POLYETHYLENE COMPOSITIONS AND FILMS INCLUDING POLYETHYLENE COMPOSITIONS

Abstract

Polyethylene compositions are described that can have a density of 0.910 g / cm³ to 0.924 g / cm³ and a melt index (I²) of 0.1 g / 10 minutes to 0.5 g / 10 minutes and include an area of ​​a first polyethylene fraction in the temperature range of 45 °C to 80 °C of an elution profile using the enhanced comonomer composition distribution (iCCD) analysis method; an area of ​​the second polyethylene fraction in the temperature range of 80 °C to 95 °C of the elution profile; and an area of ​​the third polyethylene fraction in the temperature range of 95 °C to 110 °C of the elution profile. The area of ​​the second polyethylene fraction can include at least 5% of the total area of ​​the elution profile. The area of ​​the third polyethylene fraction can include at least 25% of the total area of ​​the elution profile. A ratio of the area of ​​the first polyethylene fraction to the area of ​​the second polyethylene fraction can be 6 to 15.

Description

The modalities described in this description generally relate to polyethylene compositions and, more specifically, relate to multilayer films that include polyethylene compositions. BACKGROUND OF THE INVENTION Multilayer films are used in packaging applications, including flexible packaging. It is advantageous that both monolayer and multilayer polymer films, which may include blown or cast films, demonstrate sufficient toughness and puncture resistance while also allowing for material cost reductions, for example, by reducing thickness (i.e., using thinner film thicknesses) or reducing or eliminating relatively expensive materials such as polyamides. SUMMARY OF THE INVENTION Various polymerization techniques using different catalyst systems have been employed to produce polyolefin compositions suitable for packaging applications. However, despite research efforts in developing suitable compositions, Ref. 341646 for packaging applications, there is still a need for suitable compositions that have a good balance of physical properties at desirable polymer composition densities. Furthermore, to achieve this balance, conventional methods may incorporate a polar material, such as polyamide, which can increase process complexity, complicate the film structure, produce non-recyclable multilayer films, and increase material costs compared to using other polyolefins. Therefore, it is beneficial for monolayer and multilayer polymer films, which may include blown or cast films, to demonstrate toughness while simultaneously allowing for reduced material costs and / or increased recyclability. Multilayer films are needed that exhibit stiffness and physical properties, such as puncture resistance, that meet customer and industry requirements. The embodiments described herein satisfy these needs by providing a polyethylene composition that, when used in single-layer or multi-layer films, can provide a balance of improved stiffness and enhanced abrasion resistance properties (e.g., dart, puncture energy, tear). In one or more embodiments, the polyethylene composition may include an area of ​​the first polyethylene fraction, an area of ​​the second polyethylene fraction, and an area of ​​the third polyethylene fraction, where each fraction has an area within the elution profile as described herein. The use of such polyethylene compositions may allow for suitable puncture resistance relative to the modulus. According to one or more of the available methods, a polyethylene composition is provided. The polyethylene composition may include an area of ​​the first polyethylene fraction in the 45°C to 80°C temperature range of an elution profile obtained using the enhanced comonomer composition distribution (iCCD) analysis method; an area of ​​the second polyethylene fraction in the 80°C to 95°C temperature range of the elution profile obtained using the iCCD analysis method; and an area of ​​the third polyethylene fraction in the 95°C to 120°C temperature range of the elution profile obtained using the iCCD analysis method. The area of ​​the second polyethylene fraction may include at least 5% of the total area of ​​the elution profile. The area of ​​the third polyethylene fraction may include at least 25% of the total area of ​​the elution profile.The ratio of the area of ​​the first polyethylene fraction to the area of ​​the second polyethylene fraction can be 6 to 15. The polyethylene composition can have a density of 0.910 g / cm3 to 0.924 g / cm3 and a melt index (I2) of 0.1 g / 10 minutes to 0.5 g / 10 minutes. ML / IZ / ZUZO / U aoz I According to one or more of the embodiments, a polyethylene composition is provided. The polyethylene composition may include an area of ​​the first polyethylene fraction in the temperature range of 45°C to 80°C of an elution profile by the enhanced comonomer composition distribution (iCCD) analysis method; an area of ​​the second polyethylene fraction in the temperature range of 80°C to 95°C of the elution profile by the iCCD analysis method, wherein the area of ​​the second polyethylene fraction comprises at least 5% of the total area of ​​the elution profile; and an area of ​​the third polyethylene fraction in the temperature range of 95°C to 120°C of the elution profile by the iCCD analysis method, wherein the area of ​​the third polyethylene fraction comprises at least 25% of the total area of ​​the elution profile. The polyethylene composition may have a density of 0.910 g / cm³ to 0.924 g / cm3, a melting index (I2) of 0.1 g / 10 minutes to 0.5 g / 10 minutes and a molecular weight distribution, expressed as the ratio of weighted average molecular weight to number average molecular weight (Mw / Mn), in the range of 2.0 to 5.0. A film is provided in accordance with one or more additional modalities. The film may be a single-layer film or a multi-layer film that includes a composition. ML / IZ / ZUZO / UOZ I of polyethylene in at least one layer of the film. The polyethylene composition may include an area of ​​the first polyethylene fraction in the temperature range of 45 °C to 80 °C of an elution profile using the enhanced comonomer composition distribution (iCCD) analysis method; an area of ​​the second polyethylene fraction in the temperature range of 80 °C to 95 °C of the elution profile using the iCCD analysis method; and an area of ​​the third polyethylene fraction in the temperature range of 95 °C to 120 °C of the elution profile using the iCCD analysis method. The area of ​​the second polyethylene fraction may include at least 5% of the total area of ​​the elution profile. The area of ​​the third polyethylene fraction may include at least 25% of the total area of ​​the elution profile.The ratio of the area of ​​the first polyethylene fraction to the area of ​​the second polyethylene fraction can be 6 to 15. The polyethylene composition can have a density of 0.910 g / cm3 to 0.924 g / cm3 and a melt index (I2) of 0.1 g / 10 minutes to 0.5 g / 10 minutes. These and other modalities are described in more detail in the following Detailed Description in conjunction with the accompanying figures. BRIEF DESCRIPTION OF THE FIGURES The following detailed description of specific modalities of the present description can be better understood when read together with the following figures, where a ΜΛ / ΙΖ / ΖυΖΟ / υΊ aoz I similar structure is indicated with similar reference numbers and in which: Figure 1 graphically represents the elution profile of a polyethylene composition, according to one or more of the modes described herein; and Figure 2 schematically represents a reactor system useful for producing polyethylene compositions, according to one or more of the modes described herein. DETAILED DESCRIPTION OF THE INVENTION The following describes specific forms of the present application. These forms are provided to ensure that this description is comprehensive and complete and fully conveys the scope of the claimed subject matter to those skilled in the art. The term polymer refers to a polymeric compound prepared by the polymerization of monomers, whether of the same or different types. The generic term polymer therefore encompasses the term homopolymer, which generally refers to a polymer prepared from only one type of monomer, as well as copolymer, which refers to a polymer prepared from two or more different monomers. The term interpolymer, as used herein, refers to a polymer prepared by the polymerization of at least two different types of monomers. Thus, the generic term interpolymer includes a copolymer or polymer prepared from more than two different types of monomers, such as terpolymers. Polyethylene, or ethylene-based polymer, refers to polymers comprising more than 50% by mole of units derived from an ethylene monomer. This includes ethylene-based copolymers or homopolymers (i.e., units derived from two or more comonomers). Common forms of ethylene-based polymers known in the art include, but are not limited to, low-density polyethylene (LDPE); linear low-density polyethylene (LLDPE); ultra-low-density polyethylene (ULDPE); very low-density polyethylene (VLDPE); single-site catalyzed linear low-density polyethylene, which includes both linear and substantially linear low-density resins (m-LLDPE); medium-density polyethylene (MDPE); and high-density polyethylene (HDPE). The term composition, as used herein, refers to a mixture of materials comprising the composition, as well as reaction products and decomposition products formed from the composition materials. As used herein, polypropylene or polymer ML / IZ / ZUZO / UZ aoz I propylene-based refers to a polymer comprising, in polymerized form, more than 50 mol% of units derived from a propylene monomer. This includes propylene homopolymer, polypropylene random copolymer, impact polypropylene copolymer, propylene / α-olefin copolymer, and propylene / α-olefin copolymer. The term LOPE may also be called high-pressure ethylene polymer or highly branched polyethylene and is defined as the polymer that is homopolymerized or partially or completely copolymerized in autoclaves or tubular reactors at pressures greater than 14,500 psi (100 MPa) with the use of free radical initiators, such as peroxides (see, for example, U.S. Patent No. 4,599,392, which is incorporated herein by reference in its entirety). Typically, LDPE resins have a density in the range of 0.916 g / cm³ to 0.940 g / cm³. The term LLDPE includes resin manufactured using Ziegler-Natta catalyst systems as well as resin manufactured using single-site catalysts, including, but not limited to, bis-metallocene catalysts (sometimes referred to as mLLDPE), phosphinimine, and geometry-restricted catalysts, and resins manufactured using post-metallocene molecular catalysts, including, but ML / IZ / ZUZO / UZ aoz I are not limited to bis(biphenylphenoxy) catalysts (also called polyvalent aryloxy ether catalysts). LLDPE includes linear, substantially linear, or heterogeneous ethylene-based copolymers or homopolymers. LLDPEs contain fewer long-chain branches than LDPEs and include the substantially linear ethylene polymers further defined in U.S. Patent 5,272,236, U.S. Patent 5,278,272, U.S. Patent 5,582,923, and U.S. Patent 5,733,155, each of which is incorporated herein by reference in its entirety; homogeneously branched linear ethylene polymer compositions, such as those in U.S. patent no.3,645,992, which is incorporated herein by reference in its entirety; heterogeneously branched ethylene polymers, such as those prepared according to the process described in U.S. Patent 4,076,698, which is incorporated herein by reference in its entirety; and mixtures thereof (such as those described in U.S. Patents 3,914,342 and 5,854,045, which are incorporated herein by reference in their entirety). LLDPE resins may be manufactured by gas-phase, solution-phase, or slurry-phase polymerization, or any combination thereof, using any type of reactor or reactor configuration known in the art. The term HDPE refers to polyethylenes that have densities greater than 0.935 g / cm3 and up to 0.980 g / cm3, which are generally prepared with Ziegler-Natta catalysts, chromium catalysts or single-site catalysts which include, among others, substituted mono- or biscyclopentadienyl catalysts (typically referred to as metallocene), restricted geometry catalysts, phosphinimine catalysts and polyvalent aryloxy ether catalysts (typically referred to as bisphenyl phenoxy). The term ULDPE refers to polyethylenes with densities of 0.855 g / cm³ to 0.912 g / cm³, generally prepared with Ziegler-Natta catalysts, chromium catalysts, or single-site catalysts, including but not limited to substituted monocyclopentadienyl or biscyclopentadienyl catalysts (typically referred to as metallocene), restricted geometry catalysts, phosphinimine catalysts, and polyvalent aryloxy ether catalysts (typically referred to as bisphenylphenoxy). ULDPEs include, but are not limited to, polyethylene plastomers (ethylene-based) and polyethylene elastomers (ethylene-based). Polyethylene plastomers (ethylene-based) generally have densities of 0.855 g / cm³ to 0.912 g / cm³. Mixture, polymer blend, and similar terms ML / IZ / ZUZO / UZ aoz I signify a composition of two or more polymers. Such a mixture may be miscible or immiscible. Such a mixture may be phase-separated or not. Such a mixture may or may not contain one or more domain