The present invention relates to a metallocene-catalysed multimodal polyethylene copolymer (P), to the use of the multimodal polyethylene copolymer (P) in film applications and to a film comprising the polymer composition of the invention.

Unimodal polyethylene (PE) polymers, for instance SSC products, are usually used for film applications. Unimodal PE polymers have for instance good optical properties, like low haze, but for instance, the melt processing of such polymers is not satisfactory in production point of view and may cause quality problems of the final product as well. Multimodal PE polymers with two or more different polymer components are better to process, but e.g. melt homogenisation of the multimodal PE may be problematic resulting in inhomogeneous final products evidenced e.g. by high gel content of the final product.

WO 2021009189, WO 2021009190 and WO 2021009191 of Borealis disclose a process for preparing multimodal PE polymers in two loop reactors and one gas phase reactor.

The polymers produced in the Examples have a total density of 938 or 939 kg/m ³ . The MFR2 (190°C, 2.16 kg, ISO 1133) of the polymer components produced in the first loop is 22 g/10 min. Film properties, like sealing initiation temperature (SIT) are not mentioned at all.

Also WO 2021009192 discloses such a process. The polymer produced in the Examples has an even higher density of 951 kg/m ³ . The MFR2 (190°C, 2.16 kg, ISO 1133) of the polymer component produced in the first loop is 32 g/10 min. Film properties, like sealing initiation temperature (SIT) are not mentioned at all.

WO2021013552, Reference Example RE3 discloses a polymer comprising an ethylene-1- butene polymer component and an ethylene-1 -hexene polymer component, produced in one loop reactor and one gas phase reactor using as metallocene complex bis(l-methyl-3- n-butylcyclopentadienyl) zirconium (IV) dichloride. Films produced with such a polymer have a sealing initiation temperature (SIT) of 91 °C and a dart drop impact strength of 345 g only.

WO2021191018 disclose a process for preparing multimodal PE polymers in two loop reactors and one gas phase reactor using as metallocene complex bis(l-methyl-3-n- butylcyclopentadienyl) zirconium (IV) dichloride. The polymer according to IE1 has a MFR2 of the polymer produced in the gas phase reactor of 1.65 g/10 min. The film made with this polymer has quite high haze of 42.2% W02016083208 again discloses a polymer comprising an ethylene-1 -butene polymer component and an ethylene-1 -hexene polymer component, produced in one loop reactor and one gas phase reactor using as metallocene complex bis(l-methyl-3-n- butylcyclopentadienyl) zirconium (IV) dichloride. Film properties, like sealing initiation temperature (SIT) or dart drop impact strength (DDI) are not mentioned at all.

US2014194277 discloses blends of two different separately produced (each in one reactor only) polyethylene copolymers (A) and (B). Film properties, like sealing initiation temperature (SIT) or dart drop impact strength (DDI) are not mentioned at all.

There is a continuous need to find multimodal PE polymers with different property balances for providing tailored solutions to meet the increasing demands of the end application producers e.g. for reducing the production costs while maintaining or even improving the end-product properties. Tailored polymer solutions are also needed to meet the requirements of continuously developing equipment technology in the end application field. Therefore, there is a need in the art for providing a material that provides low sealing initiation temperature, good optical properties and mechanical properties, especially dart drop (impact strength). In other words, a material is desirable that provides an advantageous combination of preferable sealing properties, good optics and mechanical properties, especially SIT, haze and dart drop, to films prepared from such a material.

Description of the invention

The present invention is therefore directed to a metallocene-catalysed multimodal polyethylene copolymer (P), which consists of

(i) 30.0 to 70.0 wt% of an ethylene-1 -butene polymer component (A), and

(ii) 70.0 to 30.0 wt% of an ethylene-1 -hexene polymer component (B), whereby the ethylene-1 -butene polymer component (A) has a density in the range of from 920 to 950 kg/m ³ , an MFR2 (190°C, 2.16 kg, ISO 1133) in the range of from 2.0 to 40.0 g/10 min, a 1 -butene content in the range of 0.5 to 5.0 wt%, based on the ethylene-1 -butene polymer component (A) and an isolated 1 -butene comonomer unit amount of > 95 %, whereby the isolated 1 -butene comonomer unit amount is calculated according to formula (I)

EXE

EXE% = 100 X

EXE + EXX + XXX

X being the number of 1 -butene branches per 1000 carbon (kCb); and wherein ethylene-1 -butene polymer component (A) consists of an ethylene polymer fraction (A-1) and an ethylene polymer fraction (A-2), wherein the ethylene polymer fraction (A-1) has a density in the range of 920 to 960 kg/m ³ ; and a MFR ₂ (190°C, 2.16 kg, ISO 1133) in the range of 1.0 to 20.0 g/10 g/10 min, and the ethylene polymer fraction (A-2) has a density in the range of from 930 to 950 kg/m ³ , and a MFR ₂ (190°C, 2.16 kg, ISO 1133) in the range of 3.0 to 40.0 g/10 min; and the ethylene polymer component (B) has a density in the range of from 880 to 915 kg/m ³ , an MFR ₂ (190°C, 2.16 kg, ISO 1133) in the range of from 0.01 to 1.5 g/10 min a 1 -hexene content in the range of 15.0 to 25.0 wt% based on the ethylene-1 -hexene polymer compound (B), an isolated 1 -hexene comonomer unit amount according to formula (I), wherein X being the number of 1 -hexene branches per 1000 carbon (kCb); fulfilling the equation EXE% > -1.1875 * C6 (of (B) in wt%) + 110.41 ; and whereby the multimodal polyethylene copolymer (P) has a density in the range of from 905 to 915 kg/m ³ , an MFR ₂ (190°C, 2.16 kg, ISO 1133) in the range of from 0.5 to below 2.0 g/10 min and a ratio of the MFR ₂₁ (190°C, 21.6 kg, ISO 1133) to MFR ₂ (190°C, 2.16 kg, ISO 1133), MFR ₂ I/MFR ₂ , in the range of from 22 to 50.

