis of the methyl region adjusted overlooked areas included in this area is not associated with the primary insert, and plots of the primary insert is excluded from this field:

P12=ICH3+P12e.

The total number of propene quantitatively assessed as the sum of the initially inserted propene and all other present regiodirection:

Ptotal=P12+PE.

The molar percentage 2.1 retroreective quantify the total content of propene:

[A]mol.%=100·(P21e/Ptotal).

For copolymere the typical signals, appropriate insertion of ethylene (Cheng, H. N., Macromolecules 17 (1984), 1950).

It is also reported that (Resconi, L., Cavallo, L., Fait, A., Piemontesi, F., Chem. Rev. 2000, 100, 1253; Wang, W-J., Zhu, S., Macromolecules 33 (2000), 1157; Cheng, H.N., Macromolecules 17 (1984), 1950) for regiodirection require amendment due to the impact of such defects on the content of the co monomer.

The molar fraction of ethylene in the polymer is quantitatively evaluated using the method of Wang et. al. (Wang, W-J., Zhu, S., Macromolecules 33 (2000), 1157) through the integration of multiple signals across a spectral region13C{1H} spectrum obtained under specified conditions. This method was chosen for its accuracy, reliability and the ability to explain the presence of regiodirection if necessary. Integral field slightly adjust to improve the applicability to a wide within the content of comonomers.

The molar percentage of co monomer, is introduced into the polymer, calculated on the molar fraction according to:

E[mol.%]=100·fE.

The mass percentage of co monomer, is introduced into the polymer, calculated on the molar fraction according to:

E[wt.%]=100·(fE·to 28.05)/((fE·to 28.05)+((1-fE)·42,08)).

The distribution of the sequence of co monomer in the triads determined by using the method Kakugo et al. (Kakugo, M., Naito, Y., Mizunuma, K., Miyatake, T. Macromolecules 15 (1982) 1150) through the integration of multiple signals across a spectral region13C{1H} spectrum obtained under given conditions is H. This method was chosen for its reliability. Integral field slightly adjust to improve the applicability to a wide within the content of comonomers.

The molar percentage of a specified sequence of co monomer in the triads of the polymer is calculated by the molar fraction determined by the method of Kakugo et al. (Kakugo, M., Naito, Y., Mizunuma, K., Miyatake, T. Macromolecules 15 (1982) 1150) according to:

XXX[mol.%]=100·fXXX.

The molar fraction of co monomer incorporated into the polymer, defined by the distribution of the sequence of co monomer in the triads, rely on the distribution of triads using the known necessary equations (Randall, J. Macromol. Sci., Rev. Macromol. Chem. Phys. 1989, C29, 201):

fXEX=fEEE+fPEE+fPEP,

fXPX=fPPP+fEPP+fEPE,

where PEE and SWU represents the sum of the reversible sequences RAY/EUR and SWU/RRE respectively.

The randomness of the distribution of co monomer quantitatively assessed as the relative number of isolated sequences of ethylene compared to all entered by ethylene. The coincidence count distribution of sequences in the triads using the equation:

R(E)[%]=100·(fPEP/fXEX).

Observed characteristic signals corresponding to the introduction of 1-hexene, and the content of 1-hexene calculated as the molar percentage of 1-hexene in the polymer, N(mol.%), according to:

[N]=Htot/(Ptot+Htot),

where:

Htot=IαB4)/2+I(αα4)×2,

where I(α4) represents the integral αB4plots at 44.1 parts per million, which defines an isolated 1-hexene, introduced in RNR sequence, and I(αα4) represents the integral αα4 areas at 41.6 parts per million, which determines successively introduced 1-hexene in RNR sequence.

Ptot=integral of all CH3 areas methyl region with the amendment applied to an underestimation of the other propenoic units that are not addressed in this area, and the revaluation of other sites found in this area.

N(mol.%)=100×[N]

which are then translated in wt.% using correlation

N(wt.%)=(100×Nmol.%×84,16)/(Nmol.%×84,16+(100-Nmol.%)×42,08).

Statistical distribution calculated from the ratio of the content of hexene present in isolated (RRRR) and consecutive (RNRR) sequences introduced the co monomer And:

[LV]<[N]2

Mw, Mn, MWD.

Mw/Mn/MWD measured using gel chromatography (GPC) according to the following method.

