EP4688426A1 - Pet-free package with pp-evoh-multilayer structure - Google Patents

Abstract

Multilayer film made of polymeric material comprising polypropylene homopolymers, polypropylene copolymers and EVOH in an amount of at least 96 wt.-%, preferably at least 98 wt.-% with respect to polymeric material, the multilayer film comprising at least 6 layers: base layer (BL) / lamination layer (LL) / tie layer 1 (TL1) / core layer (CL) / tie layer 2 (TL2) / sealing layer (SL), whereby none of the layers contains polyethylene terephthalate (PET).

Description

PET-free Package with PP-EVOH-Multilayer Structure Field of the invention The present invention relates to a multilayer film structure and packages for food packaging, particularly packages for food including a lid and a tray which can be subjected to mechanical recycling. It also relates to mechanically recycled compositions based on these structures and packages. Background The market of foods for large-scale retail via supermarket chains and the like requires sophisticated packaging and packing materials, above all to increase the preservability of these foods and the aesthetic quality of the packages, for example with regard to the transparency of the container. One of the technical requirements of the food retail market is that of having available packages formed by a tray, or container, and by a top film or cover, which offer a suitable barrier to prevent oxygen from entering the tray to preserve the quality of the product contained therein. A known package commonly used on the market, includes a polyethylene terephthalate (PET) carrier (single or three-layer), to which there is applied a three-layer laminated film PE/EVOH/PE. Such package systems are commonly referred to as modified atmosphere packaging systems (MAP). The PET carrier makes recycling nearly impossible in any polyolefin stream, while the barrier film laminate (PE/EVOH/PE) makes recycling difficult and expensive in the PET stream. There was a deep felt need to have a package made from polymers being compatible in a way that simple shredding and re-extrusion of the mixed plastic results in compositions having reasonable mechanical performance. There was also a deep felt need to have a multilayer film having a low water vapor transmission rate and also low oxygen transmission rate as high gas permeability was described in the prior art. US2022081523A1 describes a highly gas permeable film comprising an ethylene-vinyl alcohol copolymer (A), a polyolefin (B) and an acid-modified ethylene alpha olefin copolymer (C), wherein in some embodiments A+B+C of the ethylene-vinyl alcohol copolymer (a) to a total amount of the unmodified polyolefin (B) and the acid modified ethylene alpha olefin copolymer (C) is from 78/22 to 62/38. EP1059163A2 describes a multilayer structure where an A layer made of an ethylene-vinyl alcohol copolymer resin (A) and a C layer made of a polypropylene (C) are laminated via a B layer made of an adhesive resin (B). EP1059163A2 teaches biaxially stretching by a factor of 4 to 10 times larger in the longitudinal direction and 5 to 12 times larger in the transverse direction. Such biaxially oriented polypropylene (BOPP) films are commonly known to have better barrier properties than non-oriented films, but also require complex processing equipment. It has been found that a packaging system for MAP with polymer-wise identical construction in tray and lid can be made by combining polypropylene support layers with a polypropylene based multilayer barrier system and EVOH. The present invention is based on the surprising finding that such a packaging system can be recycled mechanically. Summary of the invention The present invention concerns a multilayer film made of polymeric material comprising polypropylene homopolymers, polypropylene copolymers and EVOH in an amount of at least 96 wt.-%, preferably at least 98 wt.-% with respect to polymeric material, the multilayer film comprising at least 6 layers: base layer (BL) / lamination layer (LL) / tie layer 1 (TL1) / core layer (CL) / tie layer 2 (TL2) / sealing layer (SL), whereby none of the layers contains polyethylene terephthalate (PET); and whereby the base layer (BL) comprises a polypropylene homopolymer and/or a random propylene copolymer; and whereby the lamination layer (LL) comprises a random propylene copolymer; and whereby the tie layer 1 (TL1) comprises a polar modified polypropylene copolymer preferably selected from the group consisting of maleic anhydride grafted polypropylene (PP-g-MAH), maleic anhydride grafted polypropylene co-grafted with styrene (PP-g-MAH- coSt) , or a combination thereof; and whereby the core layer (CL) comprises an ethylene vinyl alcohol copolymer (EVOH); and whereby the tie layer 2 ( TL2) comprises a polar modified polypropylene copolymer preferably selected from the group consisting of maleic anhydride grafted polypropylene (PP-g-MAH), or maleic anhydride grafted polypropylene copolymer co-grafted with styrene (PP-g-MAH-coSt), or a combination thereof; and whereby the sealing layer (SL) comprises a random propylene copolymer, and whereby the multilayer film is not biaxially oriented. The present invention further concerns a package comprising a tray and a lid being made from a multilayer film. The present invention further concerns a material obtainable by mechanical recycling of the multilayer film according to any one of claims 1 to 11 or the package according to claims 12 or 13, preferably having one or more of the following properties: - a melt flow rate of 3.0 to 10 g/10 min (ISO1133; 2.16 kg; 230°C); - a tensile modulus (ISO 527, injection molded test specimen) of 1300 to 2000 MPa; - a strain at break (ISO 527, injection molded test specimen) of at least 400%, preferably at least 500% and most preferably at least 600%. The term film as used herein is equivalent with sheet. According to common understanding, sheet merely denotes a relatively thick film. The inventive multilayer film is not biaxially oriented. A biaxially oriented polypropylene (BOPP) film is film stretched in both machine and transverse directions, producing molecular chain orientation in two directions. Thus, “not biaxially oriented” encompasses merely stretching of the film or sheet in one direction. Visbreaking denotes a process of extruding polypropylene or polypropylene copolymers together with radical initiators, conventionally peroxides, and, generally additives such as stabilizers for shorting of polymer chain length by chemical reaction. Polar modified polypropylene generically denotes polypropylenes modified by grafting of polar groups and/or denotes the incorporation of polar group(s) containing monomers. “Grafted polypropylene” denotes a polypropylene with one or more species connect to the main chain as side-chains. A typical example is maleic anhydride grafted polypropylene (PP-g-MAH) or maleic anhydride grafted polypropylene with co-grafted styrene(PP-g-MAH-coSt). Package denotes a packaging article. Mechanically recycling is defined as shredding and re-extrusion, optionally in the presence of further additives and optionally with further processing steps in the mechanical recycling line. “Recycled” denotes the situation that a material has undergone a first use by a private or industrial consumer and the material is used a second time. The multilayer film as described herein preferably has a water vapor transmission rate (WVTR, ISO 15106-2:2003, measured at 38 °C; 85% relative humidity) of less than 0.30 g/m² , more preferably of less than 0.28 g/m² per day. In a further aspect, the multilayer film as described herein preferably has an oxygen transmission rate (OTR, 23 °C; 100 % O2; 0 % RH; differential pressure method) measured according to ISO 15105-1:2007 of less than 5.0 cm³/m².d.bar, more preferably less than 2.0 cm³/m².d.bar and most preferably less than 1.4 cm³/m².d.bar. The polypropylene homopolymer and/or the random propylene copolymer comprised in the base layer (BL) of the multilayer film has one or more of the following properties: - a melt flow rate, MFR₂, from 1.5 to 15, preferably 2.0 to 12 g/10min (ISO1133; 2.16kg; 230°C); - a melting temperature (DSC, ISO 11357) within the range of 150 to 172°C; preferably in the range of 150 to 158°C; - ethylene being the only comonomer present in case of a copolymer; - less than 0.9 wt.-% of units derived from ethylene, preferably less than 0.5 wt.-% of units derived from ethylene; - a flexural modulus (ISO 178; measured on injection molded specimens, conditioned at 23°C) of at least 1600 MPa, preferably up to 2300 MPa; - a content of 2.1-regio-defects of 0.2 mol-% or more, preferably 0.35 mol-% or more; - is preferably derived from a single site catalyst; - is o a blend of a single site catalyst derived polymer and a Ziegler-Natta derived polymer, o more preferably a blend of a single site catalyst derived polymer and a Ziegler-Natta derived polymer containing a polymeric nucleating agent, o even more preferably a blend obtained by blending 97.0 to 99.0 wt.-% of a single site catalyst derived polymer with 1.0 to 3.0 wt.-% of a Ziegler-Natta derived polymer containing a polymeric nucleating agent, whereby the percentages refer to the total of said blend, o most preferably a blend obtained by blending 97.0 to 99.0 wt.-% of a single site catalyst derived polymer with 1.0 to 3.0 wt.-% of a Ziegler- Natta derived polymer containing polyvinylcyclohexane, whereby the percentages refer to the total of said blend; - a xylene cold soluble fraction (analyzed according to ISO 16152) of less than 0.5 wt.-%; - is comprised in an amount of more than 97.0 wt.-% with respect to the base layer (BL). It is preferred that the polypropylene in the base layer (BL) is a homopolymer. Alternatively, but less preferably random propylene copolymers with very low amounts of ethylene such as less than 0.9 wt.-% or less than 0.5 wt.-% can be used. Such random propylene copolymers are frequently denoted mini-randoms. The preferred melting temperature is from 150 to 172°C; more preferably in the range of 150 to 158°C. Usually, a range of 150 to 158°C can be achieved by use of a single site catalyst. In contrast, a range of 160 to 170°C can be achieved by use of a Ziegler-Natta catalyst. When the polypropylene is made by a single site catalyst under adequate conditions a preferred content of 2.1-regio-defects of 0.2 mol-% or more, and more preferably 0.35 mol- % or more can be obtained, a normal upper limit being 1.0 mol-%. The degree of 2.1-regio- defects may be influenced by the polymerization temperature. The xylene cold soluble fraction (analyzed according to ISO 16152) is preferably less than 0.50 wt.-%; more preferably less than 0.40 wt.-%. All features as described above with respect to the homopolymer and/or the random propylene copolymer shall also hold for blends, particularly the blends of a single site catalyst derived polymer and a Ziegler-Natta derived polymer, as described above. This means the blend comprised in the base layer (BL) of the multilayer film has one or more of the following properties: - the blend is a mixture of a homopolymer and/or a random propylene copolymer - the blend has a melt flow rate, MFR₂, from 1.5 to 15, preferably 2.0 to 12 g/10min (ISO1133; 2.16kg; 230°C); - the blend has a melting temperature (DSC, ISO 11357) within the range of 150 to 172°C; preferably in the range of 150 to 158°C; - ethylene is the only comonomer present in the blend in case of a copolymer; - the blend has less than 0.9 wt.-% of units derived from ethylene, preferably less than 0.2 wt.-% of units derived from ethylene; - the blend has a flexural modulus (ISO 178; measured on injection molded specimens, conditioned at 23°C) of at least 1600 MPa, preferably up to 2300 MPa; - the blend has a content of 2.1-regio-defects of 0.2 mol-% or more, preferably 0.35 mol-% or more; most preferably up to 1.0 mol-%; - the blend is preferably a mixture of a single site catalyst derived polymer and a Ziegler-Natta derived polymer, preferably the blend is a mixture of a single site catalyst derived polymer and a Ziegler-Natta derived polymer containing a polymeric nucleating agent, even more preferably the blend is obtained by blending 97.0 to 99.0 wt.