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

State of the art mLLDPE (metallocene catalysed linear low density polyethylene) is widely used everywhere in daily life, like packaging, due to its excellent cost I performance ratios. One of the famous drawback is the narrow molecular weight distribution and therefore less shear thinning, which leads to the problem in film conversion, e.g. limiting the throughput.

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 reactor is 22 g/10 min. Film properties, like tensile modulus (TM), tear resistance and dart drop impact strength (DDI) are not mentioned at all.

Also WO 2021009192 discloses such a process. The polymer produced in the Examples has a 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 tensile modulus (TM), tear resistance and dart drop impact strength (DDI) are not mentioned at all.

Although a lot of development work has already been done in this field, there is still 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. A common problem in tailoring properties is that very often an improvement of one property leads to a worsening of another property, e.g. by increasing the stiffness, very often the toughness drops down.

Therefore, there is a need in the art for providing a material that provides well-balanced mechanical properties, especially tensile modulus, tear resistance and dart drop (impact strength). In other words, a material is desirable that provides an advantageous combination of tensile modulus, tear resistance and dart drop, to films prepared from such a material.

In addition, such films should further show a well-balanced and continuously improved overall performance.

Such an improvement in the overall performance of a blown film can be expressed by the optomechanical ability (OMA), which is the ratio of mechanical (especially tear resistance (TD) and tensile modulus (TD)) behaviour, to optical performance, namely haze.

It has now been found, that a metallocene-catalysed multimodal polyethylene polymer (P) made with a specific metallocene catalyst and having a specific polymer design has such a desired improved performance.

The films made from such a metallocene-catalysed multimodal polyethylene polymer (P) have in addition an improved balance of properties, especially an improved overall performance.

Description of the invention

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

(i) 35.0 to 50.0 wt% of a polyethylene component (A), and

(ii) 50.0 to 65.0 wt% of a polyethylene component (B), whereby the polyethylene component (A) has a density (ISO 1183) in the range of from 952 to 970 kg/m ³ , a MFR2 (190°C, 2.16 kg, ISO 1133) in the range of from 1.0 to 15.0 g/10 min, a 1 -butene content (determined with ¹³ C{ ¹ H} NMR) in the range of 0.01 to 0.20 mol%, based on the polyethylene component (A) and whereby the polyethylene 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 (ISO 1183) in the range of from 945 to 965 kg/m ³ and a MFR2 (190°C, 2.16 kg, ISO 1133) in the range of from 0.5 to 8.0 g/10 min and the ethylene polymer fraction (A-2) has a density (ISO 1183) in the range of from 950 to 970 kg/m ³ , and an MFR2 and (190°C, 2.16 kg, ISO 1133) the range of 1.0 to 15.0 g/10 min; the polyethylene component (B) has a density (ISO 1183) in the range of from 900 to 940 kg/m ³ , a MFR2 (190°C, 2.16 kg, ISO 1133) in the range of from 0.01 to 2.0 g/10 min a 1 -hexene content (determined with ¹³ C{ ¹ H} NMR) in the range of 0.2 to 5.0 mol% based on the polyethylene compound (B); whereby the multimodal polyethylene polymer (P) has a density (ISO 1183) in the range of from 927 to 950 kg/m ³ , a MFR2 (190°C, 2.16 kg, ISO 1133) in the range of from 0.1 to 3.0 g/10 min, a molecular weight distribution (Mw/Mn) determined with GPC in the range of 4.6 up to 7.0, a ratio of the molecular weight (Mw) of the low crystalline fraction (LOF) to the molecular weight (Mw) of the high crystalline fraction (HOF), Mw(Tp(LCF)/Mw(Tp(HCF), determined as described in the experimental part, in the range of from 0.8 to 4.0.

Unexpectedly the multimodal polyethylene polymer (P) of the invention provides improved mechanical properties to films such as high tensile modulus and/or high drat drop impact strength and at the same time improved tear resistance.

The invention is therefore further directed to a film comprising at least one layer comprising the metallocene-catalysed multimodal polyethylene polymer (P).