The mass-average molecular weight (Mw), srednecenovogo molecular weight (Mn) and molecular weight distribution (MWD=Mw/Mn) is measured using a method based on ISO 16014-1:2003 and ISO 16014-4:2003. Use the device Waters Alliance GPCV 2000 with a refractometric detector and online viscometer at ISOE is lovanii columns 3 TSK-gel (GMHXL-HT) from TosoHaas and 1,2,4-trichlorobenzene (TCB, stable 200 mg/l 2,6-di tertbutyl-4-methyl-phenol) as solvent at a temperature of 145°C and a constant flow rate of 1 ml/minute. For analysis Inuktitut 216,5 l sample solution. Column calibrated using the relative calibration of narrow 19 MWD polystyrene standards (PS) in the range of 0.5 kg/mol to 11,500 kg/mol and well-studied broad standards of polypropylene. All samples receive dissolving in the range of 5 to 10 mg of polymer in 10 ml (160°C) stabilized TCB (same as mobile phase) and incubated for 3 hours with continuous mixing before sampling in device for GPC.

The average molecular weight, distribution of molecular weight, branching g'(Mn, Mw, MWD, g') is determined using SEC/VISC-LS.

Average molecular weight (Mw, Mn), molecular weight distribution (MWD) and their limits described in the index polydispersity, PDI=Mw/Mn where Mn is srednecenovogo molecular weight, and Mw represents a mass-average molecular weight), determined using gel chromatography (GPC) according to ISO 16014-4 2003. A PL 220 (Polymer Laboratories GPC with refractive index (RI) with the online chetyrehkratnym type viscometer (PL-BV 400-NT) and the dual detector light scattering (PL-LS 15/90 detector light scattering) angle of 15° and 90°. As the stationary phase to use is lance 3 Olexis and 1x Olexis Guard from Polymer Laboratories, and as mobile phase 1,2,4-trichlorobenzene (TCB, stabilized with 250 mg/l 2,6-di tertbutyl-4-methyl-phenol) as solvent at a temperature of 160°C and a constant flow rate of 1 ml/minute. For analysis Inuktitut 200 l sample solution. The corresponding constants of the detector along with the amounts of delay of the detector determines when using narrow standard PS (MWD=1.01) with a molar mass 132900 g/mol and a viscosity 0,4789 DL/g Corresponding dn/dc for standard PS TCB is 0,053 cm3/year

The molar mass of each elution determine when using ambient light, using a combination of two angles of 15° and 90°. All process data and carry out the calculation using software Cirrus Multi-Offline SEC-Software Version 3.2 (Polymer Laboratories a Varian inc. Company). The molecular weight calculated by using the option in the Cirrus software "use combination of LS angles" in the field "sample calculation options subfield of slice MW data from.

Data processing is described in detail in G. Saunders, P.A.G: Cormack, S. Graham; D..Sherrington, Macromolecules, 2005, 38, 6418-6422. Mwieach elution define an angle of 90° using the following equation:

Mwi=KLS*R(θ)90dndmi> c*R*P(θ)

The coefficient of relay R(θ)90° 90° measured when using the LS detector, and R is the response RI detector. The function of the scattering particles P(θ) is determined by using both angles (15° and 90°), as described in .Jackson and H.G.Barth (C.Jackson and H.G.Barth, "Molecular Weight Sensitive Detectors" in Handbook of Size Exclusion Chromatography and related techniques, C. - S. Wu, 2nded., Marcel Dekker, New York, 2004, str). For low - and high-molecular area in which weaker signal LS detector or RI detector, respectively, using a linear approach for the correlation of the ratio of the elution volume corresponding to a molecular mass.

The ratio dn/dc used in the equation are calculated according to the constant RI detector, the concentration of the sample and the peak area readings of the detector of the analyzed sample.

The relative amount of branching determined by using the index g' of the sample branched polymer. Index long chain branching (LCB) is defined as g'=[η]br/[η]lin. It is known that if g' is increased, the content of branching decreases. [η] is intrinsic viscosity at a temperature of 160°C in trichlorobenzene polymer sample at a certain molecular weight, and measure when using on-line viscometer and de is the sector concentration. Intrinsic viscosity is measured as described in the reference Cirrus Multi-Offline SEC-Software Version 3.2 using equation Solomon-Gatesman.

The necessary concentration of each elution determine when using RI detector.

[η]linrepresents the intrinsic viscosity of a linear pattern, and [η]brrepresents the viscosity of branched sample of the same molecular weight and chemical composition. Srednekovoi g'nand bulk g'wdefined as the following:

g'n=0iai*[η]br,i[η]lin,iai

g'w=0iAi*[η]br,i[η]lin,i 0iAi*([η]br,i[η]lin,i)2

where aiis dW/dlogM fraction I, Airepresents the cumulative dW/dlogM polymer up to fractions of L. Index [η]linlinear control (linear isotactic PP) depending on the molecular weight is measured using on-line detector viscosity. The following parameters K and α are K=30,68·10-3and α=0,681) linear control with a molecular mass within logM=4.5 to 6.1 in. Index [η]linmolecular weight for calculating g' calculated by the following equation [η]lin,I=K·Miα·[η]br,Iby measuring for each sample using online viscosity detector and detector concentration.