-% of a single site catalyst derived polymer with 1.0 to 3.0 wt.-% of a Ziegler-Natta derived polymer containing a polymeric nucleating agent, whereby the percentages refer to the total of said blend, most preferably the blend is obtained by blending 97.0 to 99.0 wt.-% of a single site catalyst derived polymer with 1.0 to 3.0 wt.-% of a Ziegler-Natta derived polymer containing polyvinylcyclohexane, whereby the percentages refer to the total of said blend; - the blend has a xylene cold soluble fraction (analyzed according to ISO 16152) of less than 0.5 wt.-%; - the blend is comprised in an amount of more than 97.0 wt.-% with respect to the base layer (BL). The random propylene copolymer as comprised in the lamination layer (LL) and/or the sealing layer (SL) has one or more of the following properties: - a melt flow rate, MFR₂, from 5.0 to 15 g/10min (ISO1133; 2.16kg; 190°C); - ethylene being the only comonomer present; - an ethylene content of 1.0 to 6.0 wt.-%, preferably 1.0 to 3.0 wt.-%; - a melting temperature (DSC, ISO 11357) within the range of 122 to 145°C, preferably 123 to 136°C; - a content of 2.1-regio-defects of 0.2 mol-% or more, preferably 0.35 mol-% or more; - is derived from a phthalate free Ziegler Natta catalyst or preferably from a single site catalyst; - a xylene cold soluble fraction (analyzed according to ISO 16152) of less than 1.0 wt.-%, preferably less than 0.8 wt.-%; - a flexural modulus (ISO 178; measured on injection molded specimens, conditioned at 23°C) of at least 600 MPa, preferably at least 800 MPa; - is visbroken; - is comprised in an amount of more than 97.0 wt.-% with respect to the lamination layer (LL), or the sealing layer (SL) respectively. The preferred melting temperature (DSC, ISO 11357) falls within the range of 122 to 145°C, more preferably 123 to 136°C. A melting temperature of 123 to 136°C may be accomplished via use of a single site catalyst. Preferably the content of 2.1-regio-defects is 0.2 mol-% or more, more preferably 0.35 mol-% or more, a normal upper limit being 1.0 mol-%. The use of a single site catalyst introduces 2.1 regio-inversions, whereby the amount thereof can be modified by polymerization temperature variation. In an alternative embodiment, the random propylene copolymer as comprised in the lamination layer (LL) and/or the sealing layer (SL) may be derived from a phthalate free Ziegler Natta catalyst. The xylene cold soluble fraction (analyzed according to ISO 16152) is preferably less than 1.0 wt.-%, more preferably less than 0.8 wt.-%. The flexural modulus (ISO 178; measured on injection molded specimens, conditioned at 23°C) is preferably at least 600 MPa, more preferably at least 800 MPa. The random propylene copolymer as comprised in the lamination layer (LL) and/or the sealing layer (SL) may be visbroken. Visbreaking allows straightforward adaptation of the melt flow rate. The random propylene copolymer is preferably comprised in an amount of more than 97.0 wt.-% with respect to the lamination layer (LL), or the sealing layer (SL) respectively. The multilayer film according to the present invention is preferably characterized by the lamination layer (LL) and the sealing layer (SL) comprising the same random propylene copolymer. The ethylene vinyl alcohol copolymer (EVOH) yielding the core layer (CL) has one or more of the following properties: - a density (ISO 1183) of 1190 to 1230 kg/m³ - a melt flow rate, MFR₂, from 0.5 to 5.0 g/10min (ISO1133; 2.16kg; 190°C) - a melting temperature (DSC; ISO11357) of 175°C or more, preferably up to 190°C. Such ethylene vinyl alcohol copolymers (EVOH) are commercially available for example from Kuraray Co. Ltd. The ethylene vinyl alcohol copolymer (EVOH) based core layer (CL) is encapsulated by two tie layers (TL1, TL2). Those tie layers (TL1, TL2) are preferably made from a maleic anhydride grafted polypropylene (PP-g-MAH) or a maleic anhydride grafted polypropylene co-grafted with styrene (PP-g-MAH-coSt). Styrene co-grafted maleic anhydride grafted polypropylene (PP-g-MAH-coSt) are standard materials and commercially available from the producers in this field of technology. It is preferred that the material of tie layer 1 (TL1) is identical with the material of tie layer 2 (TL2). Preferably, the polar modified polypropylene copolymer comprised in the tie layer 2 (TL2) has one or more of the following properties: - is a maleic anhydride grafted polypropylene (PP-g-MAH), optionally a maleic anhydride grafted polypropylene comprising co-grafted styrene (PP-g-MAH-coSt), - a melt flow rate from 7.0 to 100.0 g/10min (ISO1133; 5kg; 190°C) - a density (ISO 1183) of 870 to 900 kg/m³ - a melting temperature (ASTM D3418) within the range of 135°C to 155°C; - is identical with the material of tie layer 1 (TL1). Preferably, the layer thicknesses of the multilayer film according to the present invention are as follows: - base layer (BL) from 50 to 350 micrometer, more preferably 70 to 300 micrometer; and/or - lamination layer (LL) from 5 to 50 micrometer, more preferably 7 to 35 micrometer; and/or - tie layer 1 (TL1) from 1 to 7 micrometer, more preferable 1 to 4 micrometer; and/or - core layer (CL) from 3 to 15 micrometer; more preferably 4 to 12 micrometer; and/or - tie layer 2 (TL2) from 1 to 7 micrometer; more preferably 1 to 4 micrometer and/or - sealing layer (SL) from 5 to 50 micrometer, more preferably 7 to 35 micrometer. More preferably, the layer thicknesses of the multilayer film according to the present invention are as follows: - base layer (BL) from 70 to 300 micrometer; and - lamination layer (LL) from 7 to 35 micrometer; and - tie layer 1 (TL1) from 1 to 4 micrometer; and - core layer (CL) from 4 to 12 micrometer; and - tie layer 2 (TL2) from 1 to 4 micrometer and - sealing layer (SL) from 7 to 35 micrometer. It is further preferred that the total thickness of the multilayer film is from 70 to 440 micrometer, preferably from 90 to 390 micrometer, like from 100 to 250 micrometer. The inventive multilayer film is preferably obtainable by (a) producing a cast film via extrusion of the base layer polypropylene homopolymer and/or the random propylene copolymer (b) coextruding a barrier cast film including lamination layer, tie layer 1, core layer, tie layer 2 and sealing layer (LL/TL1/CL/TL2/SL); and (c) press-laminating the cast film produced in step a) and the barrier cast film produced in step b) at a temperature within a range of 120 to 130°C. In yet a further aspect, the present invention concerns a package comprising a tray and a lid being made from the multilayer film as disclosed herein. All preferred aspect as to the multilayer film shall also hold for the package. The package according to the present invention includes polypropylene, polypropylene copolymers and EVOH in an amount to at least 96 wt.-%, preferably at least 98 wt.-% with respect to the package. This excludes substantial amounts of other materials such as undesirable PET. In yet a further aspect, the present invention is concerned with a material obtainable by mechanical recycling of the multilayer film as described herein or the package as described herein, preferably having one or more of the following properties: - a melt flow rate of 3.0 to 10 g/10 min (ISO1133; 2.16 kg; 230°C); - a tensile modulus (ISO 527, injection molded test specimen) of 1300 to 2000 MPa; - a strain at break (ISO 527, injection molded test specimen) of at least 400%, preferably at least 500% and most preferably at least 600%. The material according to the present invention preferably has one or more of the following properties: - a melt flow rate of 3.0 to 10 g/10 min (ISO1133; 2.16 kg; 230°C); - a strain at break (ISO 527, injection molded test specimen) of at least 700%. A strain at break (ISO 527, injection molded test specimen) of at least 700% easily can be achieved when the base layer (BL) comprises a polypropylene single site catalyst derived homopolymer and/or a single-site catalyst derived random propylene copolymer. The processes for - preparing the polypropylene homopolymer and/or a random propylene copolymer as comprised in the base layer (BL), and - the random propylene copolymer comprised in the lamination layer (LL) and/or the sealing layer (SL) are described in the following. Polymerization processes which are suitable for producing the random copolymer generally comprise at least two polymerization stages and each stage can be carried out in solution, slurry, fluidized bed, bulk or gas phase. The term “polymerization reactor” shall indicate that the main polymerization takes place. Thus in case the process consists of one or two polymerization reactors, this definition does not exclude the option that the overall system comprises for instance a pre-polymerization step in a pre-polymerization reactor. The term “consist of” is only a closing formulation in view of the main polymerization reactors. The term “sequential polymerization process” indicates that the C₂C₃ random copolymer (A) or the propylene homopolymer is produced in at least two reactors connected in series. Accordingly, such a polymerization system comprises at least a first polymerization reactor (R1) and a second polymerization reactor (R2), and optionally a third polymerization reactor (R3). The first polymerization reactor (R1) is preferably a slurry reactor and can be any continuous or simple stirred batch tank reactor or loop reactor operating in bulk or slurry. Bulk means a polymerization in a reaction medium that comprises of at least 60 % (w/w) monomer. According to the present invention, the slurry reactor is preferably a (bulk) loop reactor. The second polymerization reactor (R2) and the optional third polymerization reactor (R3) are preferably gas phase reactors (GPRs), i.e. a first gas phase reactor (GPR1) and a second gas phase reactor (GPR2). A gas phase reactor (GPR) according to this invention is preferably a fluidized bed reactor, a fast fluidized bed reactor or a settled bed reactor or any combination thereof. A preferred multistage process is a “loop-gas phase”-process, such as developed by Borealis (known as BORSTAR® technology) described e.g. in patent literature, such as in EP 0 887 379, WO 92/12182, WO 2004/000899, WO 2004/111095, WO 99/24478, WO 99/24479 or in WO 00/68315. A further suitable slurry-gas phase process is the Spheripol® process of Basell. Preferably, in the instant process for producing the C₂C₃ random copolymer and/or the propylene homopolymer as defined above the conditions for the first reactor (R-1), i.e. the slurry reactor (SR), like a loop reactor (LR), of step (a) may be as follows: - the temperature is within the range of 40°C to 110°C, preferably between 60°C and 100°C, more preferably between 65 and 95 °C, - the pressure is within the range of 20 bar to 80 bar, preferably between 40 bar to 70 bar, - hydrogen can be added for controlling the molar mass in a manner known per se. Subsequently, the reaction mixture of the first reactor (R-1) is transferred to the second reactor (R-2), i.e. gas phase reactor (GPR-1), where the conditions are preferably as follows: - the temperature is within the range of 50°C to 130°C, preferably between 60°C and 100°C, - the pressure is within the range of 5 bar to 50 bar, preferably between 15 bar to 35 bar, - hydrogen can be added for controlling the molar mass in a manner known per se. Preferably, the random copolymer and/or the propylene homopolymer is produced in the presence of a metallocene catalyst. Thus, the random copolymer and/or the propylene homopolymer is produced by a process comprising the following steps: a) polymerizing in a first reactor propylene and ethylene, obtaining polymer fraction (A-1) of the random copolymer, b) transferring said polymer fraction (A-1) and unreacted comonomers of the first reactor in a second reactor (R-2), c) feeding to said second reactor (R-2) propylene and ethylene, d) polymerizing in said second reactor (R-2) and in the presence of said polymer fraction (A-1) propylene and ethylene obtaining polymer fraction (A-2) said polymer fraction (A-1) and said polymer fraction (A-2) form the random copolymer as used herein. The polymerization takes place in the presence of a metallocene catalyst comprising (a) a complex of formula (I):