In one further embodiment of the present invention, the optomechanical ability (OMA) according to formula n n/T A _

Haze (40 pm) [%] of films determined on 40 pm test blown film is at least 2000 [MPa*g/%] up to 8000 [MPa*g/%], preferably in the range of from 2100 [MPa*g/%] up to 6500 [MPa*g/%], more preferably in the range of from 2200 [MPa*g/%] up to 5500 [MPa*g/%], wherein the Tensile Modulus in transverse direction is measured according to ISO 527-3 at 23°C on 40 pm test blown films, tear resistance in transverse direction determined according to ISO 6383-2 on a 40 pm test blown film and haze is measured according to ASTM D1003 on a 40 pm test blown film. 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 polymer is defined in this invention as multimodal polyethylene polymer (P), which has been produced in the presence of a metallocene catalyst.

Polyethylene polymers which have been produced in the presence of a metallocene catalyst, 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.

For the purpose of the present invention “multimodal polyethylene polymer (P), which comprises polyethylene component (A) and polyethylene component (B)” means that the polymer 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 polymer (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 polymer (P).

Polymers 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.

Term “multimodal” in context of multimodal polyethylene polymer (P) means herein multimodality with respect to melt flow rate (MFR) of the polyethylene components (A) and (B), i.e. the polyethylene components (A) and (B) have different MFR values. The multimodal polyethylene polymer (P) can have further multimodality with respect to one or more further properties between the polyethylene components (A) and (B), as will be described later below.

The multimodal polyethylene polymer (P) of the invention as defined above, below or in claims is also referred herein shortly as “multimodal PE” or “multimodal polymer (P)”.

The following preferable embodiments, properties and subgroups of multimodal PE and the polyethylene 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 polyethylene component (A) and (B) and ethylene polymer fractions (A-1) and (A-2)

The metallocene produced multimodal polyethylene polymer (P) is referred herein as “multimodal”, since the polyethylene component (A), including ethylene polymer fractions (A-1) and (A-2), and polyethylene 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 polyethylene components (A) and (B).

The metallocene produced multimodal polyethylene polymer (P) consists of

(i) 35.0 to 50.0 wt% of a polyethylene component (A), and

(ii) 50.0 to 65.0 wt% of a polyethylene component (B).

The amount of (A) and (B) add up to 100.0 wt%. The polyethylene 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 or may be the same, preferably the MFR2 of the two fractions are different.

The ethylene polymer fraction (A-1) has an MFR2 (190°C, 2.16 kg, ISO 1133) in the range of 0.5 to 8.0 g/10 min, preferably of 0.6 to 7.5 g/10 min, more preferably of 0.8 to 7.0 g/10 min and most preferably 1.0 to 7.0 g/10 min.

The ethylene polymer fraction (A-2) has an MFR2 (190°C, 2.16 kg, ISO 1133) in the range of 1.0 to 15.0 g/10 min, preferably of 1.5 to 12.0 g/10 min, more preferably of 2.0 to 10.0 g/10 min, even more preferably of 2.5 to 9.5 g/10 min, and most preferably 3.0 to 9.0 g/10 min.

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

The ethylene polymer component (A) has an MFR2 (190°C, 2.16 kg, ISO 1133) in the range of 1.0 to 15.0 g/10 min, preferably of 1.5 to 10.0 g/10 min, more preferably of 2.0 to 8.0 g/10 min and even more preferably of 2.5 to 7.0 g/10 min.

The ethylene polymer component (B) has an MFR2 (190°C, 2.16 kg, ISO 1133) in the range of 0.01 to 2.0 g/10 min, preferably of 0.03 to 1.6 g/10 min, more preferably of 0.05 to 1.2 g/10 min and even more preferably of 0.06 to 1 .0 g/10 min, like 0.07 to 0.8 g/10 min.

The MFR2 (190°C, 2.16 kg, ISO 1133) of the multimodal polymer (P) is in the range of 0.1 to 3.0 g/10 min, preferably 0.2 to 2.5 g/10 min and more preferably 0.3 to 2.0 g/10 min.

In an embodiment of the present invention, the multimodal polymer (P) has a MFR21/MFR2 ratio (MFR21 measured at 190°C and 21.6 kg, according to ISO 1133) in the range of 20.0 to 40.0, preferably of 22.0 to 35.0 and more preferably of 24.0 to 32.0.

Naturally, in addition to multimodality with respect to, i.e. difference between, the MFR2 of polyethylene 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) and/or type present in the polyethylene components (A) and (B); and/or the density of the polyethylene components (A) and (B).