Unexpectedly the multimodal polyethylene copolymer (P) of the invention provides improved sealing properties to films, such as especially low sealing initiation temperature (SIT) in combination with improved mechanical properties to films such as high dart drop strength (DDI).

The invention is therefore further directed to a film comprising at least one layer comprising the metallocene-catalysed multimodal polyethylene copolymer (P). The film is characterized by a sealing initiation temperature (SIT) measured as described in the experimental part on a 40 pm monolayer test blown film of below 82°C, preferably in the range of 60°C to 80°C, more preferably in the range of 65°C to 78°C, like 68°C to 78°C.

In an embodiment of the invention the films furthermore have in addition to the low SIT, a dart drop impact (DDI) determined according to ASTM D1709, method A on a 40 pm monolayer test blown film of at least 1000 g to more than 1700 g, preferably at least 1200 g to more than 1700 g, more preferably at least 1500 g to more than 1700 g.

Definitions

Where the term "comprising" is used in the present description and claims, it does not exclude other non-specified elements of major or minor functional importance. For the purposes of the present invention, the term "consisting of" is considered to be a preferred embodiment of the term "comprising of". If hereinafter a group is defined to comprise at least a certain number of embodiments, this is also to be understood to disclose a group, which preferably consists only of these embodiments.

Whenever the terms "including" or "having" are used, these terms are meant to be equivalent to "comprising" as defined above.

Where an indefinite or definite article is used when referring to a singular noun, e.g. "a", "an" or "the", this includes a plural of that noun unless something else is specifically stated.

Metallocene catalysed multimodal polyethylene copolymer is defined in this invention as multimodal polyethylene copolymer (P), which has been produced in the presence of a metallocene catalyst.

Term “multimodal” in context of multimodal polyethylene copolymer (P) means herein multimodality with respect to melt flow rate (MFR) of the ethylene polymer components (A) and (B) as well as ethylene polymer fraction (A-1) and (A-2), i.e. the ethylene polymer components (A) and (B), as well as fractions (A-1) and (A-2) have different MFR values. The multimodal polyethylene copolymer (P) can have further multimodality with respect to one or more further properties between the ethylene polymer components (A) and (B) as well as between fractions (A-1) and (A-2), as will be described later below. The multimodal polyethylene copolymer (P) of the invention as defined above, below or in claims is also referred herein shortly as “multimodal PE” or “multimodal copolymer (P)”.

For the purpose of the present invention “multimodal polyethylene copolymer (P) which comprises polyethylene component (A) and polyethylene component (B)” means that the multimodal polyethylene copolymer (P) is produced in an at least 2-stage sequential polymerization process, wherein first component (A) is produced and component (B) is then produced in the presence of component (A) in a subsequent polymerization step, yielding the multimodal polyethylene copolymer (P) or vice versa, i.e. first component (B) is produced and component (A) is then produced in the presence of component (B) in a subsequent polymerization step, yielding the multimodal polyethylene copolymer (P). Polyethylenes produced in a multistage process are also designated as "in-situ" or “reactor” blends. The resulting end product consists of an intimate mixture of the polymers from the two or more reactors, the different molecular-weight-distribution curves of these polymers together forming a molecular-weight-distribution curve having a broad maximum or two or more maxima, i.e. the end product is a multimodal polymer mixture.

The following preferable embodiments, properties and subgroups of multimodal PE and the ethylene polymer components (A) and (B) thereof, as well as the ethylene polymer fractions (A-1) and (A-2) and the film of the invention including the preferable ranges thereof, are independently generalisable so that they can be used in any order or combination to further define the preferable embodiments of the multimodal PE and the article of the invention.

Multimodal PE as well as ethylene polymer component (A) and (B) and ethylene polymer fractions (A-1) and (A-2)

The metallocene produced multimodal polyethylene copolymer (P) is referred herein as “multimodal”, since the ethylene-1 -butene polymer component (A), including ethylene polymer fractions (A-1) and (A-2), and ethylene-1 -hexene polymer component (B) have been produced under different polymerization conditions resulting in different Melt Flow Rates (MFR, e.g. MFR2). I.e. the multimodal PE is multimodal at least with respect to difference in MFR of the ethylene polymer components (A) and (B).

The metallocene produced multimodal polyethylene copolymer (P) consists of

(i) 30.0 to 70.0 wt% of an ethylene-1 -butene polymer component (A), and

(ii) 70.0 to 30.0 wt% of an ethylene-1 -hexene polymer component (B). The amount of (A) and (B) add up to 100.0 wt%.

The ethylene-1 -butene polymer component (A) consists of an ethylene polymer fraction (A- 1) and (A-2), whereby the MFR2 of the ethylene polymer fractions (A-1) and (A-2) may be different from each other.

The ethylene polymer fraction (A-1) has a MFR2 (190°C, 2.16 kg, ISO 1133) in the range of 1.0 to 20.0 g/10 min, preferably of 1.5 to 18.0 g/10 min, more preferably of 2.0 to 16.0 g/10 min and even more preferably of 2.5 to 14.0 g/10 min, like 3.0 to 12.0 g/10 min.