M is zirconium or hafnium; each X is a sigma ligand; L is a divalent bridge selected from -R'₂C-, -R'₂C-CR'₂-, -R'₂Si-, -R'₂Si-SiR'₂-, -R'₂Ge-, wherein each R' is independently a hydrogen atom, C₁-C₂₀-hydrocarbyl, tri(C₁-C₂₀-alkyl)silyl, C₆-C₂₀-aryl, C₇-C₂₀-arylalkyl or C₇-C₂₀-alkylaryl; R² and R²' are each independently a C₁-C₂₀ hydrocarbyl radical optionally containing one or more heteroatoms from groups 14-16; R^5' is a C_1-20 hydrocarbyl group containing one or more heteroatoms from groups 14-16 optionally substituted by one or more halo atoms; R⁶ and R^6' are each independently hydrogen or a C_1-20 hydrocarbyl group optionally containing one or more heteroatoms from groups 14-16; wherein R^6´ is preferably a tertiary alkyl group R⁷ is hydrogen or C_1-20 hydrocarbyl group optionally containing one or more heteroatoms from groups 14-16; R⁷´ is hydrogen; Ar is independently an aryl or heteroaryl group having up to 20 carbon atoms optionally substituted by one or more groups R¹; Ar' is independently an aryl or heteroaryl group having up to 20 carbon atoms optionally substituted by one or more groups R¹; each R¹ is a C_1-20 hydrocarbyl group or two R¹ groups on adjacent carbon atoms taken together can form a fused 5 or 6 membered non aromatic ring with the Ar group, said ring being itself optionally substituted with one or more groups R⁴; each R⁴ is a C_1-20 hydrocarbyl group; and (ii) a cocatalyst comprising at least one or two compounds of a group 13 metal, e.g. Al and/or boron compound. The catalyst used in the process of the invention is in solid particulate form. As mentioned above it can be supported on a conventional carrier know to an art skilled person. Preferably, the used catalyst is free from an external carrier. Ideally, the catalyst is obtainable by a process in which (a) a liquid/liquid emulsion system is formed, said liquid/liquid emulsion system comprising a solution of the catalyst components (i) and (ii) dispersed in a solvent so as to form dispersed droplets; and (b) solid particles are formed by solidifying said dispersed droplets. The term C_1-20 hydrocarbyl group includes C_1-20 alkyl, C_2-20 alkenyl, C_2-20 alkynyl, C_3-20 cycloalkyl, C_3-20 cycloalkenyl, C_6-20 aryl groups, C_7-20 alkylaryl groups or C_7-20 arylalkyl groups or of course mixtures of these groups such as cycloalkyl substituted by alkyl. Unless otherwise stated, preferred C_1-20 hydrocarbyl groups are C_1-20 alkyl, C_4-20 cycloalkyl, C_5-20 cycloalkyl-alkyl groups, C_7-20 alkylaryl groups, C_7-20 arylalkyl groups or C_6-20 aryl groups, especially C_1-10 alkyl groups, C_6-10 aryl groups, or C_7-12 arylalkyl groups, e.g. C_1-8 alkyl groups. Most especially preferred hydrocarbyl groups are methyl, ethyl, propyl, isopropyl, tertbutyl, isobutyl, C_5-6-cycloalkyl, cyclohexylmethyl, phenyl or benzyl. The term halo includes fluoro, chloro, bromo and iodo groups, especially chloro groups, when relating to the complex definition. The oxidation state of the metal ion is governed primarily by the nature of the metal ion in question and the stability of the individual oxidation states of each metal ion. It will be appreciated that in the complexes of the invention, the metal ion M is coordinated by ligands X so as to satisfy the valency of the metal ion and to fill its available coordination sites. The nature of these σ-ligands can vary greatly. Such catalysts are described in WO2013/007650, which is incorporated herein by reference. Thus, preferred complexes of use in the invention are of formula (II') or (II)

M is zirconium or hafnium; each X is a sigma ligand, preferably each X is independently a hydrogen atom, a halogen atom, C_1-6 alkoxy group, C_1-6 alkyl, phenyl or benzyl group; L is a divalent bridge selected from -R'₂C-, -R'₂C-CR'₂-, -R'₂Si-, -R'₂Si-SiR'₂-, -R'₂Ge-, wherein each R' is independently a hydrogen atom, C_1-20 alkyl, C_3-10 cycloalkyl, tri(C_1-20- alkyl)silyl, C_6-20-aryl, C_7-20 arylalkyl or C7_-20 alkylaryl; each R² or R²' is a C_1-10 alkyl group; R⁵' is a C_1-10 alkyl group or Z'R³' group; R⁶ is hydrogen or a C_1-10 alkyl group; R⁶' is a C_1-10 alkyl group or C_6-10 aryl group; preferably a tertiary alkyl group; R⁷ is hydrogen, a C_1-6 alkyl group or ZR³ group; R⁷' is hydrogen; Z and Z' are independently O or S; R³' is a C_1-10 alkyl group, or a C_6-10 aryl group optionally substituted by one or more halo groups; R³ is a C_1-10-alkyl group; each n is independently 0 to 4, e.g. 0, 1 or 2; and each R¹ is independently a C_1-20 hydrocarbyl group, e.g. C_1-10 alkyl group. Further preferred complexes of use in the invention are of formula (III') or (III):

M is zirconium or hafnium; each X is a sigma ligand, preferably each X is independently a hydrogen atom, a halogen atom, C_1-6 alkoxy group, C_1-6 alkyl, phenyl or benzyl group; L is a divalent bridge selected from -R'₂C- or -R'₂Si- wherein each R' is independently a hydrogen atom, C_1-20 alkyl or C_3-10 cycloalkyl; R⁶ is hydrogen or a C_1-10 alkyl group; R^6' is a C_1-10 alkyl group or C_6-10 aryl group, preferably a tertiary alkyl group; R⁷ is hydrogen, C_1-6 alkyl or OC_1-6 alkyl; Z' is O or S; R^3' is a C_1-10 alkyl group, or C_6-10 aryl group optionally substituted by one or more halo groups; n is independently 0 to 4, e.g. 0, 1 or 2; and each R¹ is independently a C_1-10 alkyl group. Further preferred complexes of use in the invention are of formula (IV') or (IV):

M is zirconium or hafnium; each X is a sigma ligand, preferably each X is independently a hydrogen atom, a halogen atom, C_1-6-alkoxy group, C_1-6-alkyl, phenyl or benzyl group; each R' is independently a hydrogen atom, C_1-20 alkyl or C_3-7 cycloalkyl; R⁶ is hydrogen or a C_1-10 alkyl group; R^6' is a C_1-10 alkyl group or C_6-10 aryl group, preferably a tertiary alkyl group; R⁷ is hydrogen, C_1-6 alkyl or OC_1-6 alkyl; Z' is O or S; R^3' is a C_1-10 alkyl group, or C_6-10 aryl group optionally substituted by one or more halo groups; n is independently 0, 1 to 2; and each R¹ is independently a C_3-8 alkyl group. Most especially, the complex of use in the invention is of formula (V') or (V):