configurations, determined from electron transmission spectroscopy, light scattering, X-ray scattering, and any other method known in the art. The mixtures are not laminates, but one or more layers of a laminate may contain a mixture. Such mixtures may be prepared as dry blends, formed in situ (e.g., in a reactor), melt blends, or by the use of other techniques known to those skilled in the art. Multilayer structure or multilayer film means any structure that has more than one layer. For example, a multilayer structure (e.g., a film) can have two, three, four, five, six, seven, or more layers. A multilayer structure can be described with a letter for each layer. For example, a three-layer structure designated as A / B / C can have a middle layer, (B), and two outer layers, (A) and (C). The expressions comprising, including, having, and their derivatives do not exclude the presence of any additional component, step, or process, whether specifically described or not. For the avoidance of doubt, all compositions claimed using the term comprising may include any additive, adjuvant, or IVIA / t / ZUZÓ / UΊ UOZ I additional compound, whether polymeric or otherwise, unless otherwise indicated. Conversely, the term consisting essentially of excludes from the scope of any subsequent recitation any other component, stage, or procedure, except those not essential to operability. The term consisting of excludes any component, stage, or procedure not specifically delineated or enumerated. Multimodal polyethylene composition and characterization As used in this description, the polyethylene compositions described herein may be referred to as multimodal polyethylene compositions. In one or more embodiments, the multimodal polyethylene composition is formed from the polymerization of ethylene and comonomers such as a C3-C12 alkene. The comonomers considered include C6-C9 alkenes, such as 1-octene and 1-hexene. In one or more embodiments, the comonomer is 1-octene. In one or more embodiments, the multimodal polyethylene composition may have a density of 0.910 g / cm³ to 0.924 g / cm³, when measured in accordance with ASTM D7 92. In embodiments, the multimodal polyethylene compositions described herein may have densities of 0.910 g / cm³ to 0.922 g / cm³, 0.910 g / cm³ to 0.920 g / cm³, 0.910 g / cm³ to 0.918 g / cm³, 0.910 g / cm³ to 0.916 g / cm³, 0.910 g / cm³ to 0.914 g / cm³, 0.910 g / cm³ to 0.912 g / cm³, and ML / IZ / ZUZO / U aoz I 0.912 g / cm3 to 0 . 924 g / cm3, from 0.912 g / cm3 to 0.922 g / cm3, from 0.912 g / cm3 to 0 . 920 g / cm3, from 0.912 g / cm3 to 0.918 g / cm3, from 0.912 g / cm3 to 0 . 916 g / cm3, from 0.912 g / cm3 to 0.914 g / cm3, from 0.914 g / cm3 to 0 . 924 g / cm3, from 0.914 g / cm3 to 0.922 g / cm3, from 0.914 g / cm3 to 0 . 920 g / cm3, from 0.914 g / cm3 to 0.918 g / cm3, from 0.914 g / cm3 to 0 . 916 g / cm3, from 0.916 g / cm3 to 0.924 g / cm3, from 0.916 g / cm3 to 0 . 922 g / cm3, from 0.916 g / cm3 to 0.920 g / cm3, from 0.916 g / cm3 to 0 . 918 g / cm3, from 0.918 g / cm3 to 0.924 g / cm3, from 0.918 g / cm3 to 0 . 922 g / cm3, from 0.918 g / cm3 to 0.920 g / cm3, from 0.920 g / cm3 to 0 . 924 g / cm3, from 0.920 g / cm3 to 0.922 g / cm3, from 0.922 g / cm3a 0.924 g / cm3or any combination of these ranges, when measured in accordance with ASTM D792. In one or more modalities, the multimodal polyethylene composition may have a Melt Index (la) of 0.1 g / 10 min (g / 10 min) to 0.5 g / 10 min, when measured in accordance with ASTM D-1238 at 190 °C and 2.16 kg. In the modalities, the multimodal polyethylene composition may have a melt index (I2) of 0.1 g / 10 min to 0.4 g / 10 min, from 0.1 g / 10 min to 0.3 g / 10 min, from 0.1 g / 10 min to 0.2 g / 10 min, from 0.2 g / 10 min to 0.5 g / 10 min, from 0.2 g / 10 min to 0.4 g / 10 min, from 0.2 g / 10 min to 0.3 g / 10 min, from 0.3 g / 10 min to 0.5 g / 10 min, from 0.3 g / 10 min to 0.4 g / 10 min, from 0.4 g / 10 min to 0.5 g / 10 min, or any combination of these ranges when measured according to ASTM D-1238 at 190 °C and 2.16 kg. According to the modalities, multimodal polyethylene compositions can have a molecular weight distribution, expressed as the ratio of weighted average molecular weight to number average molecular weight (Mw / Mn), in the range of 2.0 to 5.0. In various forms, the composition of multimodal polyethylene can have a molecular weight distribution of 2.0 to 4.5, 2.0 to 4.0, 2.0 to 3.5, 2.0 to 3.0, 2.0 to 2.5, 2.5 to 5.0, 2.5 to 4.5, 2.5 to 4.0, 2.5 to 3.5, 2.5 to 3.0, 3.0 to 5.0, 3.0 to 4.5, 3.0 to 4.0, 3.0 to 3.5, 3.5 to 5.0, 3.5 to 4.5, 3.5 to 4.0, 4.0 to 5.0, 4.0 to 4.5, 4.5 to 5.0, or any combination of these ranges. As described herein, the molecular weight distribution can be calculated according to gel permeation chromatography (GPC) techniques as described herein. According to one or more modalities, the composition of multimodal polyethylene can have a zero shear viscosity ratio of 3.0 to 6.0. In various forms, the multimodal polyethylene composition can have a zero shear viscosity ratio of 3.0 to 5.5, 3.0 to 5.0, 3.0 to 4.5, 3.0 to 4.0, 3.0 to 3.5, 3.5 to 6.0, 3.5 to 5.5, 3.5 to 5.0, 3.5 to 4.5, 3.5 to 4.0, 4.0 to 6.0, 4.0 to 5.5, 4.0 to 5.0, 4.0 to 4.5, 4.5 to 6.0, 4.5 to 5.5, 4.5 to 5.0, 5.0 to 6.0, 5.0 to 5.5, 5.5 to 6.0, or any combination of these intervals. According to additional modalities, multimodal polyethylene compositions may have a Dow rheology index less than or equal to 5, such as less than or equal to 4, less than or equal to 3, less than or equal to 2, or even less than or equal to 1. In one or more embodiments, the multimodal polyethylene compositions described herein may further comprise additional components such as one or more additives. Such additives include, but are not limited to, antistatic agents, color enhancers, dyes, lubricants, fillers such as T1O2 or CaCOa, opacifying agents, nucleating agents, processing aids, pigments, primary antioxidants, secondary antioxidants, UV stabilizers, antiblocking agents, slip agents, tackifiers, flame retardants, antimicrobial agents, odor-reducing agents, antifungal agents, and combinations thereof. Multimodal polyethylene compositions may contain from 0.1 to 10 percent by combined weight of such additives, based on the weight of the multimodal polyethylene composition including such additives. As described herein, a polyethylene fraction refers to a portion of the total composition of the multimodal polyethylene composition. The modalities described herein may include at least a first polyethylene fraction, a second polyethylene fraction, and a third polyethylene fraction. The various fractions included in the multimodal polyethylene composition