Patent Description:
High Frequency (HF) welding, also known as Dielectric Sealing or Radio Frequency (RF) Heat Sealing is a well-established technology that is known since the <NUM>'s. HF welding is fast and relatively easy to perform, produces a limited degradation of the polymer even when welding thick layers, does not create fumes, requires a moderate amount of energy and can produce water-, air-, and bacteria-proof welds.

High Frequency welding provides a method of contactless, direct, volumetric heating of dielectric materials, which are defined as materials that are capable of absorbing electromagnetic energy and which are also very poor electrical conductors. This is achieved by the application of an alternating electric field generated at the given frequency range to the dielectric material. The dielectric loss factor, also known as the dielectric loss index, is a measure of the energy loss in a material and is indicative of how well that material can be heated in the high frequency, alternating electric field. If a material has a relatively high dielectric loss index, it may be well-suited for subjection to dielectric heating. In such a case dielectric heating offers a clean and controllable process that eliminates problems associated with the application of direct heat to a variety of materials. Thus, the process has been found to be economically attractive for use in certain commercial and industrial manufacturing processes. Dielectric heating is typically carried out using radio frequency (RF) waves (<NUM> to <NUM>), which include microwaves (<NUM> to <NUM>). Together these wave ranges are referred to as high frequency (HF) waves.

In high frequency (HF) welding or sealing, at least one surface of a sheet or film of a suitable material as described above is welded or sealed, either to another surface of the same sheet or face of another sheet or film, in order to fabricate a sealed article. The resulting weld can be as strong as the original materials. The process involves subjecting the parts to be joined to a high frequency electromagnetic field, which is normally applied between two metal bars. These bars also act as pressure applicators during heating and cooling. The dynamic electric field causes the molecules in polar thermoplastics to oscillate.

Depending on their geometry and dipole moment, these molecules may translate some of this oscillatory motion into thermal energy and cause heating of the material.

The most prominent polymer usable in HF welding is polyvinyl chloride. However, chlorinated compounds may cause environmental or toxicological challenges that manufacturers would like to avoid.

Hence, it has been a constant topic of research to find means to make a normally non-lossy material such as polyolefins suitable for HF welding. One approach was to incorporate some proportion of a second, RF responsive material therein.

<CIT> discloses dielectric heating thermoplastic compositions including incorporating a molecular sieve with at least one interpolymer described as comprising (i) polymer units derived from at least one aliphatic olefin monomer having from <NUM> to <NUM> carbon atoms; and (ii) polymer units derived from (a) at least one vinyl or vinylidene aromatic monomer, or (b) from at least one sterically hindered aliphatic or cycloaliphatic vinyl or vinylidene monomer, or (c) from a combination of at least one vinyl or vinylidene aromatic monomer and at least one sterically hindered aliphatic or cycloaliphatic vinyl or vinylidene monomer, and optionally, (d) polymer units derived from at least one ethyleneically unsaturated polymerizable monomer other than that derived from (a), (b) or (c). An example thereof would be an ethylene-styrene interpolymer.

<CIT> describes HF weldable polypropylene compositions consisting of fine metal oxide particles, ion-substituted zeolite, and polypropylene. The ion-substituted zeolite, in which a portion or all of the exchangeable ions are replaced with ammonium ions and silver ions, is used as a nucleating agent and chlorine scavenger.

<CIT> proposes to use zinc oxide, bentonite clay, or crystalline and amorphous alkali or alkaline earth metal aluminosilicates as HF sensitizers for high molecular weight, high density polyethylene or ultrahigh molecular weight polyethylene. It is taught therein that the radio frequency sensitizers have to be essentially dried prior to use.

However, all of these attempts have the drawback of inclusion of materials into the composition, which are not otherwise needed for the property profile of the composition itself. Therefore, attempts were made to include the dipole characteristic directly into the polymer.