The rate of melt flow (MFR).

The flow rate of the melt is measured under a load of 2.16 kg (MFR2) at 230°C. the flow Rate of the melt is the amount of polymer in grams which device, standardized testing with the according ISO 1133, extradiol for 10 minutes at a temperature of 230°C. under load of 2.16 kg

The fraction soluble in cold xylene (XCS wt.%).

The fraction soluble in cold xylene (XCS), determined at a temperature of 23°C according to ISO 6427.

The gel content is identical to the fraction insoluble in hot xylene (XHI), which is determined by extracting 1 g of thinly sliced polymer in 350 ml of xylene in to conventional Soxhlet extractions within 48 hours at boiling temperature. The remaining solid fraction is dried at a temperature of 90°C and weighed to determine the insoluble fraction.

The melting temperature Tmthe crystallization temperature Tcdetermine when using the calorimeter Mettler TA820 with carrying out differential scanning calorimetry (DSC) 5-10 mg samples. Both curves: and crystallization, and melting - receive at the rate of 10°C/minute on scanogram heating and cooling in the range from 30°C to 225°C. the crystallization Temperature and melting take as the peak of the endotherm and ectotherm.

Also when using the DSC method according to ISO 11357-3 measure the enthalpy of melting and crystallization (Hmand Hc).

Elementary analysis.

Below is a simple analysis that is used to determine the content of basic residues, which mainly remains of the catalyst, in particular the remnants of Al VI Si in the polymer. These remnants of Al, b and Si can be in any form such as elemental or ionic form, and can be removed and defined in polypropylene using described below ICP method. The method is also used for determining content in the polymer Ti. It is clear that can be used other known methods, leading to similar results.

ICP spectrometry (inductively coupled plasma emission spectrometry).

The ICP device: a Device for determining the content of Al, and Si represents the ICP Optima 2000 DV, PSN 620785 (supplier Perkin Elmer Instruments, Belgium) software.

The detection limits of 0.10 parts per million (Al), 0.10 parts per million (C), 0.10 parts per million (Si).

The polymer sample is first burned when using the known method, and then dissolved in a suitable acidic solvent. Rearing standards for the calibration curve is dissolved in the same solvent as the sample, and the concentration is chosen so that the concentration of the sample coincides with the standard calibration curve.

Parts per million by weight:

Ash content: the ash content measured according to ISO 3451-1 (1997).

The calculated ash content of Al, Si and:

Ash and the above elements, Al and/or Si and/or b can also be calculated in the polypropylene based on Polimeri the sure activity is given as an example of the catalyst. These figures give an upper limit on the presence of these residues to the catalytic Converter.

Therefore, the evaluation of the residues of the catalyst is carried out based on the composition of the catalyst and the efficiency of the polymerization catalyst residues in the polymer:

General catalyst residues [ppm]=1/efficiency [kgpp/g catalyst]×100

All residues [ppm]=wAl,catalyst[%]×total catalyst residues [ppm]/100

The remains of Zr [ppm]=wZr,catalyst[%]×total catalyst residues [ppm]/100

(Similar calculations can also be used for residues In, Cl, and Si).

The residual chlorine content:

The content of residual Cl in the samples is measured using a known method, such as x-ray fluorescence spectrometry (XRF). Using x-ray fluorescence spectrometer Philips PW2400, PSN 620487, (Supplier: Philips, Belgium) software X47. The detection limit of CL is 1 part per million.

Power electrical breakdown (EB%).

Complies with IEC 60243-1, Second edition (1998-01).

The method describes how to measure the strength of the electrical breakdown of the insulation material of the plates of the compression molding.

Definition:

Eb: Eb-Ub/d.

The strength of the electric field applied to the sample, in which there is a breakdown. In homogeneous what's plates and films that corresponds to the strength of electric breakdown, divided by the thickness of the plate/film (d), unit: kV/mm For each BOPP (VOR) film hold 10 individual measurements of the breakdown. The results of 10 individual measurements of the breakdown BOPP films appreciate when using the graph of the Weibull distribution, where 63 percentile corresponds to the strength of breakdown (Eb 63%). The parameter β represents the slope of the linear regression through these 10 points (also see CEI 727-2; First Edition (1993-02)).

Effect of electric breakdown is determined at 50 Hz high-voltage chamber when using metal rods as electrodes, as specified in IEC 60243-1, Second edition (1998-01) (4.1.2). The voltage at the film/plate increases at the rate of 2 kV/s to breakdown.