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

According to the present invention, the polyethylene component (A) is preferably a polyethylene homopolymer.

In view of the present invention by polyethylene homopolymer a polymer is meant, which comprises at least 99.0 wt%, especially at least 99.5 wt% ethylene monomer units. Thus, the polyethylene homopolymer may comprise up to 1.0 wt% comonomer units, but preferably comprises comonomers only up to 0.5 wt%, like up to 0.2 wt% or even up to 0.1 wt% only.

The comonomer optionally being present in the polyethylene component (A) is 1 -butene.

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)) I (weight fraction of component B)

The total amount of 1 -butene, based on the multimodal polymer (P) is preferably in the range of from 0.01 to 0.10 mol%, preferably 0.02 to 0.08 mol% and more preferably 0.02 to 0.06 mol%. The total amount of 1 -hexene, based on the multimodal polymer (P) preferably is in the range of 0.1 to 3.0 mol%, preferably 0.2 to 2.0 mol% and more preferably 0.3 to 1 .2 mol%.

The total amount (mol%) of 1 -butene, present in the polyethylene component (A) is of 0.01 to 0.20 mol%, preferably of 0.02 to 0.15 mol%, more preferably of 0.03 to 0.10 mol%, based on the polyethylene component (A).

The total amount (mol%) of 1 -hexene, present in the polyethylene component (B) is of 0.2 to 5.0 mol%, preferably of 0.3 to 3.0 mol%, more preferably of 0.4 to 2.0 mol%, based on the polyethylene component (B).

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

The density of the polyethylene component (A) is in the range of 952 to 970 kg/m ³ , preferably of 953 to 968 kg/m ³ , more preferably 955 to 965 kg/m ³ and/or the density of the polyethylene component (B) is of in the range of 900 to 940 kg/m ³ , preferably of 905 to 935 kg/m ³ and more preferably of 910 to 930 kg/m ³ .

The polymer fraction (A-1) has a density in the range of from 945 to 965 kg/m ³ , preferably of 948 to 962 kg/m ³ , more preferably of 950 to 960 kg/m ³ .

The density of the polymer fraction (A-2) is in the range of from 950 to 970 kg/m ³ , preferably of 955 to 965 kg/m ³ .

The density of polymer fraction (A-1) and (A-2) may be the same or may be different from each other.

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

The density of the multimodal polymer (P) is in the range of 927 to 950 kg/m ³ , preferably of 930.0 to 945 kg/m ³ and more preferably of 932.0 to 942.0 kg/m ³ . More preferably the multimodal polymer (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 polyethylene components, (A) and (B), as defined above, below or in the claims including any of the preferable ranges or embodiments of the polymer composition.

The multimodal polymer (P) furthermore has a molecular weight distribution (Mw/Mn) determined with GPC in the range of at least 4.6 up to 7.0, preferably in the range of 4.8 to 6.8 and more preferably in the range of 5.0 to 6.5.

In addition, the multimodal polymer (P) has a ratio of the molecular weight (Mw) of the low crystalline fraction (LCF) to the molecular weight (Mw) of the high crystalline fraction (HCF), Mw(Tp(LCF)/Mw(Tp(HCF), determined as described in the experimental part, in the range of from 0.8 to 4.0, preferably in the range of 0.9 to 3.5 and more preferably of 1.0 to 3.0.

In an embodiment of the present invention, the half peak breadth of the low crystalline fraction (LCF) in a TREF profile with LogM>5.2, determined as described in the experimental part, of the multimodal polymer (P) is in the range of 2.0 to 15.0, preferably 3.0 to 12.0, more preferably 3.5 to 10.0 and even more preferably 4.0 to 9.0.

Definition of High crystalline fraction (HCF) and Low crystalline fraction (LCF):

The high crystalline fraction (HCF) is the amount in wt% of the polymer fraction with a crystallisation temperature higher than 90°C, which mainly contains the homo-polyethylene chains or chains with a very low branching content.

The low crystalline fraction (LCF) is than the amount in wt% of the polymer fraction with a crystallisation temperature between 30 to below 90°C.