<CIT> discloses compositions comprising silane-grafted polyolefins and a crystalline zeolite. The compositions are shapeable into articles, which can be cross-linked after shaping by exposure to humidity and/or microwaves.

<CIT>) provides a polyethylene based resin composition using ethylene-vinyl acetate copolymer and ethylene-glycidyl methacrylate copolymer, in particular (A) <NUM>-<NUM> parts by weight of high-density polyethylene resin having <NUM>-<NUM>/cm<NUM> of density and <NUM>-<NUM>/<NUM> of melting index; (B) <NUM>-<NUM> parts by weight of ethylene-vinyl acetate copolymer having amount of vinyl acetate in <NUM>-<NUM> parts by weight and <NUM>-<NUM>/<NUM> of melting index; and (C) <NUM>-<NUM> parts by weight of ethylene-glycidyl methacrylate copolymer having the amount of glycidyl methacrylate in <NUM>-<NUM> parts by weight. Further attempts were made to provide HF weldable compositions based on polyolefins in combination with vinyl acetates, cf. <CIT> discloses the usage of blends of propylene-ethylene copolymers and an ethylene-alkyl acrylate copolymer for HF welding. Further attempts are based on carbon monoxide base monomers (<CIT>) and polyamides (<CIT>). Apart from the general problem of not having the possibility to process pure polyolefinic material, ethylene vinyl acetates as used in the prior art are known to have inferior mechanical properties afforded by some applications involving HF welding.

Other attempts were made, in which films were produced having different layers, wherein at least one layer has dielectric properties suitable for HF welding and the other layer is a polyolefin receiving the heat from the other layer during HF welding, i.e. in a sandwich structure, cf. <CIT>) and <CIT>). However, those applications do not allow for a pure polyolefin article to be welded by HF welding.

Therefore, in view of the problems cited above, there is still a need for polymer compositions suitable for HF welding, which avoid chlorinated material such as PVC, allow for direct processing (i.e. without the help of other materials such as molecular sieves or helper layers in the film), exhibiting good seal strength and printability. In particular, there is a need for such polymer compositions which can be formed into HF weldable structures, including, for example, a film a sheet, a foam, a profile, fibers, a molding, or a fabricated article.

It has now surprisingly been found that the above-mentioned object can be achieved by a cross-linkable polyethylene composition for high frequency welding comprising.

It has been further found that above-mentioned object is solved by an article suitable for high frequency welding comprising said cross-linkable polyethylene composition.

It has been further found that above-mentioned object is solved by the use of said cross-linkable polyethylene composition for high frequency welding.

The present invention relates to a cross-linkable polyethylene composition for high frequency welding comprising.

The cross-linkable polyethylene composition has preferably a sealing time of lower than <NUM>, preferably lower than <NUM>, and most preferably lower than <NUM>. The cross-linkable polyethylene composition has preferably a seal strength of at least <NUM> N/mm<NUM>, preferably at least <NUM> N/mm<NUM>, more preferably at least <NUM> N/mm<NUM>, and most preferably at least <NUM> N/mm<NUM>.

Thereby, the composition is preferably prepared by compounding the two polymers (A) and (B) in an extruder. In the following said two polymers are described in more detail.

Preferably, the total amount of polymers (A) and (B) in the composition is higher or equal than <NUM> wt. -% with respect to the total weight of the composition, more preferably higher or equal than <NUM> wt. -% and most preferably higher or equal than <NUM> wt.

Also preferably, the weight ratio of polymer (A) to polymer (B) in the composition is preferably in the range from <NUM>:<NUM> to <NUM>:<NUM>, more preferably from <NUM>:<NUM> to <NUM>:<NUM> and most preferably from <NUM>:<NUM> to <NUM>:<NUM>.

The term 'high frequency welding' as used herein denotes a method of contactless, direct, volumetric heating of polymers by the application of an alternating electric field generated at the given frequency range to the polymer. The method usually utilizes frequencies in the range of <NUM> to <NUM>, preferably <NUM> to <NUM>, more preferably <NUM> to <NUM>, more preferably <NUM> to <NUM>, and most preferably of <NUM>.