Porosity: BET with gaseous N2, ASTM 4641, device Micromeritics Tristar 3000; sample preparation: at 50°C, 6 hours under vacuum.

Surface area: BET with gaseous N2 ASTM D of 3,663, the device Micromeritics Tristar 3000: the sample preparation is carried out at a temperature of 50°C, 6 hours under vacuum.

The average particle size (d50) is measured using Coulter Counter LS200 at room temperature in the environment of n-heptane.

Technology stepped isothermal stratification (SIST).

For SIST analysis carried out isothermal crystallization in the melt Mettler TA820 DSC using 3±0.5 mg samples with decreasing temperatures ranging from 200°C to 105°C.

(i) the sample is dissolved, ablaut at a temperature of 225°C for 5 minutes,

(ii) then cooled with 80°C/min to 145°C,

(iii) was incubated for 2 hours at a temperature of 145°C,

(iv) then cooled with 80°C./min to 135°C

(v) was incubated for 2 hours at a temperature of 135°C

(vi) then cooled with 80°C/min to 125°C,

(vii) was incubated for 2 hours at a temperature of 125°C,

(viii) then cooled with 80°C./min to 115°C,

(ix) was incubated for 2 hours at a temperature of 115°C,

(x) then cooled with 80°C./min to 105°C,

(xi) was incubated for 2 hours at 105°C.

After the last stage, the sample is cooled at 80°C/min to -10°C and get the melting curve, heating the cooled sample at 10°C/min up to 200°C. All the measurements were carried out in nitrogen atmosphere. The enthalpy of melting is recorded as a function of temperature and evaluated by measuring the enthalpy of melting fractions during melting in a temperature range

from 50 to 60°C; 60 to 70°C; 70 to 80°C; 80 to 90°C; 90 to 100°C.; 100 to 110°C.; 110 to 120°C.; 120 to 130°C.; 130 to 140°C.; 140 to 150°C.; 150 to 160°C; from 160 to 170°C.; from 170 to 180°C; 180 to 190°C 190 up to 200°C.

Thus, the melting of crystallized material can be used to calculate the distribution of the thickness of a lamella according to the equation Thomson-Gibbs (Ur. 1).

Tm=T0( 1-2σΔH0L)(1)

where T0=457 K, ΔN0=134×106J/m3and σ=0,0496 j/m2and L represents the thickness of the leafs.

The modulus of tensile elasticity is measured according to ISO 527-2 (crosshead speed = 50 mm/min; 23°C) using the obtained injection-molded specimens as described in EN ISO 1873-2 (form bones for dogs, thickness 4 mm).

Century Examples.

Data examples SIST table 5-9 is shown in figure 1.

The used catalyst was prepared as in Example 5 WO 03/051934, where it uses the catalyst was replaced by razmer(cyclohexyl)silanediol bis(2-methyl-4-(4-tert-butylphenyl)indenyl)zirconium dichloride. Razmer(cyclohexyl)silanediol bis(2-methyl-4-(4-tert-butylphenyl)indenyl)zirconium dichloride receive according to WO 2005 105863 A2, Examples 17-18.

Obtaining a catalyst.

In teklemariam stainless steel reactor 90 DM3with a shirt get a comprehensive solution at a temperature of -5°C, adding 0.85 kg 24.5 wt.% solution ((2,2,3,3,4,4,5,5,6,6,7,7,8,8,9,9,9-heptadecadiene)oxiran)/toluene very slowly (3.4 ml/min) 13.5 kg of 30 wt.% solution of MAO(methylalumoxane)/toluene. The temperature was raised to 25°C and stirred the solution for 60 the minutes. After adding 210 g of the complex solution is stirred for additional two hours. This mixture is pumped at a speed of 5 l/h in a pair of rotor-stator 4M. In the rotor-stator at a peripheral speed of 4 m/s, the mixture is stirred with a flow rate of 32 l/h with hexadecafluoro-1,3-dimethylcyclohexane with obtaining, thus, of the emulsion. Drops in the emulsion utverjdayut excess flow 450 l/h hexadecafluoro-1,3-dimethylcyclohexane at a temperature of 76°C in a Teflon hose. The hose is connected with 160 DM3the reactor is jacketed stainless steel, equipped with a helical mixing element. In this reactor, the catalyst particles are separated from hexadecafluoro-1,3-dimethylcyclohexane by the difference in density. After using the complex solution of the catalyst particles are dried at 160 DM3reactor at a temperature of 70°C in a flow of nitrogen of 5 kg/hour for 7 hours.

Below is a definition of the limits of porosity and surface area.