The ethylene polymer fraction (A-2) has a MFR2 (190°C, 2.16 kg, ISO 1133) in the range of 3.0 to 40.0 g/10 min, preferably of 3.2 to 30.0 g/10 min, more preferably of 3.5 to 20.0 g/10 min and most preferably of 3.5 to 10.0 g/10 min.

The MFR2 of the ethylene polymer components (A) and (B) are different from each other.

The ethylene polymer component (A) has a MFR2 (190°C, 2.16 kg, ISO 1133) in the range of 2.0 to 40 g/10 min, preferably of 2.5 to 30 g/10 min, more preferably of 3.0 to 20 g/10 min and even more preferably of 3.2 to 10 g/10 min.

The ethylene polymer component (B) has a MFR2 (190°C, 2.16 kg, ISO 1133) in the range of 0.01 to 1.5 g/10 min, preferably of 0.05 to 1.5 g/10 min, more preferably of 0.1 to 1.2 g/10 min and even more preferably of 0.2 to 1.0 g/10 min.

The MFR2 (190°C, 2.16 kg, ISO 1133) of the multimodal copolymer (P) is in the range of 0.5 to 2.0 g/10 min, preferably 0.8 to 1.8 g/10 min, more preferably 1.0 to 1.5 g/10 min.

The multimodal copolymer (P) has a ratio of the MFR21 (190°C, 21.6 kg, ISO 1133) to MFR2 (190°C, 2.16 kg, ISO 1133), MFR21/MFR2, in the range of from 22 to 50, preferably from 25 to 40, more preferably from 28 to 35.

In an embodiment of the invention it is preferred the ratio of the MFR2 (190°C, 2.16 kg, ISO 1133) of ethylene-1 -butene polymer component (A) to the MFR2 (190°C, 2.16 kg, ISO 1133) of the final multimodal copolymer (P) is at least 2.5 to 20.0, preferably 3.0 to 15.0 and more preferably of 3.5 to 10.0.

Naturally, in addition to multimodality with respect to, i.e. difference between, the MFR2 of ethylene polymer components (A) and (B), the multimodal PE of the invention can also be multimodal e.g. with respect to one or both of the two further properties: multimodality with respect to, i.e. difference between, the comonomer content(s) present in the ethylene polymer components (A) and (B); and/or the density of the ethylene polymer components (A) and (B).

Preferably, the multimodal copolymer (P) is further multimodal with respect to the comonomer content of the ethylene polymer components (A) and (B).

The comonomer type for the polymer fractions (A-1) and (A-2) is the same, thus both fractions therefore have 1 -butene as comonomer.

The comonomer content of component (A) and (B) can be measured, or, in case, and preferably, one of the components is produced first and the other thereafter in the presence of the first produced in so called multistage process, then the comonomer content of the first produced component, e.g. component (A), can be measured and the comonomer content of the other component, e.g. component (B), can be calculated according to following formula:

Comonomer content (mol%) in component B = (comonomer content (mol%) in final product - (weight fraction of component A * comonomer content (mol%) in component A)) / (weight fraction of component B)

The total amount of 1 -butene, based on the multimodal polymer (P) is preferably in the range of from 0.1 to 1.0 wt%, preferably 0.2 to 0.8 wt% and more preferably 0.3 to 0.6 wt%. The total amount of 1 -hexene, based on the multimodal polymer (P) preferably is in the range of 2.0 to 20.0 wt%, preferably 4.0 to 18.0 wt% and more preferably 6.0 to 15.0 wt%. The total amount (wt%) of 1 -butene, present in the ethylene-1 -butene polymer component

(A) is of 0.5 to 5.0 wt%, preferably of 0.8 to 4.0 wt%, more preferably of 1.0 to 3.0 wt%, even more preferably of 1.0 to 2.0 wt%, based on the ethylene-1 -butene polymer component (A).

The total amount (wt%) of 1 -hexene, present in the ethylene-1 -hexene polymer component

(B) is of 15.0 to 25.0 wt%, preferably of 16.0 to 22.0 wt%, more preferably of 17.0 to 20.0 wt%, based on the ethylene-1 -hexene polymer component (B).

Even more preferably the multimodal polymer (P) of the invention is further multimodal with respect to difference in density between the ethylene polymer component (A) and ethylene polymer component (B). Preferably, the density of ethylene polymer component (A) is different, preferably higher, than the density of the ethylene polymer component (B).

The density of the ethylene polymer component (A) is in the range of 920 to 950 kg/m ³ , preferably of 925 to 950 kg/m ³ , more preferably 930 to 945 kg/m ³ and/or the density of the ethylene polymer component (B) is of in the range of 880 to 915 kg/m ³ , preferably of 885 to 905 kg/m ³ and more preferably of 888 to 900 kg/m ³ .

The polymer fraction (A-1) has a density in the range of from 920 to 960 kg/m ³ , preferably of 925 to 955 kg/m ³ , more preferably of 930 to 950 kg/m ³ , like 935 to 945 kg/m ³ .

The density of the polymer fraction (A-2) is in the range of from 930 to 950 kg/m ³ , preferably of 935 to 945 kg/m ³ .

The metallocene catalysed multimodal copolymer (P) is preferably a linear low density polyethylene (LLDPE) which has a well known meaning.