wherein each X is a sigma ligand, preferably each X is independently a hydrogen atom, a halogen atom, C_1-6-alkoxy group, C_1-6-alkyl, phenyl or benzyl group; R' is independently a C_1-6 alkyl or C_3-10 cycloalkyl; R¹ is independently C_3-8 alkyl; R⁶ is hydrogen or a C_3-8 alkyl group; R^6' is a C_3-8 alkyl group or C_6-10 aryl group, preferably a tertiary C_4-8 alkyl group; R^3' is a C_1-6 alkyl group, or C_6-10 aryl group optionally substituted by one or more halo groups; and n is independently 0, 1 or 2. Particular compounds of the invention include: rac-anti-Me₂Si(2- rac-anti-Me₂Si(2- rac-anti-Me₂Si(2-Me- rac-anti-Me₂Si(2- Me-4-Ph-6-tBu- Me-4-(p-tBuPh)- 4-(3,5-di-tBuPh)-6- Me-4-Ph-6-tBu- Ind)(2-Me-4-Ph-5- Ind)(2-Me-4-Ph-5- tBu-Ind)(2-Me-4-Ph- Ind)(2-Me-4,6-di- OMe-6-tBu- OMe-6-tBu- 5-OMe-6-tBu- Ph-5-OMe- Ind)ZrCl₂ Ind)ZrCl₂ Ind)ZrCl₂ Ind)ZrCl₂ rac-anti- rac-anti- rac-anti-Me₂Si(2- rac-anti-Me₂Si(2- Me₂Si(2-Me-4- Me(CyHex)Si(2- Me-4-(3,5-di- Me-4-(3,5-di- (p-tBuPh)- Me-4-Ph-6-tBu- tBuPh)-7-Me- tBuPh)-7-OMe- Ind)(2-Me-4- Ind)(2-Me-4-Ph- Ind)(2-Me-4-Ph-5- Ind)(2-Me-4-Ph-5- Ph-5-OC₆F₅)-6- 5-OMe-6-tBu- OMe-6-tBu- OMe-6-tBu- iPr-Ind)ZrCl₂ Ind)ZrCl₂ Ind)ZrCl₂ Ind)ZrCl₂ rac-anti- rac-anti- rac-anti-Me₂Si(2- rac-anti-Me₂Si(2- Me₂Si(2-Me-4- Me₂Si(2-Me-4- Me-4-(p-tBuPh)- Me-4-(p-tBuPh)- (p-tBuPh)-6- (p-tBuPh)- Ind)(2-Me-4-(3,5- Ind)(2-Me-4-Ph-5- tBu-Ind)(2-Me- Ind)(2-Me-4-(4- tBu2Ph)-5-OMe- OiBu-6-tBu- 4-Ph-5-OMe-6- tBuPh)-5-OMe- 6-tBu-Ind)ZrCl₂ Ind)ZrCl₂ tBu-Ind)ZrCl₂ 6-tBu-Ind)ZrCl₂ Most preferably rac-anti-Me₂Si(2-Me-4-(p-tBuPh)-Ind)(2-Me-4-Ph-5-OMe-6-tBu-Ind)ZrCl₂ is used. The synthesis of these materials is described in WO2013/007650. To form an active catalytic species it is normally necessary to employ a cocatalyst as is well known in the art. Cocatalysts comprising one or more compounds of Group 13 metals, like organoaluminium compounds or borates or combinations therefrom used to activate metallocene catalysts are suitable for use in this invention. Thus, the cocatalyst is preferably an alumoxane, like MAO. As an alternative borate cocatalysts can also be employed. It is also possible to use a combination of an alumoxane and a borate cocatalyst. As borate cocatalyst, the use of B(C₆F₅)₃, C₆H₅N(CH₃)₂H:B(C₆F₅)₄, (C₆H₅)₃C:B(C₆F₅)₄ or Ni(CN)₄[B(C₆F₅)₃]₄ ^2- is especially preferred. Further suitable cocatalysts are described in WO2013/007650. Suitable amounts of cocatalyst will be well known to the person skilled in the art and are for example disclosed in WO2015/11135. The catalyst used to manufacture the random copolymers and the propylene homopolymer(s) is ideally provided in solid particulate form but unsupported, i.e. no external carrier is used. In order to provide the catalyst of the invention in solid form but without using an external carrier, it is preferred if a liquid-liquid emulsion system is used. The process involves forming dispersing catalyst components (i) and (ii) in a solvent, and solidifying said dispersed droplets to form solid particles. In particular, the method involves preparing a solution of one or more catalyst components; dispersing said solution in an solvent to form an emulsion in which said one or more catalyst components are present in the droplets of the dispersed phase; immobilising the catalyst components in the dispersed droplets, in the absence of an external particulate porous support, to form solid particles comprising the said catalyst, and optionally recovering said particles. This process enables the manufacture of active catalyst particles with improved morphology, e.g. with a predetermined spherical shape and particle size and without using any added external porous support material, such as an inorganic oxide, e.g. silica. Also desirable surface properties can be obtained. WO2013/007650 again contains comprehensive details of this process. The use of the heterogeneous, non-supported catalysts, (i.e. “self-supported” catalysts) might have, as a drawback, a tendency to dissolve to some extent in the polymerization media, i.e. some active catalyst components might leach out of the catalyst particles during slurry polymerization, whereby the original good morphology of the catalyst might be lost. These leached catalyst components are very active possibly causing problems during polymerization. Therefore, the amount of leached components should be minimized, i.e. all catalyst components should be kept in heterogeneous form. Furthermore, the self-supported catalysts generate, due to the high amount of catalytically active species in the catalyst system, high temperatures at the beginning of the polymerization, which may cause melting of the product material. Both effects, i.e. the partial dissolving of the catalyst system and the heat generation, might cause fouling, sheeting and deterioration of the polymer material morphology. In order to minimize the possible problems associated with high activity or leaching, it is preferred to "prepolymerize" the catalyst before using it in polymerization process. It has to be noted that prepolymerization in this regard is part of the catalyst preparation process, being a step carried out after a solid catalyst is formed. This catalyst prepolymerization step is not part of the actual polymerization configuration, which might comprise a conventional process prepolymerization step as well. After the catalyst prepolymerization step, a solid catalyst is obtained and used in polymerization. Catalyst "prepolymerization" takes place following the solidification step of the liquid-liquid emulsion process hereinbefore described. Prepolymerization may take place by known methods described in the art, such as that described in WO 2010/052263, WO 2010/052260 or WO 2010/052264. Preferable embodiments of this aspect of the invention are described herein. As monomers in the catalyst prepolymerization step preferably alpha-olefins are used. Preferable C₂-C₁₀ olefins, such as ethylene, propylene, 1-butene, 1-pentene, 1-hexene, 4- methyl-1-pentene, 1-heptene, 1-octene, 1-nonene 1-decene, styrene and vinylcyclohexene are used. Most preferred alpha-olefins are ethylene and propylene. The catalyst prepolymerization may be carried out in gas phase or in an inert diluent, typically oil or fluorinated hydrocarbon, preferably in fluorinated hydrocarbons or mixture of fluorinated hydrocarbons. Preferably perfluorinated hydrocarbons are used. The melting point of such (per)fluorinated hydrocarbons is typically in the range of 0 to 140°C, preferably 30 to 120°C , like 50 to 110°C. Where the catalyst prepolymerization is done in fluorinated hydrocarbons, the temperature for the prepolymerization step is below 70°C, e.g. in the range of -30 to 70°C, preferably 0- 65°C and more preferably in the range 20 to 55°C. Pressure within the prepolymerization vessel is preferably higher than atmospheric pressure to minimize the eventual leaching of air and/or moisture into the catalyst vessel. Preferably the pressure is in the range of at least 1 to 15 bar, preferably 2 to 10 bar. The prepolymerization vessel is preferably kept in an inert atmosphere, such as under nitrogen or argon or similar atmosphere. Prepolymerization is continued until the prepolymerization degree defined as weight of polymer matrix/weight of solid catalyst before prepolymerization step is reached. The degree is below 25, preferably 0.5 to 10.0, more preferably 1.0 to 8.0, most preferably 2.0 to 6.0. Use of the catalyst prepolymerization step offers the advantage of minimizing leaching of catalyst components and thus local overheating. After prepolymerization, the catalyst can be isolated and stored. The polymers as used herein further comprise one or more additives in a total amount of from 0.1 up to 2.0 wt.-%, based on the resulting stabilized polymer selected from the group consisting of - UV stabilizers - antioxidants - acid scavengers - chloride inhibitor - dispersing agents - slip agents, - anti-block agents, - antistatic agents, and - alpha-nucleating agents. Such additives are commonly known to an art skilled person. Slip agents are also commonly known in the art. Slip agents migrate to the surface and act as lubricants polymer to polymer and polymer against metal rollers, giving reduced coefficient of friction (CoF) as a result. Examples are fatty acid amides, like erucamide (CAS No. 112-84-5), oleamide (CAS No. 301-02-0), stearamide (CAS No. 124-26-5) or combinations thereof. Examples of antioxidants which are commonly used in the art, are sterically hindered phenols (such as CAS No. 6683-19-8, also sold as Irganox 1010 FF™ by BASF), phosphorous based antioxidants (such as CAS No.31570-04-4, also sold as Hostanox PAR 24 (FF)™ by Clariant, or Irgafos 168 (FF)TM by BASF), sulphur based antioxidants (such as CAS No.693- 36-7, sold as Irganox PS-802 FL™ by BASF), nitrogen-based antioxidants (such as 4,4’- bis(1,1’- dimethylbenzyl)diphenylamine), or antioxidant blends. Acid scavengers are also commonly known in the art. Examples are calcium stearates, sodium stearates, zinc stearates, magnesium and zinc oxides, synthetic hydrotalcite (e.g. SHT, CAS No. 11097-59-9), lactates and lactylates, as well as calcium stearate (CAS No. 1592-23-0) and zinc stearate (CAS No. 557-05-1). Particularly preferred is Hycite 713 as commercially available from BASF AG. Common antiblocking agents are natural silica such as diatomaceous earth (such as CAS No.60676-86-0 (SuperfFloss™), CAS No. 60676-86-0 (SuperFloss E™), or CAS No. 60676-86-0 (Celite 499™)), synthetic silica (such as CAS No. 7631-86-9, CAS No. 7631- 86-9, CAS No.7631-86-9, CAS No. 7631-86-9, CAS No. 7631-86-9, CAS No. 7631-86-9, CAS No. 112926- 00-8, CAS No. 7631-86-9, or CAS No. 7631-86-9), silicates (such as aluminium silicate (Kaolin) CAS No. 1318-74-7, sodium aluminum silicate CAS No. 1344- 00-9, calcined kaolin CAS No. 92704-41-1, aluminum silicate CAS No. 1327-36-2, or calcium silicate CAS No. 1344-95-2), synthetic zeolites (such as sodium calcium aluminosilicate hydrate CAS No. 1344- 01-0, CAS No. 1344-01-0, or sodium calcium aluminosilicate, hydrate CAS No. 1344-01-0). Suitable UV-stabilisers are, for example, Bis-(2,2,6,6-tetramethyl-4-piperidyl)-sebacate (CAS No. 52829-07-9, Tinuvin 770); 2-hydroxy-4-n-octoxy-benzophenone (CAS No. 1843- 05-6, Chimassorb 81). Alpha nucleating agents like sodium benzoate (CAS No.532-32-1); a mixture of aluminium- hydroxy-bis[2,2'-methylene-bis(4,6-di-t-butylphenyl)phosphate] and lithium myristate (commercially available as Adekastab NA-21 of Adeka Palmarole, France) or 1,3:2,4- bis(3,4- dimethylbenzylidene)sorbitol (CAS No. 135861-56-2, commercially available as Millad 3988 of Milliken, USA) can also be added. Suitable antistatic agents are, for example, glycerol esters (CAS No. 97593-29-8) or ethoxylated amines (CAS No. 71786-60-2 or 61791-31-9) or ethoxylated amides (CAS No. 204-393-1). Usually these additives are added in quantities of 100-1.000 ppm for each single component. Preferably at least an antioxidant is added. If additional polymeric components are blended, there amount preferably should be less than 2.0 wt.