The crosslinkable polyolefin composition of the present invention comprises a copolymer (A) of ethylene and a C<NUM> to C<NUM> alpha-olefin co-monomer.

The copolymer (A) may encompass high density, medium density, low density and even very low density ethylene copolymers. It may preferably have a density in the range of from <NUM> to <NUM>/m<NUM>, more preferably from <NUM> to <NUM>/m<NUM>, even more preferably from <NUM>/m<NUM> to <NUM>/m<NUM>, and most preferably <NUM> to <NUM> °kg/m<NUM>, measured according to ISO <NUM>-<NUM>:<NUM>.

The copolymer (A) may preferably have a MFR<NUM> of from <NUM> to <NUM>/<NUM>, more preferably from <NUM> to <NUM>/<NUM>, even more preferably from <NUM> to <NUM>/<NUM>, and most preferably from <NUM> to <NUM>/<NUM>, measured according to ISO <NUM>.

The copolymer (A) is preferably a copolymer of ethylene with a C<NUM> to C<NUM> alpha-olefin co-monomer, more preferably with a C<NUM> to C<NUM> alpha-olefin co-monomer, such as propylene, <NUM>-butene, <NUM>-hexene, <NUM>-octene and <NUM>-decene, even more preferably with a C<NUM> to C<NUM> alpha-olefin co-monomer and still even more preferably with a C<NUM> to C<NUM> alpha-olefin co-monomer. Most preferably, copolymer (A) is a copolymer of ethylene and <NUM>-octene. The copolymer of ethylene and <NUM>-octene may preferably have a density in the range of <NUM> to <NUM>/m<NUM>, more preferably in the range of <NUM> to <NUM>/m<NUM>, even more preferably in the range of from <NUM> to <NUM>/m<NUM>, measured according to ISO <NUM>-<NUM>:<NUM>.

The ethylene copolymer (A) preferably has a DSC peak melt point measured according to ISO <NUM> of from <NUM> to <NUM>, more preferably of from <NUM> to <NUM>.

More preferably, copolymer (A) is a bipolymer of ethylene and the C<NUM> to C<NUM> alpha-olefin co-monomer, most preferably copolymer (A) is a bipolymer of ethylene and <NUM>-octene.

Preferably, ethylene-<NUM>-butene or ethylene-<NUM>-octene copolymers (plastomers) can be used. Any copolymer of ethylene and <NUM>-butene or <NUM>-octene having the above defined properties may be used. Preferred materials are commercially available, i. from Borealis under the tradename Queo, from DOW Chemical Corp (USA) under the tradename Engage or Affinity, or from Mitsui Chemicals under the tradename Tafmer.

Alternatively, these plastomers can be prepared by known processes, in a one stage or two stage polymerization process, comprising solution polymerization, slurry polymerization, gas phase polymerization or combinations therefrom, in the presence of suitable catalysts, like vanadium oxide catalysts or single-site catalysts, e.g. metallocene or constrained geometry catalysts, known to the person skilled in the art. Preferably, metallocene type catalysts are used.

Preferably, these plastomers are prepared by a one stage or two stage solution polymerization process, especially by high temperature solution polymerization process at temperatures higher than <NUM>.

Such process is essentially based on polymerizing the monomer and a suitable comonomer in a liquid hydrocarbon solvent in which the resulting polymer is soluble. The polymerization is carried out at a temperature above the melting point of the polymer, as a result of which a polymer solution is obtained. This solution is flashed in order to separate the polymer from the unreacted monomer and the solvent. The solvent is then recovered and recycled in the process.

Preferably, the solution polymerization process is a high temperature solution polymerization process, using a polymerization temperature of higher than <NUM>. More preferably, the polymerization temperature is at least <NUM>, even more preferably at least <NUM>. The polymerization temperature can be up to <NUM>.