can be quantified by their temperature range in an elution profile using the enhanced comonomer composition distribution (iCCD) analysis method. Unless otherwise specified, any elution profile mentioned herein is the elution profile observed by iCCD. Examples of such fractions will be better understood in light of the accompanying examples.In general, the first fraction may include a peak in the temperature range of the first fraction, the second fraction may include a peak in the temperature range of the second fraction, and the third fraction may include a peak in the temperature range of the third fraction. The multimodal polyethylene compositions described herein may be termed multimodal, meaning that they include at least two peaks in their elution profile. Some modalities may be trimodal, meaning that three main peaks are present. With reference to the described iCCD distribution, Figure 1 schematically represents a sample iCCD 100 distribution along with the cumulative weight fraction 200 curve. Figure 1 generally represents several features of iCCD profiles, including a fraction 102 and a fraction 106. Fraction 102 has a peak at 104, and fraction 106 has a peak at 108. Each fraction has a mean peak width of 110 and 112. It is understood that the profile in Figure 1 is not derived from experimentation or observation but is provided for informational purposes to describe particular features of an iCCD elution profile. In one or more embodiments, the multimodal polyethylene compositions described herein may have a first polyethylene fraction defined by an area in the 45°C to 80°C temperature range of an elution profile obtained using the enhanced comonomer composition distribution (iCCD) analysis method. As used herein, in some embodiments, the area of ​​the first polyethylene fraction may be defined as the area in the elution profile below the single peak of the first polyethylene fraction between 45°C and 80°C. The area of ​​the first polyethylene fraction may correspond to the total relative mass of the polymer fraction in the multimodal polyethylene composition. In some embodiments, the first polyethylene fraction may have a single peak in a temperature range of 45 °C to 80 °C in an iCCD elution profile. As used herein, a single peak refers to an iCCD where a particular fraction includes only a single peak. That is, in some embodiments, the iCCD of the first polyethylene fraction includes only an upward-sloping region followed by a downward-sloping region to form the single peak. In one or more embodiments, the single peak of the first polyethylene fraction may be in a temperature range of 45 °C to 80 °C, such as 40 °C to 75 °C. Not limited to theory, it is believed that at least in some embodiments of the polyethylene composition described herein, where a double reactor design is used for polymerization, a combination of a higher-density crystalline domain and a lower-density amorphous domain may exist.Impact resistance is primarily controlled by the amorphous region or bonding concentrations that connect adjacent sheets. The relative bonding concentration is estimated to be relatively high when the density is less than 0.910 g / cm³. The peak of the first polymer fraction in the compositions described herein can be found in the temperature range of 45 °C to 80 °C, which may provide a higher bonding concentration for functional benefits such as improved toughness. It must be understood that a peak in the first polyethylene fraction may not be formed by a local minimum in the respective polyethylene fraction at a defined temperature limit. That is, the peak must be a peak within the context of the entire spectrum, not a peak formed by the threshold temperature. ML / IZ / ZUZO / UZ aoz I of a polyethylene fraction. For example, if a single peak followed by a single valley were present in a polyethylene fraction (an upward slope followed by a downward slope followed by an upward slope), only a single peak would be present in the polyethylene fraction. In one or more modalities, the area of ​​the first polyethylene fraction may comprise at least 40% of the total area of ​​the elution profile (e.g., at least 42%, at least 44%, at least 46%, at least 48%, at least 50%, at least 52%, or even at least 54% of the total area of ​​the elution profile). For example, the area of ​​the first polyethylene fraction may comprise from 40% to 65% of the total elution profile area, such as from 40% to 60%, from 40% to 55%, from 40% to 50%, from 40% to 45%, from 45% to 65%, from 45% to 60%, from 45% to 55%, from 45% to 50%, from 50% to 65%, from 50% to 60%, from 50% to 55%, from 55% to 65%, from 55% to 60%, from 60% to 65% of the total elution profile area. In one or more embodiments, the weight average molecular weight of the first polyethylene fraction may be less than or equal to 250,000 g / mol, such as from 20,000 g / mol to 250,000 g / mol or from 20,000 g / mol to 200,000 g / mol. In embodiments, the weight average molecular weight of the first polyethylene fraction may be from 20,000 g / mol to 250,000 g / mol, from 20,000 g / mol to 200,000 g / mol, from 20,000 g / mol to 150,000 g / mol, from 20,000 g / mol to 100,000 g / mol, from 20,000 g / mol to 50,000 g / mol, from 50,000 g / mol to 250,000 g / mol, from 50,000 g / mol to 200,000 g / mol, from 50,000 g / mol to 150,000 g / mol, from 50,000 g / mol to 100,000 g / mol, from 100,000 g / mol to 250,000 g / mol, from 100,000 g / mol to 200,000 g / mol, from 100,000 g / mol to 150,000 g / mol, of 150,000 g / mol to 250,000 g / mol, 150,000 g / mol to 200,000 g / mol, 200,000 g / mol to 250,000 g / mol, or any combination of these ranges. The molecular weight of the polyethylene fractions can be calculated based on the GPC results, as described later in this document. In one or more embodiments, the multimodal polyethylene composition may have a second polyethylene fraction defined by an area in the 80°C to 95°C temperature range of an elution profile obtained using the enhanced comonomer composition distribution (iCCD) analysis method. As used herein, in some embodiments, the area of ​​the second polyethylene fraction can be defined as the area in the elution profile below a single peak of the second polyethylene fraction between 80°C and 95°C. Not limited to theory, it is believed that the comonomer distribution in the second polyethylene fraction may contribute to improved properties when the multimodal polyethylene composition is extruded into a film. For example, ML / IZ / ZUZO / UZ yoz I such improved properties may include improved puncture resistance. The second polyethylene area fraction may correspond to the total relative mass of the polymer fraction in the