-% with respect to the resulting polymer mixture. When the polypropylene homopolymer or random copolymer is made by a Ziegler Natta catalyst, it is preferably nucleated by polymeric nucleating agent. The propylene homopolymer composition (H-PP) comprises a reactor blend of a propylene homopolymer and a polymeric nucleating agent. The polymeric nucleating agent is present in an amount in the range from 20 to 300 wt- ppm, more preferably 20 to 200 wt-ppm, most preferably 20 to 100 wt-ppm, relative to the total weight of the nucleated polypropylene homopolymer. The polymeric nucleating agent comprises a monomer (I) of the general formula H₂C=CH-CHR¹R² (I) wherein R¹ and R² are either individual alkyl groups with one or more carbon atoms or form an optionally substituted saturated, unsaturated or aromatic ring or a fused ring system containing 4 to 20 carbon atoms, whereby in case R¹ and R² form an aromatic ring, the hydrogen atom of the –CHR¹R² moiety is not present. Preferably, the monomer (I) of the polymeric nucleating agent is selected from the group consisting of vinyl cyclohexane, vinyl cyclopentane and 4-methylpent-1-ene, most preferably the monomer is vinylcyclohexane. Whilst other monomers may be present in the polymeric nucleating agent, most commonly propylene monomers, it is preferred that the polymeric nucleating agent consists of monomers of the general formula (I). In one particularly preferred embodiment, the polymeric nucleating agent is a homopolymer of vinyl cyclohexane (pVCH). Since the nucleated propylene homopolymer is present as a reactor blend of a propylene homopolymer and the polymeric nucleating agent when a Ziegler Natta catalyst is used, all polymer properties that relate to the Ziegler Natta catalyst derived propylene homopolymer have been measured for nucleated propylene homopolymer. The propylene homopolymer and the random propylene copolymer can be produced in the presence of (a) a Ziegler-Natta catalyst (ZN-C) comprising compounds (TC) of a transition metal of Group 4 to 6 of IUPAC, a Group 2 metal compound (MC) and an internal phthalate free donor (ID); (b) optionally a co-catalyst (Co), and (c) optionally an external donor (ED). The propylene homopolymer composition (H-PP) is preferably produced in a sequential polymerization process irrespective of the catalyst nature. The same process layout as described above with respect to the random polypropylene copolymer may be used again irrespective of the catalyst nature. Thus, the propylene homopolymer of the first polymerization reactor (R1), i.e. the first fraction of the final propylene homopolymer, more preferably the polymer slurry of the loop reactor (LR) containing the first fraction of the final propylene homopolymer, is directly fed into the second polymerization reactor (R2), i.e. into the (first) gas phase reactor (GPR1), without a flash step between the stages. This kind of direct feed is described in EP 887379 A, EP 887380 A, EP 887381 A and EP 991684 A. By "direct feed" is meant a process wherein the content of the first polymerization reactor (R1), i.e. of the loop reactor (LR), the polymer slurry comprising the the first fraction of the propylene homopolymer composition (H-PP1) is led directly to the next stage gas phase reactor. Suitable Ziegler Natta catalyst having a phthalate free internal donor are well-known in the art and for example described in WO 2015197435 A1, WO 2015197354 A2 and WO 2015197434 A1. Process for preparing the multilayer film according to the present invention is straightforward and can be accomplished on the basis of common general knowledge applying the following steps: (a) producing a cast film via extrusion of the base layer polypropylene homopolymer and/or the random propylene copolymer (b) coextruding a barrier cast film including lamination layer, tie layer 1, core layer, tie layer 2 and sealing layer (LL/TL1/CL/TL2/SL); and (c) press-laminating the cast film produced in step a) and the barrier cast film produced in step b) at a temperature within a range of 120 to 130°C. Detailed description In the following two particularly preferred embodiments of the multilayer film are described. A first particularly preferred embodiment concerns a multilayer film made of polymeric material comprising polypropylene homopolymers, polypropylene copolymers and EVOH in an amount of at least 96 wt.-%, preferably at least 98 wt.-% with respect to polymeric material, the multilayer film comprising at least 6 layers: base layer (BL) / lamination layer (LL) / tie layer 1 (TL1) / core layer (CL) / tie layer 2 (TL2) / sealing layer (SL), whereby none of the layers contains polyethylene terephthalate (PET); and whereby the base layer (BL) comprises a polypropylene homopolymer; and whereby the lamination layer (LL) comprises a random propylene copolymer; and whereby the tie layer 1 (TL1) comprises a polar modified polypropylene copolymer selected from the group consisting of maleic anhydride grafted polypropylene (PP-g- MAH), maleic anhydride grafted polypropylene co-grafted with styrene (PP-g-MAH-coSt), or a combination thereof; and whereby the core layer (CL) comprises an ethylene vinyl alcohol copolymer (EVOH); and whereby the tie layer 2 ( TL2) comprises a polar modified polypropylene copolymer selected from the group consisting of maleic anhydride grafted polypropylene (PP-g- MAH), maleic anhydride grafted polypropylene co-grafted with styrene (PP-g-MAH-coSt), or a combination thereof; and whereby the sealing layer (SL) comprises a random propylene copolymer; and whereby the multilayer film is not biaxially oriented, wherein the polypropylene homopolymer comprised in the base layer (BL) has one or more of the following properties: - a melt flow rate, MFR₂, from 1.5 to 15, preferably 2.0 to 12 g/10min (ISO1133; 2.16kg; 230°C); - a melting temperature (DSC, ISO 11357) within the range of 150 to 158°C; - a content of 2.1-regio-defects of 0.2 mol-% or more, preferably 0.35 mol-% or more determined by NMR spectroscopy; - is derived from a single site catalyst; - is preferably o a blend of a single site catalyst derived polymer and a Ziegler-Natta derived polymer, o more preferably a blend of a single site catalyst derived polymer and a Ziegler-Natta derived polymer containing a polymeric nucleating agent, o even more preferably a blend obtained by blending 97.0 to 99.0 wt.-% of a single site catalyst derived polymer with 1.0 to 3.0 wt.-% of a Ziegler-Natta derived polymer containing a polymeric nucleating agent, whereby the percentages refer to the total of said blend, o most preferably a blend obtained by blending 97.0 to 99.0 wt.-% of a single site catalyst derived polymer with 1.0 to 3.0 wt.-% of a Ziegler- Natta derived polymer containing polyvinylcyclohexane, whereby the percentages refer to the total of said blend; - a xylene cold soluble fraction (analyzed according to ISO 16152) of less than 0.5 wt.-%; - is comprised in an amount of more than 97.0 wt.-% with respect to the base layer (BL). All preferred aspects as disclosed in the specification and in the claims shall also hold for this particularly preferred embodiment as far as appropriate. A second particularly preferred embodiment concerns a multilayer film made of polymeric material comprising polypropylene homopolymers, polypropylene copolymers and EVOH in an amount of at least 96 wt.-%, preferably at least 98 wt.-% with respect to polymeric material, the multilayer film comprising at least 6 layers: base layer (BL) / lamination layer (LL) / tie layer 1 (TL1) / core layer (CL) / tie layer 2 (TL2) / sealing layer (SL), whereby none of the layers contains polyethylene terephthalate (PET); and whereby the base layer (BL) comprises a polypropylene homopolymer; and whereby the lamination layer (LL) comprises a random propylene copolymer; and whereby the tie layer 1 (TL1) comprises a polar modified polypropylene copolymer selected from the group consisting of maleic anhydride grafted polypropylene (PP-g- MAH), maleic anhydride grafted polypropylene co-grafted with styrene (PP-g-MAH-coSt), or a combination thereof; and whereby the core layer (CL) comprises an ethylene vinyl alcohol copolymer (EVOH); and whereby the tie layer 2 ( TL2) comprises a polar modified polypropylene copolymer selected from the group consisting of maleic anhydride grafted polypropylene (PP-g- MAH), maleic anhydride grafted polypropylene co-grafted with styrene (PP-g-MAH-coSt), or a combination thereof; and whereby the sealing layer (SL) comprises a random propylene copolymer; and whereby the multilayer film is not biaxially oriented, wherein the polypropylene homopolymer comprised in the base layer (BL) has one or more of the following properties: - a melt flow rate, MFR₂, from 1.5 to 15, preferably 2.0 to 12 g/10min (ISO1133; 2.16kg; 230°C); - a melting temperature (DSC, ISO 11357) within the range of 150 to 158°C; - a content of 2.1-regio-defects of 0.2 mol-% or more, preferably 0.35 mol-% or more determined by NMR spectroscopy; - is derived from a single site catalyst; - is preferably o a blend of a single site catalyst derived polymer and a Ziegler-Natta derived polymer, o more preferably a blend of a single site catalyst derived polymer and a Ziegler-Natta derived polymer containing a polymeric nucleating agent, o even more preferably a blend obtained by blending 97.0 to 99.0 wt.-% of a single site catalyst derived polymer with 1.0 to 3.0 wt.-% of a Ziegler-Natta derived polymer containing a polymeric nucleating agent, whereby the percentages refer to the total of said blend, o most preferably a blend obtained by blending 97.0 to 99.0 wt.-% of a single site catalyst derived polymer with 1.0 to 3.0 wt.-% of a Ziegler- Natta derived polymer containing polyvinylcyclohexane, whereby the percentages refer to the total of said blend; - a xylene cold soluble fraction (analyzed according to ISO 16152) of less than 0.5 wt.-%; - is comprised in an amount of more than 97.0 wt.-% with respect to the base layer (BL), and wherein further the random propylene copolymer comprised in the lamination layer (LL) and/or the sealing layer (SL) has one or more of the following properties: - a melting temperature (DSC, ISO 11357) within the range of 123 to 136°C; - a content of 2.1-regio-defects (determined by NMR spectroscopy) of 0.2 mol-% or more, preferably 0.35 mol-% or more, even more preferably from 0.2 mol-% to 1.0 mol-%, most preferably from 0.35 mol-% to 1.0 mol-%; - is derived from a single site catalyst; - a flexural modulus (ISO 178; measured on injection molded specimens, conditioned at 23°C) of at least 800 MPa; - is comprised in an amount of more than 97.0 wt.-% with respect to the lamination layer (LL). All preferred aspects as disclosed in the specification and in the claims shall also hold for this particularly preferred embodiment as far as appropriate. A third particularly preferred embodiment concerns a a material obtainable by mechanical recycling of the multilayer film as described herein or the package as described herein in the general description and the claims, preferably having one or more of the following properties: - a melt flow rate of 3.0 to 10 g/10 min (ISO1133; 2.16 kg; 230°C); - a tensile modulus (ISO 527, injection molded test specimen) of 1300 to 2000 MPa; - a strain at break (ISO 527, injection molded test specimen) of at least 600%. All preferred aspects as disclosed in the specification and in the claims shall also hold for this particularly preferred embodiment as far as appropriate.