The pressure in such a solution polymerization process is preferably in a range of <NUM> to <NUM> bar, more preferably <NUM> to <NUM> bar and even more preferably <NUM> to <NUM> bar. The liquid hydrocarbon solvent used is preferably a C<NUM>-<NUM>-hydrocarbon which may be unsubstituted or substituted by C<NUM>-<NUM> alkyl group such as pentane, methyl pentane, hexane, heptane, octane, cyclohexane, methylcyclohexane and hydrogenated naphtha. More preferably, unsubstituted C<NUM>-<NUM>-hydrocarbon solvents are used.

A known solution technology suitable for the process according to the invention is the Borceed™ technology.

The ethylene terpolymer (B) contains polar comonomer units (B1) and crosslinkable comonomer units (B2).

The ethylene terpolymer (B) may either comprise, or consist of, one or more cross-linkable ethylene copolymer(s) comprising both comonomer units (B1) and (B2), or may comprise, or consist of, a mixture of different polymers which comprises ethylene copolymers with either comonomer units (B1) or comonomer units (B2) or both comonomer units (B1) and (B2). However, regardless which polymers are used, the ethylene terpolymer (B) must contain ethylene copolymers so that both (B1) and (B2) comonomer units are present in composition (B).

Preferably, the ethylene terpolymer (B) comprises, or consists of, one or more cross-linkable ethylene copolymer(s) comprising both comonomer units (B1) and (B2), still more preferably ethylene terpolymer (B) comprises, or consists of, one cross-linkable ethylene copolymer comprising both comonomer units (B1) and (B2), and most preferably ethylene terpolymer (B) consists of one cross-linkable ethylene copolymer comprising both comonomer units (B1) and (B2).

It is preferred that in the preferred embodiment where ethylene terpolymer (B) comprises one or more, preferably one, ethylene copolymer(s) comprising both comonomer units (B1) and (B2) that the one or more, preferably one, ethylene copolymer(s) comprising both comonomer units (B1) and (B2) is present in an amount of at least <NUM> wt. -%, more preferably of at least <NUM> wt. -% of the total amount of ethylene terpolymer (B).

Ethylene copolymers having both comonomer units (B1) and (B2) are preferably obtained by copolymerization of ethylene, polar comonomer units (B1) and comonomer units with hydrolysable groups (B2). The copolymerization of the ethylene, polar comonomer units (B1) and comonomer units with hydrolysable groups (B2) may be carried out under any suitable conditions resulting in copolymerization of the monomers.

Ethylene terpolymers with both (B1) and (B2) comonomer units can be produced by radical initiated high pressure polymerization. Generally, the copolymerization of the aforementioned monomers is carried out at a temperature of about <NUM>-<NUM> and at a pressure of about <NUM>-<NUM> MPa in the presence of a radical initiator in a polymerization reactor. Usually, the polymerization is carried out continuously, preferably in a tubular reactor, or in an autoclave reactor.

Ethylene copolymers with both (B1) and (B2) comonomer units may also be produced by grafting, e.g. by the methods described in <CIT> and <CIT>. However, it is preferred that ethylene copolymers with both (B1) and (B2) comonomer units are prepared by copolymerization as described herein, and not by grafting. In other words, ethylene copolymers with both (B1) and (B2) comonomer units are preferably non-grafted ethylene copolymers with both (B1) and (B2) comonomer units.

Ethylene copolymers with both (B1) and (B2) comonomer units can be a pre-produced or in-reactor produced. Pre-produced means commercially available ethylene copolymers. Preferably, the pre-produced ethylene copolymer is a blend of two or more ethylene copolymers differing from each other, more preferably is a blend of two ethylene copolymers differing from each other.

However, ethylene copolymers with both (B1) and (B2) comonomer units are preferably in-reactor produced. Preferably, the reactor is a tubular reactor.