The molar ratio of Co/M (Al/Zr)260 mol/mol
The average particle size26 η
The Zr content0.53 wt.%
The Al content34.5 wt.%

Used in the present invention the polymers (SEE, E1, E2, except SE and SE) obtained using the above catalyst in a continuous two-stage method of polymerization, consisting of a polymerization process in mass circulation reactor) and stage vapor-phase polymerization. Before submitting to the stage polymerization in the mass of the catalyst undergoes a preliminary polymerization in water reactor prior to polymerization. The levels of hydrogen in the reactor prior to polymerization, in the circulation reactor and gas-phase reactor differ accordingly and adjusted so that the molecular weight (MFR) of the polymer from the first stage polymerization was different from the molecular weight (MFR) of the polymer from the second stage polymerization. The mass fraction of the product of the circulation reactor (division) may range from 30 to 70 wt.%. The temperature in the reactor prior to polymerization at 35°C in a circulating reactor 70°C (CE, E1) or 75°C (E2), and in gas-phase reactors 85°C. the pressure during polymerization in the circulation reactor is 53 bar and gas-phase reactor 30 bar (CE, E1) or 25 bar (E2). Separation and other parameters of the process used to obtain CE, E1 and E2, are shown in Table 1.

td align="right" namest="c0" nameend="c4"> Table 1
The receive E1, E1 and SE
SEE1E2
The separation fraction from the circulating reactor[wt.%]64,042,045
The preliminary polymerization
The flow of catalyst[g/h]1,71,92,3
The supply of propylene[kg/h]545562
The supply of hydrogen[g/h]0,50,41,8
Time[h]0,40,40,4
Circulation is eactor
H2/C3[mol/KMOL]0,070,060,07
Performance[kg/h]312923
MFR2[g/10 minutes]0,71,10,9
Division[wt.%]644245
1.GPR
H2/C3[mol/KMOL]3,62,31,5
Performance[kg/h]162829
MFR2*[g/10 m in the chick-pea] 2,04,43,2
Division[wt.%]344155
2.GPR
H2/NW[mol/KMOL]1,53,0
Performance[kg/h]112
MFR2**[g/10 minutes]1,65,0
Division[wt.%]217
The final MFR2(granules)[g/10 minutes]25,92,1

* LG(1/MFR1)·wf1+LG(1/MFR2)·wf-2=LG(1/MFRtotal),

where

MFR1pre what is MFR 2polypropylene obtained in the circulation reactor,

MFR2is calculated MFR2polypropylene obtained in 1GPR, and

FRtotalis MFR2measured for the polypropylene composition obtained in 1GPR,

** LG(1/MFR1)·wf1+LG(1/MFR2)·wf-2=LG(1/FRtotal),

where

MFR1is MFR2polypropylene composition obtained in 1GPR,

MFR2is calculated MFR2polypropylene obtained in 2GPR, and

FRtotalis MFR2measured for the polypropylene composition obtained in 2GPR.

CE, E1 and E2 get in powder form and is subjected to granulation and stabilized with Irganox 1010 (4500 ppm).

Comparative example 2 (CE) is a commercial product HB311BF from Borealis AG.

Comparative example 3 (SE) is a commercial product HC300BF from Borealis AG.

SE, SE, SE, E1 and E2 are subjected to further processing to produce BOPP films: materials ekstragiruyut and water for cooling the shaft with obtaining sheets of hardened film. The used parameters are shown in Table 2.

Table 2
The settings for the irrigation tapes
Extrude the Melting pointThe temperature of the cooling shaftThe thickness of irrigation tapes
Single screw extruder Brabender, 19 mm 1:3 with a conical design of the screw, mesh seal230°C90°C500 η

From each bulk film take samples of size 8,5 8,5 cm, slicing from the Central part of the film. These samples are subjected to biaxial orientation using laboratory BOPP installation. Square samples fixed on the frame Karo IV drawing and orienting the film five hooks on each side. When using the frame for drawing and orienting the film irrigated film stretch by a factor of five for each side, thus, the ratio of the hood 5×5. After stretching with these settings, BOPP film removed from the frame for drawing and orienting the film and subjected to testing on the gap/break, as mentioned above. When using the above process, the liquid film is subjected to biaxial orientation and conduct testing of each material, including a breakdown. These outcomes represent the average is e two dimensions.