multimodal polyethylene composition. In one or more modes, the second polyethylene fraction may include a local minimum in an elution profile. This local minimum may be located between the peak of the first polyethylene fraction and a peak in the third polyethylene fraction. According to one or more of the modalities, the area of ​​the second polyethylene fraction may comprise at least 5% of the total area of ​​the elution profile (e.g., at least 6%, at least 8%, or even at least 10% of the total area of ​​the elution profile). For example, the area of ​​the first polyethylene fraction may comprise from 5% to 15%, from 5% to 10%, or from 10% to 15% of the total area of ​​the elution profile. According to some modalities, a ratio of the area of ​​the first polyethylene fraction to the area of ​​the second polyethylene fraction can be 6 to 15, 6 to 10, 10 to 15, or any combination of these intervals. According to some modalities, a ratio of the area-weighted average molecular weight of the first polyethylene fraction to an area-weighted average molecular weight of the second polyethylene fraction may be 0.75 to 1.50, 0.75 to 1.25, 0.75 to 1.00, 1.00 to 1.50, 1.00 to 1.25, 1.25 to 1.50, or any combination of these ranges. In one or more embodiments, the weight average molecular weight of the second polyethylene fraction may be from 80,000 g / mol to 200,000 g / mol or from 80,000 g / mol to 150,000 g / mol. In additional embodiments, the weight average molecular weight of the second polyethylene fraction may be from 80,000 g / mol to 200,000 g / mol, from 80,000 g / mol to 150,000 g / mol, from 80,000 g / mol to 100,000 g / mol, from 100,000 g / mol to 200,000 g / mol, from 100,000 g / mol to 150,000 g / mol, from 150,000 g / mol to 200,000 g / mol, or any combination of these ranges. The molecular weight of the polyethylene fractions can be calculated based on the GPC results, as described later in this description. In one or more embodiments, the multimodal polyethylene composition may have a third polyethylene fraction defined by an area in the 95 °C to 120 °C temperature range of an elution profile obtained using the enhanced comonomer composition distribution (iCCD) analysis method. As used herein, in some embodiments, the area of ​​the third polyethylene fraction may be defined as the area in the elution profile below a single peak of the third polyethylene fraction between 95 °C and 120 °C. The first polyethylene area fraction may correspond to the total relative mass of the polymer fraction in the ΜΛ / ΙΖ / ΖυΖΟ / υΊ aoz I multimodal polyethylene composition. In one or more configurations, the third polyethylene fraction may exhibit a single peak in the 95°C to 120°C temperature range in the iCCD elution profile. It should be understood that a peak in the third polyethylene fraction may not be formed by a local minimum within the respective polyethylene fraction at a defined temperature limit. That is, the peak must be a peak within the context of the entire spectrum, not a peak formed by the threshold temperature of a polyethylene fraction. For example, if a single peak followed by a single valley were present in a polyethylene fraction (an upward slope followed by a downward slope followed by an upward slope), only a single peak would be present in that polyethylene fraction.The temperature range of the third polyethylene fraction from 95 to 120 °C may be desirable because the low molecular weight, high density component at 95 °C and 120 °C can allow the polyethylene to achieve a higher overall density while maintaining a lower density fraction. In one or more configurations, the width of the single peak of the third polyethylene fraction at 50 percent peak height can be 2°C to 10°C, 2°C to 8°C, 2°C to 6°C, 2°C to 4°C, 4°C to 10°C, 4°C to 8°C, 4°C to 6°C, 6°C to 10°C, 6°C to 8°C, or 8°C to 10°C. In general, temperature ranges less than 50 percent of the maximum height correspond to a smaller peak. ML / IZ / ZUZO / U aoz I pronounced. Not limited to any particular theory, it is believed that a more pronounced or narrower peak is a feature caused by the molecular catalyst and indicates minimal comonomer incorporation in the higher density fraction, allowing for higher density splitting between the first polyethylene fraction and the third polyethylene fraction. According to one or more of the modalities, the area of ​​the third polyethylene fraction may comprise at least 25% of the total area of ​​the elution profile (e.g., at least 30%, at least 35%, or even at least 40% of the total area of ​​the elution profile). For example, the area of ​​the first polyethylene fraction may comprise 25% to 50%, 25% to 45%, 25% to 40%, 25% to 35%, 25% to 30%, 30% to 50%, 30% to 45%, 30% to 40%, 30% to 35%, 35% to 50%, 35% to 45%, 35% to 40%, 40% to 50%, 40% to 45%, or 45% to 50% of the total area of ​​the elution profile. In one or more embodiments, the weight average molecular weight of the third polyethylene fraction may be less than or equal to 120,000 g / mol, such as from 20,000 g / mol to 120,000 g / mol, or from 40,000 g / mol to 65,000 g / mol. In additional embodiments, the weight average molecular weight of the third polyethylene fraction may be from 20,000 g / mol to 40,000 g / mol, from 40,000 g / mol to 60,000 g / mol, from 60,000 g / mol to 80,000 g / mol, from 80,000 g / mol to 100,000 g / mol, or from ML / IZ / ZUZO / UOZ I 100,000 g / mol to 120,000 g / mol or any combination of these ranges. The molecular weight of the polyethylene fractions can be calculated based on the GPC results, as described later in this document. According to one or more of the modalities, the difference between the single peak of the second polyethylene fraction and the single peak of the first polyethylene fraction can be at least 5 °C. For example, the difference between the single peak of the second polyethylene fraction and the single peak of the first polyethylene fraction can be at least 6 °C, 7 °C, 8 °C, 9 °C, 10 °C, 11 °C, 12 °C, 14 °C, 16 °C, 18 °C, or even at least 20 °C. Polymerization Any conventional polymerization processes can be used to produce the multimodal polyethylene compositions described herein. Such conventional polymerization processes include, but are not limited to, suspension polymerization processes and solution polymerization processes, using one or more conventional reactors, such as loop reactors, isothermal reactors, stirred tank reactors, batch reactors in parallel, in series, and / or any combination thereof. The multimodal polyethylene composition can, for example, be produced by a solution-phase polymerization process using one or more loop reactors, reactors ΜΛ / ΙΖ / ΖυΖΟ / υΊ aoz I isothermal and