The polar comonomer (B1) is present in the ethylene terpolymer (B) in an amount of <NUM> to <NUM> wt.

Preferably, the polar comonomer (B1) is selected from (C<NUM>-C<NUM>)-alkyl acrylate and (C<NUM>-C<NUM>)-alkyl (C<NUM>-C<NUM>)-alkylacrylate. More preferably, the polar comonomer (B1) is selected from methyl acrylate, ethyl acrylate and/or butyl acrylate. Among these, methyl acrylate (MA) is most preferred.

Preferably, the ethylene terpolymer (B) has a MFR<NUM> (<NUM>/<NUM>) measured according to ISO <NUM> in the range from <NUM> to <NUM>/<NUM>, preferably in the range from <NUM> to <NUM>/<NUM>.

The crosslinking of ethylene copolymers with polar comonomer units and crosslinkable comonomer units is well known in the art and can be carried out by socalled moisture curing, see for example <CIT>. A silanol condensation catalyst is used as a catalyst.

The advantage of an in-reactor produced ethylene copolymer with both (B1) and (B2) comonomer units is that it can be directly used in the subsequent steps of the process of the invention.

Preferably, the cross-linkable comonomer (B2) is present in the ethylene copolymer composition (B) in an amount of <NUM> to <NUM> wt. -%, more preferably in an amount of <NUM> to <NUM> wt. -%, still more preferably in an amount of <NUM> to <NUM> wt. -%, and most preferably in an amount of <NUM> wt. -% to <NUM> wt.

Preferably, the cross-linkable comonomer units (B2) are comonomer units with hydrolysable silane-groups.

Hence, preferably, the cross-linkable comonomer units (B2) is represented by formula (I):.

Specific examples of the cross-linkable comonomer units (B2) are those wherein R<NUM> is vinyl, allyl, isopropenyl, butenyl, cyclohexenyl or gamma- (meth) acryloxy propyl; Y is methoxy, ethoxy, formyloxy, acetoxy, propionyloxy or an alkyl-or arylamino group; and R<NUM>, if present, is a methyl, ethyl, propyl, or decyl group.

A preferred cross-linkable comonomer (B2) is represented by formula (II):.

wherein A is a hydrocarbyl group having <NUM>-<NUM> carbon atoms, preferably <NUM>-<NUM> carbon atoms.

Most preferably, the cross-linkable comonomers (B2) comprise vinyl trimethoxysilane (VTMS), vinyl bismethoxyethoxysilane, vinyl triethoxysilane, gamma-(meth)acryloxypropyltrimethoxysilane, gamma(meth)-acryloxypropyltriethoxysilane, vinyl triacetoxysilane and combinations thereof.

In a preferred embodiment of the present invention, the cross-linkable polyethylene composition further comprises a silanol condensation catalyst (C).

Preferably, the silanol condensation catalyst (C) comprises, or consists of, a tin based catalyst or a sulphonic acid based catalyst, more preferably comprises, or consist of, a sulphonic acid based catalyst. The tin based catalyst is preferably dibutyl tin dilaureate (DBTL).

The sulphonic acid based catalyst is preferably represented by formula (III):.

or a precursor thereof, Ar being a benzene ring substituted with at least one hydrocarbyl radical such that the total number of carbon atoms of the hydrocarbyl radical(s) is <NUM>-<NUM>, or a naphthalene ring substituted with at least one hydrocarbyl radical such that the total number of carbon atoms of the hydrocarbyl radical(s) is <NUM>-<NUM>, and the catalyst of formula (III) containing <NUM>-<NUM> carbon atoms in total. This catalyst, as opposed to conventional silanol condensation catalysts, such as e.g. DBTL, allows crosslinking at ambient temperature, such as at room temperature.

Such organic sulphonic acids are described e.g. in <CIT>, or alternatively, in <CIT> and <CIT>.