It is within the scope of the invention, that the first and the second ethylene polymer fraction (A-1 and A-2) of the polyethylene 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 polyethylene component (A) is present in an amount of 35.0 to 50.0 wt% based on the multimodal copolymer (P), preferably in an amount of 36.0 to 48.0 wt% and even more preferably in an amount of 38.0 to 45.0 wt%. Thus, the polyethylene component (B) is present in an amount of 50.0 to 65.0 wt% based on the multimodal polymer (P), preferably in an amount of 52.0 to 64.0 wt% and more preferably in an amount of 55.0 to 62.0 wt%.

The multimodal polymer (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 polyethylene component (A) leaving the second slurry reactor is fed to the GPR to produce a trimodal polyethylene polymer. 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 how to 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 polymer (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 polymer (P). This can counted as part of the first ethylene polymer component (A).

Catalyst

The metallocene catalysed multimodal polymer (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 (IIIPAC 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, (IIIPAC 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 group, 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- -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)s 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 group, 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)s alkyl group; each p is 1 ; each R is Ci-6-al kyl 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 polyethylene components (A) and (B) of the multimodal polymer (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. The metallocene catalysed multimodal polymer (P) may contain further polymer components and optionally additives and/or fillers. In case the metallocene catalysed multimodal polymer (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 polymer (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 polymer (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 polymer (P). The film can be a monolayer film comprising the metallocene catalysed multimodal polymer (P) or a multilayer film, wherein at least one layer comprises the metallocene catalysed multimodal polymer (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 polymer (P) as such or of a blend of the metallocene catalysed multimodal polymer (P) together with further polymer(s). In case of blends, any further polymer is different from the metallocene catalysed multimodal polymer (P) and is preferably a polyolefin. Part of the above mentioned additives, like processing aids, can optionally added to the metallocene catalysed multimodal polymer (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 polymer (P) of the invention. Most preferably said at least one layer of the film of invention consists of the metallocene catalysed multimodal polymer (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 film as packing material, in particular as a packing material for food and/or medical products. Films according to the present invention have high stiffness (tensile modulus measured on a 40 pm monolayer test blown film according to ISO 527-3), i.e. > 300 MPa (in both directions) and/or dart drop impact strength (measured on a 40 pm monolayer test blown film according to ISO 7765-1 :1988) and good tear resistance (determined according to ISO 6383-2 on a 40 pm monolayer test blown film).

Thus, films according to the present invention have a tensile modulus (measured on a 40 pm monolayer test blown film according to ISO 527-3) in machine and transverse direction in the range of from 350 MPa to 700 MPa, preferably from 400 MPa to 650 MPa and more preferably from 450 to 600 MPa.

The films may furthermore or in addition have a tear resistance (determined according to ISO 6383-2 on a 40 pm monolayer test blown film) in machine direction in the range of from 14 to 50 N/mm, preferably from 15 to 40 N/mm and even more preferably from 15 to 35 N/mm and in transverse direction in the range of from 70 to 200 N/mm, preferably from 80 to 180 N/mm and more preferably from 85 to 150 N/mm.

In an embodiment the films according to the present invention 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 40 %, preferably between 5 % and 35 %, more preferably between 10 % and 30 %.

In one further embodiment of the present invention, the optomechanical ability (OMA) according to formula OMA = -

Haze (40 pm) [%] of films determined on 40 pm test blown film is at least 2000 [MPa*g/%] up to 8000 [MPa*g/%], preferably in the range of from 2100 [MPa*g/%] up to 6500 [MPa*g/%], more preferably in the range of from 2200 [MPa*g/%] up to 5500 [MPa*g/%], wherein the Tensile Modulus in transverse direction is measured according to ISO 527-3 at 23°C on 40 pm test blown films , tear resistance in transverse direction determined according to ISO 6383-2 on a 40 m test blown film and haze is measured according to ASTM D1003 on a 40 pm test blown film.

In view of the present invention, optomechanical abilty (OMA) is understood as the ratio of mechanical (especially tear resistance (TD) and tensile (TD)) behaviour, to optical performance, namely haze, wherein the mechanical properties are targeted to be as high as possible and the optical performance in the sense of haze is desired to be as low as possible.

In a further embodiment the films have a dart-drop impact strength (DDI) determined according to ISO 7765-1 :1988 on a 40 pm monolayer test blown film of 90 g up to 400 g, preferably 100 g up to 300 g and more preferably 110 g up to 200 g.