Experimental Measurement methods a) MFR₂ (230°C for polypropylene polymers; 190°C for polyethylene polymers) was measured according to ISO 1133 (230°C, 2.16 kg load). b) Quantification of microstructure by NMR spectroscopy Quantitative nuclear-magnetic resonance (NMR) spectroscopy was used to quantify the isotacticity and regio-regularity. Quantitative 13C{1H} NMR spectra were recorded in the solution-state using a Bruker Advance III 400 NMR spectrometer operating at 400.15 and 100.62 MHz for 1H and 13C respectively. All spectra were recorded using a 13C optimised 10 mm extended temperature probe head at 125° C. using nitrogen gas for all pneumatics. For propylene homopolymers approximately 200 mg of material was dissolved in 1,2- tetrachloroethane-d2 (TCE-d2). To ensure a homogenous solution, after initial sample preparation in a heat block, the NMR tube was further heated in a rotatory oven for at least 1 hour. Upon insertion into the magnet, the tube was spun at 10 Hz. This setup was chosen primarily for the high resolution needed for tacticity distribution quantification (Busico, V., Cipullo, R., Prog. Polym. Sci.26 (2001) 443; Busico, V.; Cipullo, R., Monaco, G., Vacatello, M., Segre, A. L., Macromolecules 30 (1997) 6251). Standard single-pulse excitation was employed utilising the NOE and bi-level WALTZ16 decoupling scheme (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, 11289). A total of 8192 (8 k) transients were acquired per spectrum. Quantitative 13C{1H} NMR spectra were processed, integrated and relevant quantitative properties determined from the integrals using proprietary computer programs. For propylene homopolymers all chemical shifts are internally referenced to the methyl isotactic pentad (mmmm) at 21.85 ppm. Characteristic signals corresponding to regio defects (Resconi, L., Cavallo, L., Fait, A., Piemontesi, F., Chem. Rev. 2000, 100, 1253; Wang, W-J., Zhu, S., Macromolecules 33 (2000), 1157; Cheng, H. N., Macromolecules 17 (1984), 1950) or comonomer were observed. The tacticity distribution was quantified through integration of the methyl region between 23.6-19.7 ppm correcting for any sites not related to the stereo sequences of interest (Busico, V., Cipullo, R., Prog. Polym. Sci. 26 (2001) 443; Busico, V., Cipullo, R., Monaco, G., Vacatello, M., Segre, A. L., Macromolecules 30 (1997) 6251). Specifically, the influence of regio-defects and comonomer on the quantification of the tacticity distribution was corrected for by subtraction of representative regio-defects and comonomer integrals from the specific integral regions of the stereo sequences. The isotacticity was determined at the pentad level and reported as the percentage of isotactic pentad (mmmm) sequences with respect to all pentad sequences: [mmmm]%=100*(mmmm/sum of all pentads) The presence of 2,1 erythro regio-defects was indicated by the presence of the two methyl sites at 17.7 and 17.2 ppm and confirmed by other characteristic sites. Characteristic signals corresponding to other types of regio-defects were not observed (Resconi, L., Cavallo, L., Fait, A., Piemontesi, F., Chem. Rev. 2000, 100, 1253). The amount of 2,1 erythro regio-defects was quantified using the average integral of the two characteristic methyl sites at 17.7 and 17.2 ppm: P _21e = (I _e6+I_e8)/2 The amount of 1,2 primary inserted propene was quantified based on the methyl region with correction undertaken for sites included in this region not related to primary insertion and for primary insertion sites excluded from this region: P12=I _CH3 +P _21e The total amount of propene was quantified as the sum of primary inserted propene and all other present regio-defects: P _total =P ₁₂ +P _21e The mole percent of 2,1 erythro regio-defects was quantified with respect to all propene: [21e] mol.-%=100*(P21e/P_total) c) ¹³C NMR Spectroscopy-Based Determination of C2 Content for the Calibration Standards Quantitative ¹³C{¹H} NMR spectra were recorded in the solution-state using a Bruker Avance III 400 NMR spectrometer operating at 400.15 and 100.62 MHz for ¹H and ¹³C respectively. All spectra were recorded using a ¹³C optimised 10 mm extended temperature probe head at 125° C. using nitrogen gas for all pneumatics. Approximately 200 mg of material was dissolved in 3 ml of 1,2-tetrachloroethane-d₂ (TCE-d₂) along with chromium (III) acetylacetonate (Cr(acac)₃) resulting in a 65 mM solution of relaxation agent in solvent (Singh, G., Kothari, A., Gupta, V., Polymer Testing 28 5 (2009), 475). To ensure a homogenous solution, after initial sample preparation in a heat block, the NMR tube was further heated in a rotatory oven for at least 1 hour. Upon insertion into the magnet the tube was spun at 10 Hz. This setup was chosen primarily for the high resolution and quantitatively needed for accurate ethylene content quantification. Standard single-pulse excitation was employed without NOE, using an optimised tip angle, 1 s recycle delay and a bi-level WALTZ16 decoupling scheme (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). A total of 6144 (6 k) transients were acquired per spectra. Quantitative ¹³C{¹H} NMR spectra were processed, integrated and relevant quantitative properties determined from the integrals. All chemical shifts were indirectly referenced to the central methylene group of the ethylene block (EEE) at 30.00 ppm using the chemical shift of the solvent. This approach allowed comparable referencing even when this structural unit was not present. Characteristic signals corresponding to the incorporation of ethylene were observed (Cheng, H. N., Macromolecules 17 (1984), 1950) and the comonomer fraction calculated as the fraction of ethylene in the polymer with respect to all monomer in the polymer: fE=(E/(P+E)) The comonomer fraction was quantified using the method of Wang et. al. (Wang, W-J., Zhu, S., Macromolecules 33 (2000), 1157) through integration of multiple signals across the whole spectral region in the ¹³C{¹H} spectra. This method was chosen for its robust nature and ability to account for the presence of regio-defects when needed. Integral regions were slightly adjusted to increase applicability across the whole range of encountered comonomer contents. For systems with very low ethylene content where only isolated ethylene in PPEPP sequences were observed the method of Wang et. al. was modified reducing the influence of integration of sites that are no longer present. This approach reduced the overestimation of ethylene content for such systems and was achieved by reduction of the number of sites used to determine the absolute ethylene content to E=0.5(Sββ+Sβγ+Sβδ+0.5(Sαβ+Sαγ)) Through the use of this set of sites the corresponding integral equation becomes E=0.5(I _H +I _G+0.5(I _C+I_D)) using the same notation used in the article of Wang et. al. (Wang, W-J., Zhu, S., Macromolecules 33 (2000), 1157). Equations used for absolute propylene content were not modified. The mole percent comonomer incorporation was calculated from the mole fraction: E [mol %]=100*fE. The weight percent comonomer incorporation was calculated from the mole fraction: E [wt %]=100*(fE*28.06)/((fE*28.06)+((1−fE)*42.08)) d) Tensile tests The tensile modulus, the tensile strength and the elongation at break were measured at 23 °C according to ISO 527-2 (cross head speed 1 mm/min for tensile modulus, 50 mm/min for others) using injection moulded specimens moulded at 230 °C according to ISO 527- 2(1B), produced according to EN ISO 1873-2 (dog 10 bone shape, 4 mm thickness). c) Melting temperature Tm and crystallization temperature Tc The melting temperature T_m was determined by differential scanning calorimetry (DSC) according to ISO 11357-3 with a TA-Instruments 2920 Dual-Cell with RSC refrigeration apparatus and data station. A heating and cooling rate of 10 °C/min was applied in a heat/cool/heat cycle between +23 and +210 °C. The crystallization temperature (T_c) was determined from the cooling step, while melting temperature (T_m) and melting enthalpy (H_m) are being determined in the second heating step. c) Xylene Cold Solubles (XCS) The xylene cold soluble (XCS) fraction as defined and described in the present invention was determined in line with ISO 16152 as follows: 2.0 g of the polymer were dissolved in 250 ml p-xylene at 135° C. under agitation. After 30 minutes, the solution was allowed to cool for 15 minutes at ambient temperature and then allowed to settle for 30 minutes at 25+/−0.5° C. The solution was filtered with filter paper into two 100 ml flasks. The solution from the first 100 ml vessel was evaporated in nitrogen flow and the residue dried under vacuum at 90° C until constant weight is reached. The xylene soluble fraction (percent) can then be determined as follows: XS %=(100*m*V0)/(m0*v); m0=initial polymer amount (g); m=weight of residue (g); V0=initial volume (ml); v=volume of analyzed sample (ml). d) Barrier performance (WVTR and OTR) of multilayer films Both water vapor transmission rate - WVTR (38 °C; 85% relative humidity, RH) and oxygen transmission rate - OTR (23 °C; 100 % O2; 0 % RH) were measured on the multilayer films after at least 96 h conditioning time at standard lab conditions (23°C, 30-50% RH). For WVTR, ISO 15106-2:2003 was applied using an infrared sensor for detection. For OTR, ISO 15105-1:2007 with differential pressure method was applied. Examples A multilayer film was prepared from polymers in Table 1, characterized by the parameters given in Table 2. Table 1 – Multilayer film construction and polymers base layer (BL) “Borealis HD905CF” (Ziegler Natta derived, nucleated by polymeric nucleating agent) alternatively “SSC-PPH1” (prepared as described below; single site catalyst derived; MFR2 = 4.6 g/10 min lamination layer (LL) „SSC-PPR2” (prepared as described below; single site catalyst derived, 2.5 wt.-% C2, visbroken to MFR₂=11 g/10min) alternatively Borealis RACO RD208CF (Ziegler Natta derived, 4.5 wt.-% C2, visbroken to MFR 8) tie layer 1 (TL1) DOW Bynel 50E739 (PP-g-MAH, MFR 12) core layer (CL) Kuraray Eval F171B tie layer 2 (TL2) DOW Bynel 50E739 (PP-g-MAH, MFR 12) sealing layer (SL) „SSC-PPR2” (prepared as described below; single site catalyst derived, 2.5 wt.-% C2, visbroken to MFR₂=11 g/10min) alternatively Borealis RACO RD208CF (Ziegler Natta derived, 4.5 wt.-% C2, visbroken to MFR 8) Table 2 – Characteristics of polymers Polymer Type MFR ethylene derived Flexural melting 2.16kg* content from modulus temperature catalyst / nucleation/ visbroken g/10 wt.-% MPa °C min Borealis Polypropylene 6.5 0 Ziegler 2100 168 HD905CF homopolymer Natta nucleated by polyvinylcyc lohexane “SSC- Polypropylene 4.6 0 Single site 1670 154 PPH1” homopolymer catalyst „SSC- Ethylene- 11 2.5 Single site 960 128 PPR2” propylene catalyst, random visbroken copolymer Borealis Ethylene- 8 4.5 Ziegler 650 140 RACO propylene Natta RD208CF random derived, copolymer visbroken DOW Maleic 12 n.d. n.d. n.d. 142 Bynel anhydride (ASTM 50E739 grafted D3418) (PP-g- polypropylene MAH, (PP-g-MAH) MFR 12) density:0.89 g/cm³ Kuraray EVOH 1.6 1190 - 4300 n.d. Eval F171B * 230°C for PP, 190°C for PE & EVOH; n.d. – not defined The two experimental single-site polypropylene grades were produced in a Borstar™ PP pilot plant with sequential reactors, using a liquid bulk prepolymerization reactor, a liquid bulk loop reactor and one of three available gas phase reactors. Polymerization conditions for SSC-PPH1 and SSC-PPR2 are given in Table 3. The catalyst used in the polymerization process for the two experimental single-site polypropylene grades was prepared as follows: The metallocene MC1 (rac-anti-dimethylsilandiyl(2-methyl-4-phenyl-5-methoxy-6-tert-butyl- indenyl)(2-methyl-4-(4-tert-butylphenyl)indenyl)zirconium dichloride) has been synthesized as described in WO 2013/007650. The catalyst was prepared using metallocene MC1 and a catalyst system of MAO and trityl tetrakis(pentafluorophenyl)borate according to Catalyst 3 of WO 2015/11135 with the proviso that the surfactant is 2,3,3,3-tetrafluoro-2-(1,1,2,2,3,3,3-heptafluoropropoxy)-1- propanol. Table 3 – Polymerization data for SSC-PP grades SSC-PPH1 SSC-PPR2 Prepolymerization Temperature °C 20 20 Residence time h 0.4 0.4 Loop reactor Temperature °C 70 65 Feed ratio H2/C2 mol/kmol 0.1 0.1 Feed ratio C2/C3 mol/kmol 0.0 32.1 Split wt.-% 50 52 MFR₂ g/10min 2.5 2.67 C2 content wt.-% 0.0 2.20 First GPR Temperature °C 80 83 Feed ratio H2/C2 mol/kmol 0.9 1.2 Feed ratio C2/C3 mol/kmol 0.0 119.8 Split wt.-% 50 48 Product C2 total wt.-% 0.0 2.5 2,1-regio-defects mol-% 0.6 0.5 MFR₂ g/10min 4.6 1.7 Tm °C 154 128 XCS wt.-% 0.30 0.57 SSC-PPH1 was compounded in a co-rotating twin-screw extruder Coperion ZSK 47 at 220 °C with 2.0 wt.-% of the commercial Borealis HD905CF defined above, 0.05 wt.-% of pentaerythrityl-tetrakis(3-(3’,5’-di-tert. butyl-4-hydroxyphenyl)-propionate (available as Irganox 1010 from BASF AG, Germany; CAS-no. 6683-19-8), 0.05 wt.-% of tris (2,4-di-t- butylphenyl) phosphite (available as Irgafos 168 from BASF AG, Germany; CAS-no.31570- 04-4) and 0.03 wt.-% of synthetic hydrotalcite (available as Hycite 713 from BASF AG, Germany; CAS-no.11097-59-9). SSC-PPR2 was compounded in a co-rotating twin-screw extruder Coperion ZSK 47 at 220 °C with 0.05 wt.-% of pentaerythrityl-tetrakis(3-(3’,5’-di-tert. butyl-4-hydroxyphenyl)- propionate (available as Irganox 1010 from BASF AG, Germany; CAS-no.6683-19-8), 0.05 wt.-% of tris (2,4-di-t-butylphenyl) phosphite (available as Irgafos 168 from BASF AG, Germany; CAS-no. 31570-04-4) and 0.03 wt.-% of synthetic hydrotalcite (available as Hycite 713 from BASF AG, Germany; CAS-no. 11097-59-9), using an appropriate amount of 2,5-bis(tert-butylperoxy)-2,5-dimethylhexane for visbreaking to an MFR₂ of 11.0 g/10 min. The XCS, Tm, C2(total) and content of 2,1-regio-defects were not altered during the visbreaking process. The films for the base layers (BL) from PPA or PPB were produced by monolayer cast film extrusion to the target thickness. The 5-layer barrier films consisting of lamination layer (LL), tie layer 1 (TL1), core layer (CL), tie layer 2 (TL2) and sealing layer (SL) were produced by cast film co-extrusion using a multilayer die. Subsequently, the two films were laminated thermally by compression at 124 °C. Final layer thickness values are given in the following Table 4. The comparative examples were made with pure base layer (CE1) and polyethylene terephthalate (PET) together with polyethylene layers (CE2, CE3, CE4). Table 4 – Multilayer construction and recyclate properties IE1 IE2 IE3 IE4 CE1 CE2 CE3 CE4 Base layer type PPA* PPB** PPA* PPB** PPA* PET PET PET BL thickness µm 100 100 102 100 200 150 200 255 Lamination layer type RC1*** RC1*** RC2**** RC2**** - PE1 PE1 - LL thickness µm 16 17 11 14 0 10 10 0 Tie layer 1 type TL***** TL***** TL***** TL***** - PE2 PE2 - TL1 thickness µm 2 2 2 3 0 5 5 0 Core layer type EVOH****** EVOH****** EVOH****** EVOH****** - EVOH****** - - CL thickness µm 9 12 11 11 0 5 0 0 Tie layer 2 type TL***** TL***** TL***** TL***** - PE2 PE2 - TL2 thickness µm 2 2 2 3 0 5 5 0 Sealing layer type RC1*** RC1*** RC2**** RC2**** - PE3 PE3 - SL thickness µm 21 14 17 18 0 10 10 0 Total thickness µm 150 147 145 149 200 185 230 255 * polypropylene homopolymer Borealis HD905CF (Ziegler Natta catalyst derived, nucleated by polyvinylcyclohexane); ** polypropylene homopolymer SSC-PPH1 in an amount of 98 wt.-% (cf. above, single site catalyst derived) blended with 2.0 wt.-% polypropylene homopolymer Borealis HD905CF (Ziegler Natta catalyst derived, nucleated by polyvinylcyclohexane); *** random polypropylene copolymer SSC-PPR2 (cf. above; single site catalyst derived); **** Borealis RACO RD208CF (Zielger Natta derived; random ethylene propylene copolymer; visbroken, 4.5 wt.-% content of ethylene derived groups, MFR 8 g/10min); ***** DOW Bynel 50E739 (PP-g-MAH, MFR 12 g/10min) ****** Kuraray EVOH EVAL F171B