Preferably, the silanol condensation catalyst (C) is present in an amount of <NUM> to <NUM> wt. -%, or <NUM> - <NUM> mol-% based on the total polyethylene composition.

If a masterbatch containing the catalyst is used, it is preferably used in an amount of <NUM> to <NUM> wt. -%, more preferably <NUM> to <NUM> wt. -%, and most preferably <NUM> to <NUM> wt. -%, based on the total polyethylene composition.

In addition to the base resin, usual additives for utilization with polyolefins, such as pigments, stabilizers (antioxidant agents), antiacids and/or anti-UVs, antistatic agents and utilization agents (such as processing aid agents) may be present in the polyethylene composition. Preferably, the amount of these additives is <NUM> wt. % or below, further preferred <NUM> wt. % or below, still more preferred <NUM> wt. % or below, and still more preferred <NUM> wt. % or below of the total composition.

The present invention further provides a cross-linkable polyethylene composition obtainable by a process as described above.

The invention further provides an article suitable for welding comprising, or consisting of, the cross-linkable polyethylene composition, or consisting of, the crosslinkable polyethylene composition according to the invention.

Preferably, the article is a seal or a film, in particular a tarpaulin, a belt, a sunroof, a tent, and/or geotextiles.

Finally, the invention relates to the use of the cross-linkable polyethylene composition according to the invention for high frequency welding.

The melt flow rate (MFR) was determined according to ISO <NUM> and is indicated in g/<NUM>. The MFR is an indication of the melt viscosity of the polymer. The MFR is determined at <NUM> for PE and <NUM> for PP. The load under which the melt flow rate is determined is usually indicated as a subscript, for instance MFR<NUM> is measured under <NUM> load (condition D).

Density of the polymer was measured according to ISO <NUM> / <NUM>-2B. For the purpose of this invention the density of the blend can be calculated from the densities of the components according to: <MAT> where.

The content (wt. -% and mol-%) of polar comonomer present in the polymer and the content (wt. -% and mol-%) of silane group(s) containing units (preferably comonomer) present in the polymer composition (preferably in the polymer):
Quantitative nuclear-magnetic resonance (NMR) spectroscopy was used to quantify the comonomer content of the polymer composition or polymer as given above or below in the context.

Quantitative <NUM>H NMR spectra recorded in the solution-state using a Bruker Advance III <NUM> NMR spectrometer operating at <NUM>. All spectra were recorded using a standard broad-band inverse <NUM> probehead at <NUM> using nitrogen gas for all pneumatics. Approximately <NUM> of material was dissolved in <NUM>,<NUM>-tetrachloroethane-d<NUM> (TCE-d<NUM>) using ditertiarybutylhydroxytoluen (BHT) (<NPL>) as stabiliser. Standard single-pulse excitation was employed utilising a <NUM> degree pulse, a relaxation delay of <NUM> and no sample rotation. A total of <NUM> transients were acquired per spectra using <NUM> dummy scans. A total of <NUM> data points were collected per FID with a dwell time of <NUM>, which corresponded to a spectral window of approx. The FID was then zero filled to <NUM> data points and an exponential window function applied with <NUM> line-broadening. This setup was chosen primarily for the ability to resolve the quantitative signals resulting from methylacrylate and vinyltrimethylsiloxane copolymerisation when present in the same polymer.

Quantitative <NUM>H NMR spectra were processed, integrated and quantitative properties determined using custom spectral analysis automation programs. All chemical shifts were internally referenced to the residual protonated solvent signal at <NUM> ppm.

When present characteristic signals resulting from the incorporation of vinylacytate (VA), methyl acrylate (MA), butylacrylate (BA) and vinyltrimethylsiloxane (VTMS), in various comonomer sequences, were observed[<NUM>]. All comonomer contents calculated with respect to all other monomers present in the polymer.

The vinylacytate (VA) incorporation was quantified using the integral of the signal at <NUM> ppm assigned to the *VA sites, accounting for the number of reporting nuclie per comonomer and correcting for the overlap of the OH protons from BHT when present: <MAT>.