The density of the multimodal copolymer (P) is in the range of 905 to 915 kg/m ³ , preferably of 908.0 to 915 kg/m ³ and more preferably of 910.0 to 915.0 kg/m ³ .

More preferably the multimodal copolymer (P) is multimodal at least with respect to, i.e. has a difference between, the MFR2, the comonomer content as well as with respect to, i.e. has a difference between the density of the ethylene polymer components, (A) and (B), as defined above, below or in the claims including any of the preferable ranges or embodiments of the polymer composition. Furthermore, the ethylene-1 -butene polymer component (A) is characterized by an isolated 1 -butene comonomer unit amount of > 95.0%, preferably at least 98.0% and more preferably 100%. The isolated comonomer unit amount is calculated according to formula

(I)

EXE

EXE% = 100 X

EXE + EXX + XXX wherein X being the number of 1 -butene branches per 1000 carbon (kCb).

In addition, the ethylene-1 -hexene polymer component (B) has an isolated 1-hexene comonomer unit amount according to formula (I), wherein X being the number of 1 -hexene branches per 1000 carbon (kCb); fulfilling the equation EXE% > -1.1875 * C6 (of (B) in wt%) + 110.41

Preferably, the ethylene-1 -hexene polymer component (B) fulfils the equation EXE% > -1.1875 * C6 (of (B) in wt%) + 111.41 , more preferably EXE% > -1.1875 * C6 (of (B) in wt%) + 112.41 and even more preferably EXE% > -1.1875 * C6 (of (B) in wt%) + 113.41.

The isolated 1 -hexene comonomer unit amount for component (B) is preferably > 92.0%, preferably at least 93.0% and more preferably at least 94.0%.

A suitable upper limit is < 100%, preferably 99.0 %, more preferably 98.0%.

It is within the scope of the invention, that the first and the second ethylene polymer fraction (A-1 and A-2) of the ethylene polymer component (A) are present in a weight ratio of 4:1 up to 1 :4, such as 3:1 to 1:3, or 2:1 to 1:2, or 1:1.

The ethylene polymer component (A) is present in an amount of 30.0 to 70.0 wt% based on the multimodal copolymer (P), preferably in an amount of 32.0 to 55.0 wt% and even more preferably in an amount of 34.0 to 45.0 wt%.

Thus, the ethylene polymer component (B) is present in an amount of 70.0 to 30.0 wt% based on the multimodal copolymer (P), preferably in an amount of 68.0 to 45.0 wt% and more preferably in an amount of 66.0 to 55.0 wt%.

The metallocene catalysed multimodal copolymer (P) can be produced with a 3-stage process, preferably comprising a first slurry reactor (loop reactor 1), whereby the first slurry loop reactor is connected in series with another slurry reactor (loop reactor 2), so that the first ethylene polymer fraction (A-1) produced in the loop reactor 1 is fed to the loop reactor 2, wherein the second ethylene polymer fraction (A-2) is produced in the presence of the first fraction (A-1). The loop reactor 2 is thereby connected in series to a gas phase reactor (GPR), so that the first ethylene polymer component (A) leaving the second slurry reactor is fed to the GPR to produce a trimodal polyethylene copolymer. In this case, the reaction conditions in the two slurry reactors are chosen in a way that in the two slurry reactors different products in view of MFR and/or density are produced.

Such a process is described inter alia in WO 2016/198273, WO 2021009189, WO 2021009190, WO 2021009191 and WO 2021009192. Full details of howto prepare suitable metallocene catalysed multimodal copolymer (P) can be found in these references.

A suitable process is the Borstar PE process or the Borstar PE 3G process.

The metallocene catalysed multimodal copolymer (P) according to the present invention is therefore preferably produced in a loop loop gas cascade. Such polymerization steps may be preceded by a prepolymerization step. The purpose of the prepolymerization is to polymerize a small amount of polymer onto the catalyst at a low temperature and/or a low monomer concentration. By prepolymerization it is possible to improve the performance of the catalyst in slurry and/or modify the properties of the final polymer. The prepolymerization step is preferably conducted in slurry and the amount of polymer produced in an optional prepolymerization step is counted to the amount (wt%) of ethylene polymer component (A).

The catalyst components are preferably all introduced to the prepolymerization step when a prepolymerization step is present. However, where the solid catalyst component and the cocatalyst can be fed separately it is possible that only a part of the cocatalyst is introduced into the prepolymerization stage and the remaining part into subsequent polymerization stages. Also in such cases it is necessary to introduce so much cocatalyst into the prepolymerization stage that a sufficient polymerization reaction is obtained therein.

It is understood within the scope of the invention, that the amount or polymer produced in the prepolymerization lies within 1 to 5 wt% in respect to the final metallocene catalysed multimodal copolymer (P). This can counted as part of the first ethylene polymer component (A). Catalyst

The metallocene catalysed multimodal copolymer (P) used in the process of the invention is one made using a metallocene catalyst. A metallocene catalyst comprises a metallocene complex and a cocatalyst. The metallocene compound or complex is referred herein also as organometallic compound (C).

The organometallic compound (C) comprises a transition metal (M) of Group 3 to 10 of the Periodic Table (lUPAC 2007) or of an actinide or lanthanide.

The term "an organometallic compound (C)" in accordance with the present invention includes any metallocene or non-metallocene compound of a transition metal, which bears at least one organic (coordination) ligand and exhibits the catalytic activity alone or together with a cocatalyst. The transition metal compounds are well known in the art and the present invention covers compounds of metals from Group 3 to 10, e.g. Group 3 to 7, or 3 to 6, such as Group 4 to 6 of the Periodic Table, (lUPAC 2007), as well as lanthanides or actinides.