In another embodiment, the films show improved mechanical performance (higher stiffness and/or higher dart-drop impact strength (DDI)) without deteriorating the sealing performance, which is expressed by the relation between mechanical properties and sealing properties according to formula (III): determined on 40 pm test blown film, wherein the Tensile Modulus (TM) in machine direction is measured according to ISO 527-3 at 23°C on 40 pm test blown films, DDI is the dart-drop impact strength determined according to ISO 7765-1 :1988 on a 40 pm test blown film and SIT is the sealing initiation temperature measured as described in the experimental part on a 40 pm test blown film.

Preferably TM(MD)*DDI/SIT for this embodiment is > 400, and more preferably > 420.

A suitable upper limit for TM(MD)*DDI/SIT for this embodiment is 1000, preferably 800, and more preferably 700.

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 determined at 190 °C for polyethylene. MFR may be determined at different loadings such as 2.16 kg (MFR2), 5 kg (MFR5) or 21.6 kg (MFR21).

Calculation of MFR2 of Component B and of Fraction (A-2)

IOQA = x - logB + {1 — x ) • logC i ogA—x.logB 'f

C = 1QA ( l-.Y j

For Component B:

B = MFR2 of Component (A)

C = MFR2 of Component (B)

A = final MFR2 (mixture) of multimodal polyethylene copolymer (P)

X = weight fraction of Component (A)

For Fraction (A-2):

B = MFR2 of 1st fraction (A-1)

C = MFR2 of 2nd fraction (A-2)

A = final MFR2 (mixture) of loop polymer (=Component (A))

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

Density

Density of the polymer was measured according to ISO 1183 Method A and ISO1872-2 for sample preparation 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 (1 k) 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= I§+ / 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 I (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 ppB2B2 site at 24.6 ppm accounting for the number of reporting sites per comonomer:

BEB = 2 * IPPB2B2

Due to the overlap of the *B2 and *pB2B2 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 * IppB2B2

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 I { 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 I (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 ppB4B4 site at 24.7 ppm accounting for the number of reporting sites per comonomer:

HEH = 2 * IPPB4B4

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:

Htotal = H + HH + HEH

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

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

B [mol%] = 100 * fB

H [mol%] = 100 * fH

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.

Molecular weights, molecular weight distribution, Mn, Mw, MWD:

Molecular weight averages (Mz, Mw and Mn), Molecular weight distribution (MWD) and its broadness, described by polydispersity index, PDI= Mw/Mn (wherein Mn is the number average molecular weight and Mw is the weight average molecular weight) were determined by Gel Permeation Chromatography (GPC) according to ASTM D 6474-12 using the following formulas:

For a constant elution volume interval AVj, where Aj, and Mj are the chromatographic peak slice area and polyolefin molecular weight (MW), respectively associated with the elution volume, Vj, where N is equal to the number of data points obtained from the chromatogram between the integration limits.

A high temperature GPC instrument, equipped with either infrared (IR) detector (IR4 or IR5 from PolymerChar (Valencia, Spain) or differential refractometer (Rl) from Agilent Technologies, equipped with 3 x Agilent-PLgel Olexis and 1x Agilent-PLgel Olexis Guard columns was used. As the solvent and mobile phase 1 ,2,4-trichlorobenzene (TCB) stabilized with 250 mg/L 2,6-Di tert butyl-4-methyl-phenol) was used. The chromatographic system was operated at 160 °C and at a constant flow rate of 1 mL/min. 200 pL of sample solution was injected per analysis. Data collection was performed using either Agilent Cirrus software version 3.3 or PolymerChar GPC-IR control software.

The column set was calibrated using universal calibration with 19 narrow MWD polystyrene (PS) standards in the range of 0,5 kg/mol to 11 500 kg/mol. The PS standards were dissolved at room temperature over several hours. The conversion of the polystyrene peak molecular weight to polyolefin molecular weights is accomplished by using the Mark Houwink equation and the following Mark Houwink constants:

KPS = 19 x 10 ³ mL/g, aps = 0.655

K _PE = 39 x 10 ³ mL/g, ap _E = 0.725

A third order polynomial fit was used to fit the calibration data.

All samples were prepared in the concentration range of 0,5 -1 mg/ml and dissolved at 160 °C for 3 hours for PE under continuous gentle shaking.