The methylacrylate (MA) incorporation was quantified using the integral of the signal at <NUM> ppm assigned to the 1MA sites, accounting for the number of reporting nuclie per comonomer: <MAT>.

The butylacrylate (BA) incorporation was quantified using the integral of the signal at <NUM> ppm assigned to the 4BA sites, accounting for the number of reporting nuclie per comonomer: <MAT>.

The vinyltrimethylsiloxane incorporation was quantified using the integral of the signal at <NUM> ppm assigned to the 1VTMS sites, accounting for the number of reporting nuclei per comonomer: <MAT>.

Characteristic signals resulting from the additional use of BHT as stabiliser, were observed. The BHT content was quantified using the integral of the signal at <NUM> ppm assigned to the ArBHT sites, accounting for the number of reporting nuclei per molecule: <MAT>.

The ethylene comonomer content was quantified using the integral of the bulk aliphatic (bulk) signal between <NUM> - <NUM> ppm. This integral may include the 1VA (<NUM>) and αVA (<NUM>) sites from isolated vinylacetate incorporation, *MA and αMA sites from isolated methylacrylate incorporation, 1BA (<NUM>), 2BA (<NUM>), 3BA (<NUM>), *BA (<NUM>) and αBA (<NUM>) sites from isolated butylacrylate incorporation, the *VTMS and αVTMS sites from isolated vinylsilane incorporation and the aliphatic sites from BHT as well as the sites from polyethylene sequences. The total ethylene comonomer content was calculated based on the bulk integral and compensating for the observed comonomer sequences and BHT: <MAT>.

It should be noted that half of the α signals in the bulk signal represent ethylene and not comonomer and that an insignificant error is introduced due to the inability to compensate for the two saturated chain ends (S) without associated branch sites.

The total mole fractions of a given monomer (M) in the polymer was calculated as: <MAT>.

The total comonomer incorporation of a given monomer (M) in mole percent was calculated from the mole fractions in the standard manner: <MAT>.

The total comonomer incorporation of a given monomer (M) in weight percent was calculated from the mole fractions and molecular weight of the monomer (MW) in the standard manner: <MAT>.

If characteristic signals from other specific chemical species are observed the logic of quantification and/or compensation can be extended in a similar manor to that used for the specifically described chemical species. That is, identification of characteristic signals, quantification by integration of a specific signal or signals, scaling for the number of reported nuclei and compensation in the bulk integral and related calculations. Although this process is specific to the specific chemical species in question the approach is based on the basic principles of quantitative NMR spectroscopy of polymers and thus can be implemented by a person skilled in the art as needed.

A TX HF-welding machine of Forsstrom High Frequency AB was used for welding the films. Dimensions of the line were <NUM> kW, the sealing bar 1200x25 mm and sealing pressure of <NUM> bar for polyolefins (<NUM>/cm<NUM>) and <NUM> bar for PVC (CE1). The base strip of the HF-welding bar was covered by a teflon strip.

Seal strength measurement of ultrasonic welded samples:
Analysis was performed on a tensile testing equipment with requirements as described in ISO <NUM>-<NUM>. From the samples <NUM> wide specimen are cut and mounted with the seal positioned halfway in between the clamps. Following settings are used: gauge length <NUM>, pre-load <NUM> N for <NUM>, test speed <NUM>/min, break detection at <NUM>% Fmax.

Surface energy is determined via wetting tension according to ASTM D2578-<NUM> using test-inks (mixtures of formamide and ethyl cellosolve) with a surface tension in between <NUM> and <NUM> dynes/cm, namely "AFS corona treatment tester", supplied by AFS, Augsburg, Germany.

It is important, that the tested surface area is not roughened before wetting but as smooth as possible.