In an embodiment, the organometallic compound (C) has the following formula (II): wherein each X is independently a halogen atom, a Ci- ₆ -alkyl, Ci- ₆ -alkoxy group, phenyl or benzyl group; each Het is independently a monocyclic heteroaromatic group containing at least one heteroatom selected from O or S;

L is -R'2Si-, wherein each R’ is independently Ci-20-hydrocarbyl or Ci-10-alkyl substituted with alkoxy having 1 to 10 carbon atoms;

M is Ti, Zr or Hf; each R ¹ is the same or different and is a Ci- ₆ -alkyl group or Ci- ₆ -alkoxy group; each n is 1 to 2; each R ² is the same or different and is a Ci- ₆ -alkyl group, Ci- ₆ -alkoxy group or -Si(R)3 group; each R is Ci-10-alkyl or phenyl group optionally substituted by 1 to 3 Ci- ₆ -alkyl groups; and each p is 0 to 1.

Preferably, the compound of formula (II) has the structure wherein each X is independently a halogen atom, a Ci- ₆ -alkyl, Ci- ₆ -alkoxy group, phenyl or benzyl group;

L is a Me2Si-; each R ¹ is the same or different and is a Ci- ₆ -alkyl group, e.g. methyl or t-Bu; each n is 1 to 2;

R ² is a -Si(R)3 alkyl group; each p is 1; each R is Ci- ₆ -alkyl or phenyl group.

Highly preferred complexes of formula (II) are

Most preferably the complex dimethylsilanediylbis[2-(5-trimethylsilylfuran-2-yl)-4,5- dimethylcyclopentadien-1-yl] zirconium dichloride is used.

More preferably the ethylene polymer components (A) and (B) of the multimodal copolymer (P) are produced using, i.e. in the presence of, the same metallocene catalyst.

To form a catalyst, a cocatalyst, also known as an activator, is used, as is well known in the art. Cocatalysts comprising Al or B are well known and can be used here. The use of aluminoxanes (e.g. MAO) or boron based cocatalysts (such as borates) is preferred. Polyethylene copolymers made using single site catalysis, as opposed to Ziegler Natta catalysis, have characteristic features that allow them to be distinguished from Ziegler Natta materials. In particular, the comonomer distribution is more homogeneous. This can be shown using TREF or Crystaf techniques. Catalyst residues may also indicate the catalyst used. Ziegler Natta catalysts would not contain a Zr or Hf group (IV) metal for example.

The metallocene catalysed multimodal copolymer (P) may contain further polymer components and optionally additives and/or fillers. In case the metallocene catalysed multimodal copolymer (P) contains further polymer components, then the amount of the further polymer component(s) typically varies between 3.0 to 20.0 wt% based on the combined amount of the metallocene catalysed multimodal copolymer (P) and the other polymer component(s).

The optional additives and fillers and the used amounts thereof are conventional in the field of film applications. Examples of such additives are, among others, antioxidants, process stabilizers, UV-stabilizers, pigments, fillers, antistatic additives, antiblock agents, nucleating agents, acid scavengers as well as polymer processing agent (PPA).

It is understood herein that any of the additives and/or fillers can optionally be added in so- called master batch, which comprises the respective additive(s) together with a carrier polymer. In such case the carrier polymer is not calculated to the polymer components of the metallocene catalysed multimodal copolymer (P), but to the amount of the respective additive(s), based on the total amount of polymer composition (100 wt%).

Film of the invention

The film of the invention comprises at least one layer comprising the metallocene catalysed multimodal copolymer (P). The film can be a monolayer film comprising the metallocene catalysed multimodal copolymer (P) or a multilayer film, wherein at least one layer comprises the metallocene catalysed multimodal copolymer (P). The terms “monolayer film” and multilayer film” have well known meanings in the art.

The layer of the monolayer or multilayer film of the invention may consist of the metallocene catalysed multimodal copolymer (P) as such or of a blend of the metallocene catalysed multimodal copolymer (P) together with further polymer(s). In case of blends, any further polymer is different from the metallocene catalysed multimodal copolymer (P) and is preferably a polyolefin. Part of the above mentioned additives, like processing aids, can optionally added to the metallocene catalysed multimodal copolymer (P) during the film preparation process.

Preferably, the at least one layer of the invention comprises at least 50 wt%, more preferably at least 60 wt%, even more preferably at least 70 wt%, yet more preferably at least 80 wt%, of the metallocene catalysed multimodal copolymer (P) of the invention. Most preferably said at least one layer of the film of invention consists of the metallocene catalysed multimodal copolymer (P).

Accordingly, the films of the present invention may comprise a single layer (i.e. monolayer) or may be multilayered. Multilayer films typically, and preferably, comprise at least 3 layers.

The films are preferably produced by any conventional film extrusion procedure known in the art including cast film and blown film extrusion. Most preferably, the film is a blown or cast film, especially a blown film. E.g. the blown film is produced by extrusion through an annular die and blowing into a tubular film by forming a bubble which is collapsed between nip rollers after solidification. This film can then be slit, cut or converted (e.g. gusseted) as desired. Conventional film production techniques may be used in this regard. If the preferable blown or cast film is a multilayer film then the various layers are typically coextruded. The skilled man will be aware of suitable extrusion conditions.