combinations of these. In general, the solution-phase polymerization process can be carried out in one or more well-mixed reactors, such as one or more isothermal loop reactors or one or more adiabatic reactors, at a temperature in the range of 115 to 250 °C (e.g., 115 to 210 °C), and pressures in the range of 300 to 1000 psi (e.g., 400 to 800 psi). In some embodiments, in a double reactor, the temperature in the first reactor is in the range of 115 to 190 °C (e.g., 160 to 180 °C), and the temperature of the second reactor is in the range of 150 to 250 °C (e.g., 180 to 220 °C). In some modes, in a single reactor, the temperature in the reactor is in the range of 115 to 250 °C (for example, 115 to 225 °C). The residence time in a solution-phase polymerization process can range from 2 to 30 minutes (e.g., 5 to 25 minutes). Ethylene, solvent, hydrogen, one or more catalyst systems, optionally one or more cocatalysts, and optionally one or more comonomers are continuously fed into one or more reactors. Illustrative solvents include, but are not limited to, isoparaffins. For example, such solvents are commercially available under the name ISOPAR E from ExxonMobil Chemical Co., Houston, Texas. The resulting mixture of the multimodal polyethylene composition and the solvent is then withdrawn from the reactor, and the multimodal polyethylene composition is isolated. Typically, the solvent is recovered by means of a solvent recovery unit, e.g., heat exchangers and a vapor-liquid separator drum, and then recycled back into the polymerization system. In some embodiments, the multimodal polyethylene composition can be produced by solution polymerization in a two-reactor system, for example, a double-loop reactor system, where ethylene is polymerized in the presence of one or more catalyst systems. In some embodiments, only ethylene is polymerized. In addition, one or more cocatalysts may be present. In another embodiment, the multimodal polyethylene composition can be produced by solution polymerization in a single-reactor system, for example, a single-loop reactor system, where ethylene is polymerized in the presence of two catalyst systems. In some embodiments, only ethylene is polymerized. Catalytic systems The following describes specific forms of catalyst systems that can be used, in one or more forms, to produce the multimodal polyethylene compositions described herein. It is understood that the catalyst systems described herein can be incorporated in various ways and should not be interpreted as being limited to IVIA / t / ZUZÓ / UI UOZ I the specific modalities set forth in this description. Rather, modalities are provided to make this description exhaustive and complete, and to fully convey the scope of the subject matter to those skilled in the art. The term "independently selected" is used herein to indicate that the R groups, such as R1, R2, R3, R4, and R5, may be identical or different (e.g., all R1, R2, R3, R4, and R5 may be substituted alkyls, or R1 and R2 may be a substituted alkyl and R3 may be an aryl, etc.). The use of the singular includes the use of the plural and vice versa (e.g., a hexane solvent includes hexanes). A named R group will generally have the structure recognized in the art as corresponding to R groups of that name. These definitions are intended to supplement and illustrate, not exclude, the definitions known to those skilled in the art. The term procatalyst refers to a compound that has catalytic activity when combined with an activator. The term activator refers to a compound that reacts chemically with a procatalyst in a way that converts the procatalyst into a catalytically active catalyst. As used herein, the terms cocatalyst and activator are interchangeable. When used to describe certain chemical groups that When chemical groups contain carbon atoms, an expression in parentheses of the form (Cx-Cy) means that the unsubstituted form of the chemical group has from x carbon atoms to y carbon atoms, inclusive. For example, a (C1-C40) alkyl group has from 1 to 40 carbon atoms in its unsubstituted form. In some embodiments and general structures, certain chemical groups may be substituted by one or more substituents, such as Rs. An Rs-substituted version of a chemical group defined using the parenthetical expression (Cx-Cy) may contain more than y carbon atoms, depending on the identity of any of the Rs groups. For example, an alkyl (1-C40) substituted with exactly one Rs group, where Rses phenyl (-CgHs) can contain from 7 to 46 carbon atoms.Therefore, in general, when a chemical group defined by the expression in parentheses (Cx-Cy) is substituted by one or more substituents Rs containing carbon atoms, the minimum and maximum total number of carbon atoms of the chemical group is determined by adding both ax and ay to the combined sum of the number of carbon atoms of all the substituents Rs containing carbon atoms. The term substitution means that at least one hydrogen atom (-H) bonded to a carbon atom or heteroatom of a corresponding unsubstituted compound or functional group is replaced by a substituent (e.g., Rs). The term persubstitution means that each hydrogen atom (H) bonded to a carbon atom or heteroatom of a corresponding unsubstituted compound or functional group is replaced by a substituent (e.g., RS). The term polysubstitution means that at least two, but fewer than all, hydrogen atoms bonded to carbon atoms or heteroatoms of a corresponding unsubstituted compound or functional group are replaced by a substituent. The term -H signifies a hydrogen atom or a hydrogen radical that is covalently bonded to another atom. Hydrogen and -H are interchangeable, and, unless clearly specified, mean the same thing. The term hydrocarbyl (C1-C40) refers to a hydrocarbon radical of 1 to 40 carbon atoms and the term hydrocarbylene (C1-C40) means a hydrocarbon diradical of 1 to 40 carbon atoms, wherein each hydrocarbon radical and each hydrocarbon diradical is aromatic or non-aromatic, saturated or unsaturated, linear-chain or branched-chain, cyclic (including mono- and polycyclic, fused and unfused polycyclic, including bicyclic; 3 or more carbon atoms) or acyclic and is either unsubstituted or is ΜΛ / ΙΖ / ΖυΖΟ / υΊ aoz I replaced by one or more Rs. In this description, a hydrocarbyl (C1-C4) can be an unsubstituted or substituted alkyl (C1-C40), cycloalkyl (C3-C40), cycloalkyl (C3-C20), alkylene (C1-C20), aryl (C5-C40), or aryl (C6-C20)-alkylene (C1-C20). In some embodiments, each of the above-mentioned hydrocarbyl (C1-C40) groups has a maximum of 20 carbon atoms (i.e., hydrocarbyl (C1-C20)), and in other embodiments, a maximum of 12 carbon atoms. The terms alkyl (C1-C40) and alkyl (Ct-Cys) mean