Mw(Tp(LCF)/Mw(Tp(HCF) and Half peak breadth (LCF) of TREF profile LogM>5,2

The chemical composition distribution as well as the determination of the molecular weight distribution and the corresponded molecular weight averages (Mn, Mw and Mv) at a certain elution temperature (polymer crystallinity in solution) were determined by a full automated Cross Fractionation Chromatography (CFC) as described by Ortin A., Monrabal B., Sancho-Tello J., Macromol. Symp., 2007, 257, 13-28.

A CFC instrument (PolymerChar, Valencia, Spain) was used to perform the crossfractionation chromatography (TREF x SEC). A four-band IR5 infrared detector (PolymerChar, Valencia, Spain) was used to monitor the concentration. Around 40 mg of the polymer sample was dissolved in 25 ml TCB in the stainless steel vessel for 150 min at 150°C. Once the sample was completely dissolved an aliquot of 0.5 ml was loaded into the TREF column and stabilized for 60 minutes at 110°C. The polymer was crystallized and precipitate to a temperature of 30°C by applying a constant cooling rate of 0.1 °C/min. A discontinuous elution process was performed using the following temperature steps: (30, 40, 45, 50, 53, 56, 59, 62, 64, 66, 69, 72, 76, 79, 82, 85, 89, 91 , 93, 95, 97, 100, 110, and 120).

In the second dimension, the GPC analysis, 3 PL Olexis columns and 1x Olexis Guard columns from Agilent (Church Stretton, UK) were used as stationary phase. As eluent 1 ,2,4- trichlorobenzene (TCB, stabilized with 250 mg/L 2,6-Di tert butyl-4-methyl-phenol) at 150 °C and a constant flow rate of 1 mL/min were applied. The column set was calibrated using universal calibration (according to ISO 16014-2:2003) with at least 15 narrow MWD polystyrene (PS) standards in the range of 0,5 kg/mol to 11 500 kg/mol. Following Mark Houwink constants were used to convert PS molecular weights into the PE molecular weight equivalents.

KPS = 19 x 10 ³ mL/g, aps = 0.655

K _PE = 39 x IO’ ³ mL/g, app = 0.725

A third order polynomial fit was used to fit the calibration data. Data processing was performed using the software provided from PolymerChar with the CFG instrument.

In the first step to obtain better resolved TREF peaks for high crystalline fraction (HCF) and low crystalline fraction (LCF), an a-TREF curve exclusively considering only high molecular weight fraction was created. Therefore the polymer fraction with a molar mass higher than log M of 5.2 (-158 OOOg/mol) were considered to obtain a-TREF curve of the high molecular weight fraction. (a-TREF(HMWF)). This is especially of advantage if the comonomer content in the high crystalline fraction and in the low crystalline fraction are similar, meaning that the temperature difference in the peak position of HCF and LCF are less than 20°C.

From the a-TREF(HMWF) the peak maximum of the HCF peak (Tp(HCF)) and LCF peak were determined (Tp(LCF), where the Tp(HCF) was higher than Tp(LCF) and smaller than 99°C. In figure 2 the a-TREF(HMWF) and the a-TREF profile of CE2 are shown.

In the next step the Mw at the elution temperature of Tp(LCF) and Tp(HCF) were determined. Therefore the Mw at the Tp(LCF) (Mw(Tp(LCF)) was calculated by a linear interpolation between the measured Mw values by GPC of the elution temperatures which was above the Tp(LCF) and below Tp(LCF). This was achieved by using e.g. “TREND” function in Excel.

The same procedure was done to determine the Mw at Tp(HCF).

From the obtained T p(LCF) of the a-TREF (HMWF) curve the half peak breadth was defined as the elution temperature difference between the front temperature and the rear temperature at the half of the maximum peak height of Tp(LCF). The correspondent front temperature was searched forward from 35 °C, while the rear temperature at the half of the maximum was searched backwards from 100°C, if the peaks are not well separated. If the LCF is well separated from HCF then the rear temperature was searched after the HCF. Dart drop strength (DDI)

The DDI was measured according to ISO 7765-1 :1988 I Method A from the films (nonoriented films and laminates) as produced indicated below. This test method covers the determination of the energy that causes films to fail under specified conditions of impact of a free-falling dart from a specified height that would result in failure of 50 % of the specimens tested (Staircase method A). A uniform missile mass increment is employed during the test and the missile weight is decreased or increased by the uniform increment after test of each specimen, depending upon the result (failure or no failure) observed for the specimen.