Multilayer s_tructure ^{IE1 IE2 IE3 IE4 CE1 CE2 CE3 CE4} cm³/ OTR 23°C / 0% rh m².d. 0.99 1.07 0.65 1.19 155 2.16 18.6 21.8 bar WVTR 23°C / 85% g/m². 0.25 0.26 0.26 0.26 0.44 1.23 1.36 1.53 rh d Tensile modulus MPa 2184 2247 2368 2030 2000 1676 2850 3021 Strain at break % 188 473 320 366 9 63 50 72 Fmax (puncture) N 13 14 11 12 10 36 32 45 Mechanically recycled mixture (IM) g/10 MFR PP 220°C 7.2 7.4 6.1 6.2 n.d. - - - min g/10 MFR PET 275°C - - - - n.d. 14.3 20.1 22.5 min Tensile modulus MPa 1558 1385 1651 1495 n.d. 1830 2112 2434 Strain at break % 516 771 485 875 n.d. 23 31 320 All multilayer structures were shredded and re-extruded in a conventional twin-screw extruder at 220°C.

It can be seen that the inventive multilayer structures had outstanding strain at break, excellent OTR and WVTR performance as well as acceptable tensile properties, specifically a higher tensile modulus than the pure PP film of CE1. As can be seen from the comparison of IE3 and IE4, a base layer being made from single- site catalyst derived polypropylene homopolymer resulted in an increase of the strain at break and additionally an increase of Fmax puncture energy. Water vapor transmission rate (WVTR) stayed on the same level whereas oxygen transmission rate (OTR) was somewhat deteriorated. When the lamination layers additionally were made from a single-site catalyst polypropylene homopolymer (as shown in IE2), the strain at break as well as the Fmax puncture energy could be even more improved as can be seen from the comparison of IE4 and IE2. In addition to that, the tensile modulus could be increased. The comparison of IE1 and IE2 further shows the influence (as a separated effect) of the lamination layer being made by a single-site catalyst polypropylene homopolymer. A comparison of the inventive examples with comparative example CE2 allows to understand the influence of using polypropylene versus polyethylene. The use of polypropylene results in a significantly higher stiffness as reflected by the tensile modulus, significantly improved strain at break and further significantly better oxygen transmission rate (OTR) as well as water vapor transmission rate (WVTR). Following mechanical recycling (i.e. shredding and re-extrusion), the inventive examples showed impressive strain at break and particularly an excellent balance of tensile modulus and strain at break rendering the mixed-plastic an attractive material for numerous applications. The mechanically recycled mixtures (IM) of inventive example IE2 and IE4 both being characterized by originating from a sheet containing a base layer being made from single-site catalyst derived polypropylene homopolymer showed surprisingly high strain at break values. The mechanically recycled mixtures (IM) of inventive example IE1 and IE3 both being characterized by originating from a sheet containing a base layer being made from a Ziegler- Natta catalyst derived polypropylene homopolymer showed surprisingly high stiffness.