The inks are applied with cotton buds over a surface of <NUM><NUM>, starting with a low surface tension-ink until an ink is used, which does not wet the surface anymore The surface tension is then determined visually by estimating how the liquid reacts within the first two seconds following application of the ink onto the surface. The test liquid can shrink and/or form itself into globules (individual droplets) or it can remain unchanged forming an ink-film on the test-film. When a test liquid shrinks or forms into droplets it indicates that the film has a lower surface energy than the liquid applied.

The test should be repeated as many times as necessary with test-inks having surface tension values of +/- <NUM> dynes/cm different from the first measured dynevalue, until the marking remains stable for a period of two seconds or more. Once that has been achieved, the film can be said to have that level or surface energy at least equal to that of the liquid applied.

Further applications should be made until shrinkage or droplets occur within two seconds. This last measurement should be taken as failure, and the surface energy of the liquid used for the previous measurement should be taken to be the surface energy of the film.

The surface tension for the inventive and comparative examples was tested after eight months of aging.

A1 is a very low density copolymer of polyethylene and <NUM>-octene having a density of <NUM>/m<NUM>, a MFR<NUM> (<NUM>, <NUM>) of <NUM>/<NUM>, and a peak melt point of <NUM>. It is commercially available as Queo <NUM> from Borealis AG (Austria).

A2 is a very low density copolymer of polyethylene and <NUM>-octene having a density of <NUM>/m<NUM>, a MFR<NUM> (<NUM>, <NUM>) of <NUM>/<NUM>, and a peak melt point of <NUM>. It is commercially available as Queo 8201LA from Borealis AG (Austria).

B1 is a poly(ethylene-co-butylacrylate) with density of <NUM>/m<NUM>, MFR<NUM> of <NUM>/<NUM>, an acrylate content of <NUM> wt. -% and Tm of <NUM>, produced in a commercial high pressure tubular reactor.

B2 is a terpolymer of ethylene, methyl acrylate and vinyl trimethoxysilane (VTMS) having <NUM> wt. -% methyl acrylate and <NUM> wt. -% VTMS, a MFR<NUM> (<NUM>, <NUM>) of <NUM>/<NUM>, and MFR<NUM> (<NUM>, <NUM>) of <NUM>/<NUM>, obtained according to a process as described in <CIT>.

C1 is Ambicat LE4476, which is dodecyl-benzene sulphonic acid (DBSA) used as a silanol condensation catalyst. It is commercially available from Borealis AG (Austria).

The films comprising the polymer compositions according to the examples were produced by dry-mixing the components using the weight percentages given in Table <NUM> and immediately extruding them on a Reifenhauser cast film line using the parameters as provided in Table <NUM>.

To the sealed films, a PET tape was applied to measure more correctly the seal strength of the films in order to avoid elongation. The films of the present examples are very elastic and to avoid too much elongation, the PET adhesive tape was applied at the outer side of the HF-sealed film before testing the seal strength.

Comparative example CE1 uses the commonly used PVC resulting in fast sealing times, but not very good sealing strengths.

Comparative examples CE4-<NUM> prove the good sealability of acrylate containing polyethylenes, but still have low dyne retention values. CE6 shows that compositions using only terpolymer have the problem of instant cross-linking in combination with silanol condensation catalysts. Nevertheless, CE6 still shows good dyne retention.

It can be further seen that samples having pure A1 or A2 require higher power of the sealing equipment and sealing time was longer.

Claim 1:
A cross-linkable polyethylene composition for high frequency welding comprising
- a copolymer (A) of ethylene and an α-olefin comonomer (A1) with <NUM> to <NUM> carbon atoms having a density of from <NUM> to <NUM>/m<NUM>, and
- a terpolymer (B) of ethylene, a polar comonomer (B1) and a crosslinkable comonomer (B2)
wherein the polar comonomer (B1) is present in the ethylene terpolymer (B) in an amount in the range of <NUM> to <NUM> wt-% with respect to the total weight of the ethylene terpolymer (B).