Films according to the present invention may be subjected to post-treatment processes, e.g. surface modifications, lamination or orientation processes or the like. Such orientation processes can be mono-axially (MDO) or bi-axially orientation, wherein mono-axial orientation is preferred.

In another preferred embodiment, the films are unoriented.

The resulting films may have any thickness conventional in the art. The thickness of the film is not critical and depends on the end use. Thus, films may have a thickness of, for example, 300 pm or less, typically 6 to 200 pm, preferably 10 to 180 pm, e.g. 20 to 150 pm or 20 to 120 pm. If desired, the polymer of the invention enables thicknesses of less than 100 pm, e.g. less than 50 pm. Films of the invention with thickness even less than 20 pm can also be produced whilst maintaining good mechanical properties.

Furthermore, the present invention is also directed to the use of the inventive article as packing material, in particular as a packing material for food and/or medical products. The films of the invention are characterized by a sealing initiation temperature determined as described in the experimental part on a blown film with a thickness of 40 pm of below 82°C, preferably in the range of 60°C to 80°C, more preferably in the range of 65°C to 78°C, like 68°C to 78°C.

In an embodiment, the films comprising the metallocene catalysed multimodal copolymer (P) are additionally characterized by a dart-drop impact strength (DDI) determined according to ASTM D1709, method A on a 40 pm monolayer test blown film of at least 1000 g to more than 1700 g, preferably 1200 g to more than 1700 g and more preferably 1500 g to more than 1700 g.

The upper limit of “more than 1700 g” is due to the upper detection limit of 1700 g of the respective method.

Thus, in a preferred embodiment, the films comprising the metallocene catalysed multimodal polyethylene copolymer (P) are characterized by having at least a) a sealing initiation temperature determined as described in the experimental part on a blown film with a thickness of 40 pm of below 82°C, preferably in the range of 60 to 80°C, more preferably in the range of 65°C to 78°C, like 68°C to 78°C, and b) a dart-drop impact strength (DDI) determined according to ASTM D1709, method A on a 40 pm monolayer test blown film of at least 1000 g to more than 1700 g , preferably 1200 g to more than 1700 g and more preferably 1500 g to more than 1700 g.

Films according to the present invention furthermore have good stiffness (tensile modulus measured on a 40 pm monolayer test blown film according to ISO 527-3), i.e. >150MPa (in both directions) and good optics, i.e. haze (measured on a 40 pm monolayer test blown film according to ASTM D 1003-00) of below 25%.

Thus, the films comprising the metallocene catalysed multimodal copolymer (P) may further or in addition have a haze (measured on a 40 pm monolayer test blown film according to ASTM D 1003-00) of below 25 %, preferably between 5 % and 24 %, more preferably between 10 % and 22 % and a tensile modulus (measured on a 40 pm monolayer test blown film according to ISO 527-3) in machine (MD) as well as in transverse (TD) direction in the range of from >150MPa to 300 MPa, preferably of from >150MPa to 250 MPa. The invention will be further described with reference to the following non-limiting examples.

Determination methods

Unless otherwise stated in the description or in the experimental part, the following methods were used for the property determinations of the polymers (including its fractions and components) and/or any sample preparations thereof as specified in the text or experimental part.

Melt Flow Rate

The melt flow rate (MFR) was determined according to ISO 1133 and is indicated in g/10 min. The MFR is an indication of the flowability, and hence the processability, of the polymer. The higher the melt flow rate, the lower the viscosity of the polymer. The MFR is determined at 190 °C for polyethylene. MFR may be determined at different loadings such as 2.16 kg (MFR ₂ ), 5 kg (MFR ₅ ) or 21.6 kg (MFR ₂ I).

Calculation of MFR ₂ of Component B and of Fraction (A-2)

For Component B:

B = MFR ₂ of Component (A)

C = MFR ₂ of Component (B)

A = final MFR ₂ (mixture) of multimodal polyethylene copolymer (P) X = weight fraction of Component (A)

For Fraction (A-2):

B = MFR ₂ of 1 ^st fraction (A-1)

C = MFR ₂ of 2 ^nd fraction (A-2)

A = final MFR ₂ (mixture) of loop polymer (= Component (A))

X = weight fraction of the 1 ^st fraction (A-1) Density

Density of the polymer was measured according to ASTM; D792, Method B (density by balance at 23°C) on compression moulded specimen prepared according to EN ISO 1872- 2 and is given in kg/m ³ .

Comonomer contents:

Quantification of microstructure by NMR spectroscopy

Quantitative nuclear-magnetic resonance (NMR) spectroscopy was used to quantify the comonomer content of the polymers.

Quantitative ¹³ C{ ¹ H} NMR spectra recorded in the molten-state using a Bruker Avance III 500 NMR spectrometer operating at 500.13 and 125.76 MHz for ¹ H and ¹³ C respectively. All spectra were recorded using a ¹³ C optimized 7 mm magic-angle spinning (MAS) probehead at 150°C using nitrogen gas for all pneumatics. Approximately 200 mg of material was packed into a 7 mm outer diameter zirconia MAS rotor and spun at 4 kHz. This setup was chosen primarily for the high sensitivity needed for rapid identification and accurate quantification {klimke06, parkinson07, castignolles09}. Standard single-pulse excitation was employed utilizing the NOE at short recycle delays of 3 s {pollard04, klimke06} and the RS-HEPT decoupling scheme{fillip05,griffin07}. A total of 1024 (1k) transients were acquired per spectra.