Claims

Claims 1. A multilayer film made of polymeric material comprising polypropylene homopolymers, polypropylene copolymers and EVOH in an amount of at least 96 wt.-%, preferably at least 98 wt.-% with respect to polymeric material, the multilayer film comprising at least 6 layers: base layer (BL) / lamination layer (LL) / tie layer 1 (TL1) / core layer (CL) / tie layer 2 (TL2) / sealing layer (SL), whereby none of the layers contains polyethylene terephthalate (PET); and whereby the base layer (BL) comprises a polypropylene homopolymer and/or a random propylene copolymer; and whereby the lamination layer (LL) comprises a random propylene copolymer; and whereby the tie layer 1 (TL1) comprises a polar modified polypropylene copolymer preferably selected from the group consisting of maleic anhydride grafted polypropylene (PP-g-MAH), maleic anhydride grafted polypropylene co-grafted with styrene (PP-g-MAH-coSt), or a combination thereof; and whereby the core layer (CL) comprises an ethylene vinyl alcohol copolymer (EVOH); and whereby the tie layer 2 ( TL2) comprises a polar modified polypropylene copolymer preferably selected from the group consisting of maleic anhydride grafted polypropylene (PP-g-MAH), maleic anhydride grafted polypropylene co- grafted with styrene (PP-g-MAH-coSt), or a combination thereof; and whereby the sealing layer (SL) comprises a random propylene copolymer; and whereby the multilayer film is not biaxially oriented.

2. The multilayer film according to claim 1, wherein said multilayer film has a water vapor transmission rate (WVTR, ISO 15106-2:2003, measured at 38 °C; 85% relative humidity) of less than 0.30 g/m² per day, and/or wherein said multilayer film has an oxygen transmission rate (OTR, 23 °C; 100 % O2; 0 % RH; differential pressure method) measured according to ISO 15105- 1:2007 of less than 5.0 cm³/m².d.bar, preferably less than 2.0 cm³/m².d.bar and most preferably less than 1.4 cm³/m².d.bar.

3. The multilayer film according to claim 1 or 2, wherein the polypropylene homopolymer and/or the random propylene copolymer comprised in the base layer (BL) has one or more of the following properties: - a melt flow rate, MFR₂, from 1.5 to 15, preferably 2.0 to 12 g/10min (ISO1133; 2.16kg; 230°C); - a melting temperature (DSC, ISO 11357) within the range of 150 to 172°C; preferably in the range of 150 to 158°C; - ethylene being the only comonomer present in case of a copolymer; - less than 0.9 wt.-% of units derived from ethylene, preferably less than 0.5 wt.- % of units derived from ethylene (determined by NMR spectroscopy); - a flexural modulus (ISO 178; measured on injection molded specimens, conditioned at 23°C) of at least 1600 MPa, preferably up to 2300 MPa; - a content of 2.1-regio-defects of 0.2 mol-% or more, preferably 0.35 mol-% or more determined by NMR spectroscopy; - is derived from a single site catalyst; - is preferably o a blend of a single site catalyst derived polymer and a Ziegler-Natta derived polymer, o more preferably a blend of a single site catalyst derived polymer and a Ziegler-Natta derived polymer containing a polymeric nucleating agent, o even more preferably a blend obtained by blending 97.0 to 99.0 wt.-% of a single site catalyst derived polymer with 1.0 to 3.0 wt.-% of a Ziegler-Natta derived polymer containing a polymeric nucleating agent, whereby the percentages refer to the total of said blend, o most preferably a blend obtained by blending 97.0 to 99.0 wt.-% of a single site catalyst derived polymer with 1.0 to 3.0 wt.-% of a Ziegler- Natta derived polymer containing polyvinylcyclohexane, whereby the percentages refer to the total of said blend; - a xylene cold soluble fraction (analyzed according to ISO 16152) of less than 0.5 wt.-%; - is comprised in an amount of more than 97.0 wt.-% with respect to the base layer (BL).

4. The multilayer film according to claim 1 or claim 2, wherein the random propylene copolymer comprised in the lamination layer (LL) and/or the sealing layer (SL) has one or more of the following properties: - a melt flow rate, MFR₂, from 5.0 to 15 g/10min (ISO1133; 2.16kg; 190°C); - ethylene being the only comonomer present; - an ethylene content (determined by NMR spectroscopy) of 1.0 to 6.0 wt.-%, preferably 1.0 to 3.0 wt.-%; - a melting temperature (DSC, ISO 11357) within the range of 122 to 145°C, preferably 123 to 136°C; - a content of 2.1-regio-defects (determined by NMR spectroscopy) of 0.2 mol-% or more, preferably 0.35 mol-% or more; even more preferably from 0.2 mol-% to 1.0 mol-%, most preferably from 0.35 mol-% to 1.0 mol-%; - is derived from a phthalate free Ziegler Natta catalyst or preferably from a single site catalyst; - a xylene cold soluble fraction (analyzed according to ISO 16152) of less than 1.0 wt.-%, preferably less than 0.8 wt.-%; - a flexural modulus (ISO 178; measured on injection molded specimens, conditioned at 23°C) of at least 600 MPa, preferably at least 800 MPa; - is visbroken; - is comprised in an amount of more than 97.0 wt.-% with respect to the lamination layer (LL) or the sealing layer (SL), respectively. 5. The multilayer film according to any one of the preceding claims wherein the polypropylene homopolymer and/or the random propylene copolymer comprised in the base layer (BL) has one or more of the following properties: - a melting temperature (DSC, ISO 11357) within the range of 150 to 158°C; - less than 0.

5 wt.-% of units derived from ethylene (determined by NMR spectroscopy); - a content of 2.1-regio-defects (determined by NMR spectroscopy) of 0.2 mol-% or more, preferably 0.35 mol-% or more; even more preferably from 0.2 mol-% to 1.0 mol-%, most preferably from 0.35 mol-% to 1.0 mol-%; - is derived from a single site catalyst; - is comprised in an amount of more than 97.0 wt.-% with respect to the base layer (BL); and wherein further the random propylene copolymer comprised in the lamination layer (LL) and/or the sealing layer (SL) has one or more of the following properties: - a melting temperature (DSC, ISO 11357) within the range of 123 to 136°C; - a content of 2.1-regio-defects (determined by NMR spectroscopy) of 0.2 mol-% or more, preferably 0.35 mol-% or more, even more preferably from 0.2 mol-% to 1.0 mol-%, most preferably from 0.35 mol-% to 1.0 mol-%; - is derived from a single site catalyst; - a flexural modulus (ISO 178; measured on injection molded specimens, conditioned at 23°C) of at least 800 MPa; - is comprised in an amount of more than 97.0 wt.-% with respect to the lamination layer (LL).

6. The multilayer film according to any one of the preceding claims wherein the lamination layer (LL) and the sealing layer (SL) comprise the same random propylene copolymer.

7. The multilayer film according to any one of the preceding claims wherein the ethylene vinyl alcohol copolymer (EVOH) yielding the core layer (CL) has one or more of the following properties: - a density (ISO 1183) of 1190 to 1230 kg/m³ - a melt flow rate, MFR₂, from 0.5 to 5.0 g/10min (ISO1133; 2.16kg; 190°C) - a melting temperature (DSC; ISO11357) of 175°C or more, preferably up to 190°C.

8. The multilayer film according to claim 7, whereby the ethylene vinyl alcohol copolymer (EVOH) based core layer (CL) is encapsulated by two tie layers (TL1, TL2) made from maleic anhydride grafted polypropylene (PP-g-MAH) and/or maleic anhydride grafted polypropylene comprising co-grafted styrene (PP-g-MAH- coSt).

9. The multilayer film according to any one of the preceding claims wherein the polar modified polypropylene copolymer comprised in the tie layer 2 (TL2) has one or more of the following properties: - is a maleic anhydride grafted polypropylene (PP-g-MAH), optionally a maleic anhydride grafted polypropylene comprising co-grafted styrene (PP-g-MAH- coSt), - a melt flow rate from 7.0 to 100.0 g/10min (ISO1133; 5kg; 190°C) - a density (ISO 1183) of 870 to 900 kg/m³ - a melting temperature (ASTM D3418) within the range of 135°C to 155°C; - is identical with the material of tie layer 1 (TL1).

10. The multilayer film, whereby the layer thicknesses are as follows: - base layer (BL) from 50 to 350 micrometer, preferably 70 to 300 micrometer; and/or - lamination layer (LL) from 5 to 50 micrometer, preferably 7 to 35 micrometer; and/or - tie layer 1 (TL1) from 1 to 7 micrometer, preferable 1 to 4 micrometer; and/or - core layer (CL) from 3 to 15 micrometer; preferably 4 to 12 micrometer; and/or - tie layer 2 (TL2) from 1 to 7 micrometer; preferably 1 to 4 micrometer and/or - sealing layer (SL) from 5 to 50 micrometer, preferably 7 to 35 micrometer, and whereby optionally the total thickness of the multilayer film is from 70 to 440 micrometer.

11. The multilayer film according to any one of the preceding claims, obtainable by (a) producing a cast film via extrusion of the base layer polypropylene homopolymer and/or the random propylene copolymer (b) coextruding a barrier cast film including lamination layer, tie layer 1, core layer, tie layer 2 and sealing layer (LL/TL1/CL/TL2/SL); and (c) press-laminating the cast film produced in step a) and the barrier cast film produced in step b) at a temperature within a range of 120 to 130°C, and whereby optionally the total thickness of the multilayer film is from 70 to 440 micrometer.

12. A package comprising a tray and a lid being made from a multilayer film of any one of claims 1 to 11.

13. The package according to claim 12, wherein polypropylene, polypropylene copolymers and EVOH amount to at least 96 wt.-%, preferably at least 98 wt.-% with respect to the package.

14. A material obtainable by mechanical recycling of the multilayer film according to any one of claims 1 to 11 or the package according to claims 12 or 13, preferably having one or more of the following properties: - a melt flow rate of 3.0 to 10 g/10 min (ISO1133; 2.16 kg; 230°C); - a tensile modulus (ISO 527, injection molded test specimen) of 1300 to 2000 MPa; - a strain at break (ISO 527, injection molded test specimen) of at least 400%, preferably at least 500% and most preferably at least 600%.

15. The material according to claim 14 having one or more of the following properties: - a melt flow rate of 3.0 to 10 g/10 min (ISO1133; 2.16 kg; 230°C); - a strain at break (ISO 527, injection molded test specimen) of at least 700%.