a linear or branched saturated hydrocarbon radical of 1 to 40 carbon atoms or 1 to 18 carbon atoms, respectively, that is either unsubstituted or substituted by one or more Rs. Examples of unsubstituted alkyl (C1-C40) include unsubstituted alkyl (C1-C20); unsubstituted alkyl (C1-C10); unsubstituted alkyl (C1-C5); methyl; ethyl; 1-propyl; 2-propyl; 1-butyl; 2-butyl; 2-methylpropyl; 1,1-dimethylethyl; 1-pentyl; 1-hexyl; 1-heptyl; 1-nonyl; and 1-decyl. Examples of substituted (C1-C40) alkyl are substituted (C1-C20) alkyl, substituted (C1-C10) alkyl, trifluoromethyl and [C45] alkyl. The term [C45] alkyl (in brackets) means that there is a maximum of 45 carbon atoms in the radical, including substituents, and is, for example, a (C27-C40) alkyl substituted by an Rs, which is a (C1-C5) alkyl, respectively.Each alkyl (C1-C5) can be methyl, trifluoromethyl, ethyl, 1-propyl, 1-methylethyl, or 1,1-dimethylethyl. The term aryl (Cg-Cg₀) means a mono-, bi-, or tricyclic aromatic hydrocarbon radical of 6 to 40 carbon atoms, unsubstituted or substituted (by one or more Rs), of which at least 6 to 14 of the carbon atoms are aromatic ring carbon atoms, and the mono-, bi-, or tricyclic radical comprises 1, 2, or 3 rings, respectively; wherein the 1st ring is aromatic and the 2nd or 3rd rings are independently fused or unfused, and at least one of the 2nd or 3rd rings is aromatic. Examples of unsubstituted (C6-C40) aryl include unsubstituted (C6-C20) aryl, unsubstituted (Cg-Cs) aryl, 2-alkyl(C1-C5)phenyl, 2,4-bisalkyl(C1-C5)phenyl, phenyl, and fluorenyl. tetrahydrofluorenyl; indacenyl; hexahydroindacenyl; indenyl; dihydroindenyl; naphthyl; tetrahydronaphthyl; and phenanthrene.Examples of substituted aryl(C6-C40) include substituted aryl(C1-C20); substituted aryl(Ce-Cis); 2,4-bis[alkyl(C20)]-phenyl; polyfluorophenyl; pentafluorophenyl; and fluoren-9-one-l-yl. The term cycloalkyl(C3-C40) means a saturated cyclic hydrocarbon radical of 3 to 40 carbon atoms that is either unsubstituted or substituted with one or more Rs. Other cycloalkyl groups (e.g., cycloalkyl(Cx-Cy)) are defined analogously as having x and y carbon atoms and being either unsubstituted or substituted with one or more Rs. Examples of unsubstituted cycloalkyl(C3-C40) include unsubstituted cycloalkyl(C3-C2), unsubstituted cycloalkyl(C3-C13), cyclopropyl, cyclobutyl, cyclopentyl, cyclohexyl, cycloheptyl, cyclooctyl, cyclononyl, and cyclodecyl. Examples of substituted (C3-C40) cycloalkyl include substituted (C3-C20) cycloalkyl, substituted (C3-C10) cycloalkyl, cyclopentanon-2-yl, and 1-fluorocyclohexyl. Examples of hydrocarbylenes (C1-C40) include arylene (C6-C40), cycloalkylene (C3-C40), and alkylene (C1-C40) (e.g., alkylene (C1-C20)), both unsubstituted and substituted. In some forms, the diradicals are on the same carbon atom (e.g., -CH2-) or on adjacent carbon atoms (i.e., 1,2-diradicals), or are separated by one, two, or more than two intermediate carbon atoms (e.g., respective 1,3-diradicals, 1,4-diradicals, etc.). Some diradicals include the α,ω-diradical. The α,ω-diradical is a diradical with maximum separation from the main carbon chain between the substituent carbons. Some examples of α,ω-alkylene diradicals (C2-C20) include ethan-1,2-diyl (i.e., -CH2CH2-), propan-1,3-diyl (i.e., -CH2CH2CH2-), and 2-methylpropan-1,3-diyl (i.e., -CH2CH(CH3)CH2-). Some examples of α,ω-arylene diradicals (C6-C50) include phenyl-1,4-diyl, naphthalene-2,6-diyl, and naphthalene-3,7-diyl. The term alkylene (C1-C40)” means a diradical ML / IZ / ZUZO / UZ aoz I saturated linear chain or branched chain (i.e., radicals are not on ring atoms) of 1 to 40 carbon atoms that is either unsubstituted or substituted by one or more Rs. Examples of unsubstituted (C1-C50) alkylene are unsubstituted (C1-C20) alkylene, which includes -CH2CH2-, -(CH2)3~, -(ch2)4-, -(ch2)5-, -(ch2)6-, -(ch2)7-, -(ch2)8-, -ch2c*hch3 and -(CH2)4C*(H) (CH3) unsubstituted, in which C* denotes a carbon atom from which a hydrogen atom is removed to form a secondary or tertiary alkyl radical. Examples of substituted (C1-C50) alkylene are substituted (C1-C20) alkylene, -CF2-, -C(O)- and -(CH2)14C(CH3)2(CH2)5- (i.e., a normal 6,6-dimethyl-substituted 1,20-eicosylene).Since, as mentioned above, two Rs can be taken together to form an alkylene (Ci-Cig), examples of substituted (C1-C50) alkylene also include 1,2-bis(methylene)cyclopentane, 1,2-bis(methylene)cyclohexane, 2,3-bis(methylene)-Δ,7-dimethylbicyclo[2.2.1]heptane, and 2,3-bis(methylene)bicyclo. [2.2.2]octane. The term cycloalkylene (C3-C40) refers to a cyclic diradical (i.e., the radicals are on ring atoms) of 3 to 40 carbon atoms that is either unsubstituted or substituted by one or more Rs. The term heteroatom refers to an atom other than hydrogen or carbon. Examples of heteroatoms include O, S, S(O), S(O)₂, Si(Rc)₂, P(Rp), N(RN), -N=C(Rc)₂, -Ge(Rc)₂-, or IVIA / t / ZUZÓ / U 1 aoz I -Si(Rc)-, where each Rc, each RN, and each Rp is an unsubstituted (Ci-Cis) hydrocarbyl or -H. The term heterohydrocarbon refers to a molecule or molecular structure in which one or more carbon atoms are replaced with a heteroatom. The term heterohydrocarbyl (C1-C40) refers to a heterohydrocarbon radical of 1 to 40 carbon atoms, and the term heterohydrocarbylene (C1-C40) means a heterohydrocarbon diradical of 1 to 40 carbon atoms, and each heterohydrocarbon has one or more heteroatoms. The heterohydrocarbyl radical is on a carbon atom or a heteroatom, and heterohydrocarbyl diradicals can be on: (1) one or two carbon atoms, (2) one or two heteroatoms, or (3) one carbon atom and one heteroatom.Each heterohydrocarbyl (C1-C50) and heterohydrocarbylene (C1-C50) can be unsubstituted or substituted (by one or more Rs), aromatic or non-aromatic, saturated or unsaturated, linear or branched chain, cyclic (including mono- and polycyclic, fused and non-fused polycyclic) or acyclic. The (C1-C40) heterohydrocarbyl can be (C1-C40) heteroalkyl, (C1-C40) hydrocarbyl -O-, (C1-C40) hydrocarbyl -S-, (C1-C40) hydrocarbyl -S (O) -, (C1-C40) hydrocarbyl -S (O) 2-, (C1-C40) hydrocarbyl -Si (Rc) 2-, (C1-C40) hydrocarbyl -N (RN) -, (C1-C40) hydrocarbyl -P (RF) -, (C2-C40) heterocycloalkyl, (C2-C19) heterocycloalkyl (C1-C20) alkylene, (C3-C20) cycloalkyl - (C1-C19) heteroalkylene, IVIA / t / ZUZÓ / U 1 aoz I heterocycloalkyl (C2-C19) -heteroalkylene (C1-C20) , heteroaryl (C1-C40) , heteroaryl (C1-C19) -alkylene (C1-C20) , aryl (C6-C20) -heteroalkylene (C1-C19) or heteroaryl (C1-C19) heteroalkylene(C1-C20) unsubstituted or substituted. The term heteroaryl(C4-C40) means an unsubstituted or substituted (with one or more Rs) mono-, bi-, or tricyclic heteroaromatic hydrocarbon radical with 4 to 40 carbon atoms in total and 1 