Quantitative ¹³ C{ ¹ H} NMR spectra were processed, integrated and relevant quantitative properties determined from the integrals. All chemical shifts are internally referenced to the bulk methylene signal (5+) at 30.00 ppm.

The amount of ethylene was quantified using the integral of the methylene (5+) sites at 30.00 ppm accounting for the number of reporting sites per monomer:

E= 2 the presence of isolated comonomer units is corrected for based on the number of isolated comonomer units present:

Etotal = E + (3*B + 2*H) / 2 where B and H are defined for their respective comonomers. Correction for consecutive and non-consecutive commoner incorporation, when present, is undertaken in a similar way.

Characteristic signals corresponding to the incorporation of 1 -butene were observed and the comonomer fraction calculated as the fraction of 1 -butene in the polymer with respect to all monomer in the polymer: fBtotal = Btotal / (Etotal + Btotal + Htotal)

The amount isolated 1 -butene incorporated in EEBEE sequences was quantified using the integral of the _* B2 sites at 39.8 ppm accounting for the number of reporting sites per comonomer:

B = I„B2

If present the amount consecutively incorporated 1 -butene in EEBBEE sequences was quantified using the integral of the aaB2B2 site at 39.4 ppm accounting for the number of reporting sites per comonomer:

BB = 2 * IaaB2B2

If present the amount non consecutively incorporated 1 -butene in EEBEBEE sequences was quantified using the integral of the bbB2B2 site at 24.6 ppm accounting for the number of reporting sites per comonomer:

BEB = 2 * IbbB2B2

Due to the overlap of the *B2 and *bB2B2 sites of isolated (EEBEE) and non-consecutively incorporated (EEBEBEE) 1 -butene respectively the total amount of isolated 1 -butene incorporation is corrected based on the amount of non-consecutive 1 -butene present:

B = I„B2 - 2 * IbbB2B2

Sequences of BBB were not observed. The total 1 -butene content was calculated based on the sum of isolated, consecutive and non consecutively incorporated 1 -butene:

Btotal = B + BB + BEB

The total mole fraction of 1 -butene in the polymer was then calculated as: fB = Btotal / ( Etotal + Btotal + Htotal)

Characteristic signals corresponding to the incorporation of 1 -hexene were observed and the comonomer fraction calculated as the fraction of 1 -hexene in the polymer with respect to all monomer in the polymer: fHtotal = Htotal / (Etotal + Btotal + Htotal)

The amount isolated 1 -hexene incorporated in EEHEE sequences was quantified using the integral of the _* B4 sites at 38.3 ppm accounting for the number of reporting sites per comonomer:

H = I.B4

If present the amount consecutively incorporated 1 -hexene in EEHHEE sequences was quantified using the integral of the aaB4B4 site at 40.5 ppm accounting for the number of reporting sites per comonomer: HH = 2 * IaaB4B4

If present the amount non consecutively incorporated 1 -hexene in EEHEHEE sequences was quantified using the integral of the bbB4B4 site at 24.7 ppm accounting for the number of reporting sites per comonomer:

HEH = 2 * IbbB4B4

Sequences of HHH were not observed. The total 1 -hexene content was calculated based on the sum of isolated, consecutive and non consecutively incorporated 1 -hexene:

H total = H + HH + HEH

The total mole fraction of 1 -hexene in the polymer was then calculated as: fH = Htotal / ( Etotal + Btotal + Htotal)

The mole percent comonomer incorporation is calculated from the mole fraction:

B [mol%] = 100 * f B H [mol%] = 100 * f H

The weight percent comonomer incorporation is calculated from the mole fraction:

B [wt%] = 100 * ( fB * 56.11) / ( (fB * 56.11) + (fH * 84.16) + ((1-(fB + fH)) * 28.05) )

H [wt%] = 100 * ( fH * 84.16 ) / ( (fB * 56.11) + (fH * 84.16) + ((1-(fB + fH)) * 28.05) ) References:

Klimke, K., Parkinson, M., Piel, C., Kaminsky, W., Spiess, H.W., Wilhelm, M., Macromol. Chem. Phys. 2006;207:382.

Parkinson, M., Klimke, K., Spiess, H.W., Wilhelm, M., Macromol. Chem. Phys. 2007;208:2128.

Pollard, M., Klimke, K., Graf, R., Spiess, H.W., Wilhelm, M., Sperber, O., Piel, C., Kaminsky, W., Macromolecules 2004;37:813.

Filip, X., Tripon, C., Filip, C., J. Mag. Resn. 2005, 176, 239

Griffin, J.M., Tripon, C., Samoson, A., Filip, C., and Brown, S.P., Mag. Res. in Chem. 2007 45, S1 , S198

Castignolles, P., Graf, R., Parkinson, M., Wilhelm, M., Gaborieau, M., Polymer 50 (2009) 2373

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

Zhou, Z., Kuemmerle, R., Qiu, X., Redwine, D., Cong, R., Taha, A., Baugh, D. Winniford, B., J. Mag. Reson. 187 (2007) 225 Busico, V., Carbonniere, P., Cipullo, R., Pellecchia, R., Severn, J., Talarico, G., Macromol. Rapid Commun. 2007, 28, 1128

Resconi, L, Cavallo, L., Fait, A., Piemontesi, F., Chem. Rev. 2000, 100, 1253

Sealing initiation temperature (SIT); sealing end temperature (SET), sealing range:

The method determines the sealing temperature range (sealing range) of polyethylene films, in particular blown films or cast films. The sealing temperature range is the temperature range, in which the films can be sealed according to conditions given below.