Standard conditions:

Conditioning time: > 96 h at 50 ±2 °C ±10 %rh

Test temperature: 23 °C

Dart head material: phenolic

Dart diameter: 38 mm

Drop height: 660 mm

Results: Impact failure weight - 50% [g]

Tensile modulus

The tensile test was conducted according to ISO 527-3, moreover the modulus of elasticity (secant modulus between 0.05 % and 0.25 % elongation) is also determined. Type 2 (parallel-sided specimens) specimens were used.

During testing a specimen is extended along its major axis for determination of tensile properties at constant testspeed (speed of crosshead) until the specimen fracture. During this procedure the load sustained by the specimen and the elongation, which is measured by the crosshead, are measured.

Standard conditions:

Conditioning time: > 96 h at 50 ±2 °C ±10 %rh

Test temperature: 23 °C

Gripping distance: 100 mm

Gauge length: 100 mm

Secant modulus: 0,05 % - 0,25 %

Testspeed modulus: 1 mm/min

Testspeed: 200 mm/min Haze

The haze was measured according ASTM D1003 test method (Method A - Hazemeter). The method covers the evaluation of specific light-transmitting and scattering properties of planar sections of materials such as essentially transparent plastic.

A light beam strikes the specimen and enters an integrating sphere. The sphere's interior is coated uniformly with a matte white material to allow diffusion. A detector in the sphere measures total transmittance, haze and clarity (not part of ASTM D1003).

The incident light will be diffusely transmitted changing the appearance quality of the product. This can be a result of scattering at surface structures (roughness) or internal scattering at particles like e.g. air enclosures, poorly disperged pigments, dust enclosures or cristallisation. With increasing roughness haze is increasing and transmittance of plastics is decreasing.

Standard conditions:

Conditioning time: > 96 h

Temperature: 23 °C

Test procedure: A - Hazemeter

Tear resistance (determined as Elmendorf tear (N) in machine (MD) and transverse (TD) direction):

The tear resistance was measured according to the ISO 6383-2 method. The force required to propagate tearing across a film sample was measured using a pendulum device and a constant-radius test specimen was used. The pendulum swings under gravity through an arc, tearing the specimen from pre-cut slit. The specimen was fixed on one side by the pendulum and on the other side by a stationary clamp.

The tear resistance is the force required to tear the specimen. The relative tear resistance (N/mm) was then calculated by dividing the tear resistance by the thickness of the film. 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 monolayer test 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°CGrip separation rate: 42 mm/sec

Film sample preparation

The monolayer test films consisting of the inventive multimodal polymer (P) and respective comparative polymer of 40 pm thickness, were prepared using a Collin 25 benchscale line. Film samples were produced with BUR 2.5:1. Melt temperature 199°C and frost line distance 100 mm, screw speed 126 rpm and take off speed 7.3 m/min. Experimental part

Cat.Example: Catalyst preparation for IE1 (CAT1)

Loading of SiO2:

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- yljzirconium 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 was turned to 40 rpm during MAO/tol/MC addition. MAO/tol/MC solution (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 polymer (P) with 1 -butene and 1 -hexene comonomers

Borstar pilot plant with a 3-reactor set-up (loopl - Ioop2 - GPR 1) and a prepolymerization loop reactor.

The inventive multimodal polymers (P) of example 1 (IE1) and example 2 (IE2) as well as of the comparative example (CE1) were produced by using the polymerization conditions as given in Table 1.

Table 1: Polymerization conditions

The polymers were mixed with 2400 ppm of Irganox B561 (provided by BASF) and 270 ppm of Dynamar FX 5922 (provided by 3M) compounded and extruded under nitrogen atmosphere to pellets by using a twin screw extruder ZSK18; melt temperature 192°C.

Table 2: Material properties of inventive multimodal polymer (P) and comparative copolymer, as well as film parameters *: HCF: High crystalline fraction I LCF: Low crystalline fraction. CFC data.

From the above table it can be clearly seen, that films consisting of the inventive multimodal polymer (P) show a higher tear resistance and Tensile Modulus compared to the comparative example.

Furthermore, such films have an improved overall performance, i.e. higher OMA.

Additionally, the inventive films show the best balance between stiffness, impact and sealing properties.