Table 3
The process parameters worr
Device for biaxial orientationTime hoodsExhaust velocityThe thickness of BOPP filmsThe ratio hoods
Karo IV laboratory frame for drawing and orienting the film, Bruckner Maschinenbau GmbH, Germany147°/157°C*800%/s20 η5×5
* 147°C is used for CE, E1 and E2; 157°C is used for SE and SE

Table 4
Properties
SESESEE1E2
MwD341380412260311
MWD[-]465763969365364
MFR2[]2602622615,92,1
XCS[wt.%]0,8*3,51,20,5*0,7'"
XHI[wt.%]00000
Tm[°C]152,8161,3163to 151.8152,6
Tc[°C]112,9112,7115to 113.4114,3
g'[-]0,993±,044 0,987±0,0060,987±0,0060,939±0,0080,970±0,014
Si[parts per million]0,50,50,50,50,5
Ti[parts per million]0,51,50,90,50,5
TM[MPa]122213171261
BDV[kV/mm] 5×5302±25,1309±16290±17325±15312±12
β[-]81281417
<2,1>[mol.%]0,90 00,90,9
* as measured on powdered mass at the reactor exit
TM Modulus of tensile elasticity
<2,1> is <2,1> recidivity

Table 5
SIST in SE (1)
Limits T [°C]The limits of Lc [nm]Δ [n] [j/g]Fraction [wt.%]
50-602,52-2,7300
60-702,74-2,9700
70-802,98-3,2500
80-903,26-3,6000
90-1003,61-4,030,082390,07
100-110Android 4.04-4,570,17690,17
110-1204,58 is 5.281,5031,43
120-130of 5.29-6,263,8483,66
130-1406,27-7,699,9699,49
140-1507,70 -9,95of 33.2631,65
150-1609,96 -14,0938,1236,27
>160>14,0918,1417,26

Table 6
SIST in SE (1)
Limits T [°C]The limits of Lc [nm]Δ [n] [j/g]Fraction [wt.%]
50-602,52-2,7300
60-702,74-2,9700
70-802,98-3,2500
80-903,26-3,6000
90-1003,61-4,0300
100-110Android 4.04-4,570,0685740,06
110-1204,58 is 5.280,37640,35
120-130of 5.29-6,261,020,96
130-1406,27-7,693,1822,99
140-1507,70-9,9512,311,55
150-1609,96-14,0931,5529,62
>160>14,0958,156 54,06

Table 7
SIST in SE (1)
Limits T [°C]The limits of Lc [nm]Fraction [wt.%]
50-602,52-2,730,00
60-702,74-2,970,05
70-802,98-3,250,15
80-903,26-3,600,28
90-1003,61-4,030,43
100-110Android 4.04-4,570,59
110-1204,58 is 5.280,93
120-130of 5.29-6,261,60
130-1406,27-7,693,10
140-1507,70-9,959,71
150-1609,96-4.09 to 22,62
>160>14,0960,45

Table 8
SIST in E1 (Fig 1)
Limits T [°C]The limits of Lc [nm]Δ [n] [j/g]Fraction [wt.%]
50-602,52-2,7300
60-702,74-2,970,089820,082
70-802,98-3,250,22050,20
80-903,26-3,600,45760,42
90-1003,61-4,030,74570,68
100-110Android 4.04-4,570,8640,79
110-1204,58 is 5.282,3222,11
120-130of 5.29-6,264,9334,49
130-1406,27-7,6911,0310,04
140-1507,70-9,9532,9329,96
150-1609,96-14,0936,1632,90
>160>14,0920,1718,35

Table 9
SIST in E2 (Fig 1)
Limits T [°C]The limits of Lc [nm]Δ [n] [j/g]Fraction [wt.%]
50-602,52-2,7300
60-702,74-2,9700
70-802,98-3,2500
80-903,26-3,600,079290,08
90-1003,61-4,030,27560,27
100-110Android 4.04-4,570,37270,36
110-1204,58 is 5.281,5731,53
120-130of 5.29-6,263,9323,82
130-1406,27-7,699,8579,59
140-1507,70-9,9531,1630,31
150-1609,96-14,093534,051
>160>14,0920,5319,97

1. Polypropylene with
(a) melting temperature (Tm), measured according to ISO 11357-3, 151,0 to 160,0°C,
(b) a fraction, soluble in cold xylene (XCS), not more than 1.5 wt.%,
(c) in p is adalah 45.0 to 67.0 wt.% the crystalline fraction of the thickness of the leafs in the range from 7,70 to 14,09 nm, where this fraction is determined using the stepped isothermal stratification (SIST), and
(d) from to 18.0 to 50.0 wt.% the crystalline fraction of the thickness of the leafs more than 14,09 nm, where this fraction is determined using the stepped isothermal stratification (SIST).