The lower limit (heat sealing initiation temperature (SIT)) is the sealing temperature at which a sealing strength of > 5 N is achieved. The upper limit (sealing end temperature (SET)) is reached, when the films stick to the sealing device.

The measurement was done according to the slightly modified ASTM F1921 - 12, where the test parameters sealing pressure, cooling time and test speed have been modified. The determination of the force/temperature curve was continued until thermal failure of the film.

The sealing range was determined on a J&B Universal Sealing Machine Type 4000 with a blown film of 40 pm thickness with the following further parameters:

Conditioning time: > 96 h Specimen width: 25 mm Sealing pressure: 0.4 N/mm ² (PE)

Sealing time: 1 sec

Delay time: 30 sec

Sealing jaws dimension: 50x5 mm

Sealing jaws shape: flat

Sealing jaws coating: Niptef

Sealing temperature: ambient - 240°C

Sealing temperature interval: 5°C

Start temperature: 50°C

Grip separation rate: 42 mm/sec Dart drop strength (DDI)

Dart-drop was measured using ASTM D1709, method A (Alternative Testing Technique) from the films as produced indicated below. A dart with a 38 mm diameter hemispherical head was dropped from a height of 0.66 m onto a multilayer film clamped over a hole. Successive sets of twenty specimens were tested. One weight was used for each set and the weight was increased (or decreased) from set to set by uniform increments. The weight resulting in failure of 50 % of the specimens was calculated and reported.

Film sample preparation The test films consisting of the inventive multimodal copolymer (P) and respective comparative polymers of 40 pm thickness, were prepared using a Collin 30 lab scale mono layer blown film line. The film samples were produced at 194°C, a 1:2.5 blow-up ratio, frostline distance of 120 mm.

Experimental part

Cat.Example: Catalyst preparation for IE1 and IE2 (CAT1)

Loading of Si02:

10 kg of silica (PQ Corporation ES757, calcined 600°C) was added from a feeding drum and inertized in the reactor until O2 level below 2 ppm was reached.

Preparation of MAO/tol/MC:

30 wt% MAO in toluene (14.1 kg) was added into another reactor from a balance followed by toluene (4.0 kg) at 25°C (oil circulation temp) and stirring 95 rpm. Stirring speed was increased 95 rpm -> 200 rpm after toluene addition, stirring time 30 min. Metallocene Rac- dimethylsilanediylbis{2-(5-(trimethylsilyl)furan-2-yl)-4,5-d imethylcyclopentadien-1- yl}zirconium dichloride 477 g was added from a metal cylinder followed by flushing with 4 kg toluene (total toluene amount 8.0 kg). Reactor stirring speed was changed to 95 rpm for MC feeding and returned back to 200 rpm for 3 h reaction time. After reaction time MAO/tol/MC solution was transferred into a feeding vessel.

Preparation of catalyst:

Reactor temperature was set to 10°C (oil circulation temp) and stirring 40 rpm for MAO/tol/MC addition. MAO/tol/MC solution (target 22.5 kg, actual 22.2 kg) was added within 205 min followed by 60 min stirring time (oil circulation temp was set to 25°C). After stirring “dry mixture” was stabilised for 12 h at 25°C (oil circulation temp), stirring 0 rpm. Reactor was turned 20° (back and forth) and stirring was turned on 5 rpm for few rounds once an hour.

After stabilisation the catalyst was dried at 60°C (oil circulation temp) for 2 h under nitrogen flow 2 kg/h, followed by 13 h under vacuum (same nitrogen flow with stirring 5 rpm). Dried catalyst was sampled and HC content was measured in the glove box with Sartorius Moisture Analyser, (Model MA45) using thermogravimetric method. Target HC level was < 2% (actual 1.3 %).

Catalyst for Comparative Examples (CAT2)

As catalyst CAT2 an alumoxane containing, supported catalyst containing metallocene bis(1-methyl-3-n-butylcyclopentadienyl) zirconium (IV) chloride and with enhanced ActivCat® activator technology from Grace was used. Polymerization: Inventive Examples: Inventive multimodal polyethylene copolymer (P) with 1 -butene and 1 -hexene comonomers

Borstar pilot plant with a 3-reactor set-up (loopl - loop2 - GPR 1) and a prepolymerization loop reactor.

The inventive multimodal copolymers (P) of example 1 to example 2 (IE1, IE2) as well as of the comparative examples (CE1 to CE4) were produced by using the polymerization conditions as given in Table 1.

Table 1: Polymerization conditions 26

The polymers were mixed with 2400 ppm of Irganox B561. 270 ppm of Dynamar FX 5922 compounded and extruded under nitrogen atmosphere to pellets by using a JSW extruder so that the SEI was 230 kWh/kg and the melt temperature 250°C.

Table 2: Material properties of inventive multimodal copolymer (P) and comparative copolymers, as well as film parameters

In Figure 1 it is shown that the Inventive Examples fulfil the relation EHE% > -1.1875 * C6 (in wt%) + 110.41 , whereas the Comparative Examples do not. The higher the value for EHE is, the better the comonomer insertion is, which is reflected in more isolated 1 -hexene units.

From the above table it can be clearly seen, that films consisting of the inventive multimodal copolymer (P) show a clearly higher DDI compared to the comparative examples.

Furthermore, such films have an improved overall performance, i.e. comparable sealing initiation temperature (SIT) and good stiffness and good haze, but clearly improved DDI.