2. Polypropylene with
(A1) melting temperature (Tm), measured according to ISO 11357-3, 151,0 to 160,0°C,
(b1) a fraction, soluble in cold xylene (XCS), not more than 1.5 wt.%,
(C1) in the range from of 18.0 to 50.0 wt.% the crystalline fraction of the thickness of the leafs more than 14,09 nm, where this fraction is determined using the stepped isothermal stratification (SIST), and
(d1) optional <2,1> recidivity defined using13With spectroscopy, be equal to or more than 0.4 mol.%,
or
(A2) melting temperature (Tm), measured according to ISO 11357-3, 151,0 to 160,0°C,
(b2) a fraction, soluble in cold xylene (XCS), not more than 1.5 wt.%,
(C2) from of 18.0 to 50.0 wt.% the crystalline fraction of the thickness of the leafs more than 14,09 nm, where this fraction is determined using the stepped isothermal stratification, and
(d2) <2,1> recidivity defined using13With spectroscopy, be equal to or more than 0.4 mol.%.

3. Poly is roelen according to claim 1, where polypropylene has a <2,1> recidivity defined using13C-spectroscopy equal to or more than 0.4.

4. The polypropylene according to claim 1 or 2, where the polypropylene is a homopolymer of propylene.

5. The polypropylene according to claim 1 or 2, where the polypropylene has a
(a) a molecular weight distribution (MWD)measured according to ISO 16014, from 2.8 to 8.0,
and/or
(b) the rate of flow of the melt MFR2(230°C)measured according to ISO 1133, from 2.0 to 10.0 g/10 minutes

6. The polypropylene according to claim 1 or 2, where the polypropylene has a crystallization temperature (Tc), measured according to ISO 11357-3, from 110 to 120°C.

7. The polypropylene according to claim 1 or 2, where the polypropylene has a branching index g' of 0.9 to 1.0.

8. The polypropylene according to claim 1 or 2, where the content of residual silicon is less than 0.5 parts per million.

9. The polypropylene according to claim 1 or 2, where the polypropylene is biaxially oriented film.

10. The use of polypropylene according to any one of the preceding paragraphs in biaxially oriented polypropylene film and/or film capacitor with high power electrical breakdown and the β-parameter (parameter Weibull) electrical breakdown, measured in accordance with IEC 60243, more than 8, preferably more than 12.

11. Biaxially oriented polypropylene film, where the polypropylene is a polypropylene according to any one of the preceding paragraphs is s 1-8.

12. Film capacitor or a biaxially oriented polypropylene film made of polypropylene according to any one of the preceding paragraphs 1-8.

13. A method of producing polypropylene according to any one of the preceding paragraphs 1-8, including stage polymerization of propylene and optional C2-C10α-olefin different from propylene, in the presence of catalytic systems with a surface area, measured according to ASTM D of 3,663 (N2), less than 20 m2/g and containing a catalyst comprising the transition metal compounds with formula (I):

where
X is independently a monovalent anionic ligand, such as σ-ligand,
Cf is an organic ligand selected from the group consisting of unsubstituted cyclopentadienyl, unsubstituted indenyl, unsubstituted tetrahydroindene, unsubstituted fluorenyl, substituted cyclopentadienyl, substituted indenyl, substituted tetrahydroindene and substituted fluorenyl,
provided that both SR-a ligand selected from the above group and both the CP-ligand is chemically the same, i.e. identical,
R represents a bridging group linking two CP-ligand, where R has the formula (II):

where
Y is C, Si or Ge, preferably Si,
R' - C1-C20alkyl, C4-C10cloaker, With6-C12aryl, C7-C12arylalkyl or trimethylsilyl,
provided that both R'is a residue selected from the above group, and both R'-residue chemically different.



 

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16 cl

FIELD: chemistry.

SUBSTANCE: invention relates to production of layered materials for multilayer glass and can be used as a HUD display which does not deteriorate even when exposed to light. The layered material includes an interlayer film and a retarding element placed between adhesive layers. The film of the multilayer glass contains a thermoplastic resin and a UV absorber. The UV absorber is a benzotriazole compound or a benzophenone compound and at least one compound selected from a group consisting of a malonic ester compound, an oxanilide compound and a triazine compound. Total content of the malonic ester compound, oxanilide compound and triazine compound is not less than 0.8 pts.wt, and total content of the benzotriazole compound or benzophenone compound is not less than 0.8 pts.wt per 100 pts.wt thermoplastic resin. The adhesive layer contains an adhesive, having a glass transition point of -20°C or lower.

EFFECT: layered material has high impact strength.

20 cl, 1 dwg, 3 tbl, 62 ex

FIELD: chemistry.

SUBSTANCE: invention relates to chemistry of polymers and deals with a method of obtaining hardly flammable polymer products based on polyethyleneterephthalate with biocidal properties, which can be applied in the textile industry, medicine, in products of a special purpose as well as in other fields of industry. The method of obtaining hardly flammable polymer products based on polyethyleneterephthalate with biocidal properties includes stretch forming of polyethyleneterephthalate-based polymer product in an adsorption-active liquid medium, containing modifying additives, and the product drying, with, at least, one modifying additive being a biocidal preparation and, at least, one modifying additive being a fire retardant, and one of the modifying additives is pentaerythritol.

EFFECT: reduction of the polymer material dropping with preservation of lower combustibility and biocidal activity.

8 cl

FIELD: chemistry.

SUBSTANCE: invention relates to a machine direction oriented polymer film for labels, use of such a film to label articles, a label liner and a label made from such a film. The polymer film has a multi-layer structure comprising core layer containing at least one polypropylene homopolymer, a polypropylene random copolymer or a polypropylene block copolymer or a mixture of two or more thereof and at least one modifier. The modifier contains 1-20 wt % hydrocarbon resin and a styrene block copolymer or an olefin block-copolymer different from the polypropylene block copolymer.

EFFECT: obtaining a machine direction oriented polymer film for making labels with improved physical and mechanical properties.

12 cl, 4 tbl, 2 dwg

FIELD: process engineering.

SUBSTANCE: invention relates to production of microperforated polymer film. Proposed method comprises forming of polymer film consisting of opposed first and second surfaces and multiple cavities there between. Said multiple cavities open to first surface and include the cavity surface. Cavity surface crosses the first surface. Then, fluid is fed between thrust surface and first surface. Thrust surface supports said polymer film. Second surface is subjected to heat treatment to perforate said polymer film at areas that cover said multiple cavities. Article thus made represents a solid particle filter for fluids or gases.

EFFECT: higher efficiency of production, precise perforation, high density of relative open area.

16 cl, 2 tbl, 12 dwg

FIELD: chemistry.

SUBSTANCE: composition for producing hydrophobic fire- and water-resistant films contains aqueous solution of polyvinyl alcohol, formaldehyde and an acid curing catalyst - phosphoric acid, a dispersion of solid amino plastic particles based on products of condensation of formaldehyde with urea in form of fine particles of a urea-formaldehyde resin, with overall molar ratio of the mixture of amines to formaldehyde of 1:0.8-1.3, diethanolamine, a water repellent in form of a 50% aqueous dispersion. In a second version, the composition contains a mixture of carbamide with 10-30% melamine besides formaldehyde.

EFFECT: obtaining fire-resistant films endowed with water-repellent properties and water-resistance.

5 cl, 3 tbl

FIELD: chemistry.

SUBSTANCE: invention relates to a processing aid, which is used in processing of thermoplastic polyurethanes, as well as to its obtaining and application in processing of thermoplastic polyurethanes into self-supporting films. The processing aid contains, wt %: hydrophobised, at least, partly aggregated metal oxide particles of pyrogenic origin, selected from the group, including aluminium oxide, silicon dioxide and mixtures of the said metal oxides 10-50, one or several thermoplastic polyurethanes 20-75, one or several isocyanates 0.5-25, one or several compounds, possessing an action of anti-adhesive or dispersing auxiliary substances 0.5-15. Also described are: a method of obtaining the processing aid and a method of manufacturing the self-supporting film, which includes dosing into an extruder a mixture of thermoplastic polyurethane and the processing aid, used in an amount from 0.5 to 35 wt % counted per the total amount of thermoplastic polyurethane, mixture melting and extrusion through a head for film extrusion with obtaining the film.

EFFECT: simplification of processing of thermoplastic polyurethanes, provision of maximally homogeneous mixing of thermoplastic polyurethane with liquid or viscofluid compounds, containing isocyanate groups.

6 cl, 2 tbl, 7 ex

FIELD: chemistry.

SUBSTANCE: invention relates to composition of propylene-based polymers and method of their obtaining. Method of polymerisation includes bringing propylene and optionally at least one other olefin under conditions of carrying out polymerisation in contact with catalyst composition, containing substituted phenylene-aromatic diester. Obtaining propylene-based polymer, characterised by flexural modulus higher than 260 klb/in2 (1793 MPa), according to determination in accordance with document ASTM D 790. Polymer composition for obtaining moulded articles contains propylene homopolymer, characterised by flexural modulus higher than 260 klb/in2 (1793 MPa), according to determination in accordance with document ASTM D 790, and substituted phenylene-aromatic diester, selected from the group, consisting of substituted 1,2-phenylenedibenzoate, 3-methyl-5-tert-butyl-1,2-phenylenedibenzoate and 3,5-diisopropyl-1,2-phenylenedibenzoate.

EFFECT: application of improved catalyst composition with obtaining propylene-based polymer, characterised by improved rigidity.

8 cl, 4 tbl, 5 ex

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