to 10 heteroatoms, and the mono-, bi-, or tricyclic radical comprises 1, 2, or 3 rings, respectively, wherein the 2 or 3 rings are independently fused or unfused, and at least one of the 2 or 3 rings is heteroaromatic. Other heteroaryl groups (e.g., heteroaryl(Cx-Cy), such as heteroaryl(C4-C12)) are generally defined analogously as having x and ay carbon atoms (such as 4 to 12 carbon atoms) and being unsubstituted or substituted by one or more Rs. The monocyclic heteroaromatic hydrocarbon radical is a 5-membered or 6-membered ring. The 5-membered ring has 5 less h carbon atoms, where h is the number of heteroatoms and can be 1, 2, or 3; and each heteroatom can be O, S, N, or P.Examples of 5-membered ring heteroaromatic hydrocarbon radicals are pyrrole-l-yl; pyrrole-2-yl; furan-3-yl; thiophen-2-yl; pyrazol-l-yl; isoxazol-2-yl; isothiazol-5-yl; imidazol-2-yl; oxazol-4-yl; thiazol-2-yl; 1,2,4-triazol-l-yl; 1,3,4-oxadiazol-2-yl; 1,3,4-thiadiazol-2-yl;. IVIA / t / ZUZÓ / U 1 aoz I tetrazol-l-yl; tetrazol-2-yl; and tetrazol-5-yl. The 6-membered ring has 6 less h carbon atoms, where h is the number of heteroatoms and can be 1 or 2, and the heteroatoms can be N or P. Examples of heteroaromatic hydrocarbon radicals with a 6-membered ring are pyridin-2-yl; pyrimidin-2-yl; and pyrazin-2-yl. The bicyclic heteroaromatic hydrocarbon radical can be a fused 5,6- or 6,6-ring system. Examples of bicyclic heteroaromatic hydrocarbon radicals with a fused 5,6-ring system are indole-l-yl; and benzimidazol-l-yl. Examples of bicyclic heteroaromatic hydrocarbon radicals with a fused 6,6-ring system are quinolin-2-yl; and isoquinolin-l-yl. The tricyclic heteroaromatic hydrocarbon radical can be a 5,6,5-; 5,6,6-; 6,5,6-; or 6,6,6- ring system. An example of the fused 5,6,5- ring system is 1,7-dihydropyrrolo[3,2-f]indol-l-yl.An example of a fused 5,6,6- ring system is 1H-benzo[f]indole-1-yl. An example of a fused 6,5,6- ring system is 9H-carbazol-9-yl. An example of a fused 6,5,6- ring system is 9Hcarbazol-9-yl. An example of a fused 6,6,6- ring system is acridin-9-yl. The heteroalkyl group mentioned above may be saturated linear or branched chain radicals containing (C1-C50) carbon atoms, or fewer, and one or more heteroatoms. Likewise, the heteroalkylene group may be saturated linear or branched chain diradicals containing 1 to 50 carbon atoms and one or more heteroatoms. The heteroatoms, as defined above, may include Si(Rc)3, Ge(Rc)3, Si(Rc)2, Ge(Rc)2, P(Rp)2, P(Rp), N(Rn)2, N(Rn), N, O, ORc, S, SRc, S(O), and S(O)2, wherein each of the heteroalkyl and heteroalkylene groups is either unsubstituted or substituted by one or more Rs. Examples of unsubstituted (C2-C40) heterocycloalkyl include unsubstituted (C2-C20) heterocycloalkyl, unsubstituted (C2-C10) heterocycloalkyl, aziridin-l-yl, oxetan-2-yl, tetrahydrofuran-3-yl, pyrrolidin-l-yl, tetrahydrothiophen-S,S-dioxide-2-yl, morpholin-4-yl, 1,4-dioxan-2-yl, hexahydroazepin-4-yl, 3-oxa-cyclooctyl, 5-thiocyclononyl, and 2-aza-cyclodecyl. The term halogen atom or halogen means the radical of a fluorine (F) atom, chlorine (Cl) atom, bromine (Br) atom, or iodine (I) atom. The term halide means the anionic form of the halogen atom: fluoride (F⁻), chloride (Cl⁻), bromide (Br⁻), or iodide (I⁻). The term saturated means that it lacks carbon-carbon double bonds, carbon-carbon triple bonds, and (in groups containing heteroatoms) carbon-nitrogen, carbon-phosphorus, and carbon-silicon double bonds. When a saturated chemical group is substituted by one or more Rs substituents, one or more double and / or triple bonds may be present. ML / IZ / ZUZO / UZ aoz I optionally present or not in the Rs substituents. The term unsaturated means that it contains one or more carbon-carbon double bonds, carbon-carbon triple bonds and (in groups containing heteroatoms) carbon-nitrogen, carbon-phosphorus and carbon-silicon double bonds, which do not include any such double bonds that may be present in the Rs substituents, if any, or in (hetero)aromatic rings, if any. According to some embodiments, a catalytic system for producing a polyethylene composition includes a metal-ligand complex according to formula (I): In Formula (I), M is a metal selected from titanium, zirconium, or hafnium, the metal being in a formal oxidation state of +2, +3, or +4; n is 0, 1, 2, or 3. When n is 0 and X is absent, or for each nonzero n, each X independently is a monodentate ligand that is neutral, monoanionic, or dianionic; or two Xs are taken together to form a bidentate ligand that is neutral, monoanionic, or dianionic. When n is 1, X is either a monodentate ligand or a bidentate ligand; when n is 2, each X is a monodentate ligand and is either the same or different; the metal-ligand complex is totally neutral in charge. Each Z is independently selected from -O-, -S-, -N(RN)-, or -P(RP)-;L is hydrocarbylene (C1-C40) or heterohydrocarbylene (C1-C40), wherein the hydrocarbylene (C1-C40) has a portion comprising a connecting backbone of 1 to 10 carbon atoms connecting the two Z groups of Formula (I) (to which L is attached), or the heterohydrocarbylene (C1-C40) has a portion comprising a connecting backbone of 1 to 10 carbon atoms connecting the two Z groups of Formula (I), wherein each of the 1 to 10 atoms of the connecting backbone of 1 to 10 carbon atoms of the heterohydrocarbylene (C1-C40) is independently a carbon atom or a heteroatom, wherein each heteroatom is independently O, S, S(O), S(O)2, Si(Rc)2, Ge(Rc)2, P (Rc) or N(Rc) , where each Rc is independently hydrocarbyl (C1-C30) or heterohydrocarbyl (C1-C30) ;R1 and R8 are independently selected from the group consisting of -H, hydrocarbyl (C1-C40), heterohydrocarbyl (C1-C40), -Si (Rc) 3, -Ge (Rc) 3, -P(RP)2, -N(Rn)2, -0Rc, -SRc, -NO2, -CN, -CF3, RCS(O)-,; RCS (O)2-, (Rc)2C=NRcC(O)O-, RcOC (O) RcC (O) N (RN) -, IVIA / t / ZUZÓ / UI UOZ I (Rn)2NC(O)-, halogen and radicals having formula (II), formula (III) or formula (IV): (IV) In formulas (II), (III) and (IV), each R31-35, R41-48 or R51-59 is chosen independently of (C1-C40) hydrocarbyl, (C1-C40) heterohydrocarbyl, -Si(Rc)3, -Ge(Rc)3, -P(RP)2, -N(Rn)2, -N=CHRC, -ORC, -SRC, -NO2, -CN, -CF3, RCS(O)-, RCS(O)2-, (Rc)2C=N-, RcC(O)O-, RcOC(O)-, RcC(O)N(RN)-, (Rn)2NC(O)-, halogen or -H, provided that at least one of R1 or R8 is a radical having formula (II), formula (III) or formula (IV). In formula (I), each R2~4, R5~7and r9^16 is independently selected from hydrocarbyl (C1-C40), heterohydrocarbyl (C1-C40), -Si (Rc) 3, -Ge(Rc)3, -P(Rp)2, -N(Rn)2, -N=CHRc, -ORC, -SRC, -NO2, -CN, -CF3, RCS (O)-, RCS (O) 2-, (Rc)2C=N-, RcC(O)O-, RcOC(O)-, RcC (O)N (Rn)-, (Rc)2NC(O)-, halogen and -H. In some embodiments, the multimodal polyethylene composition is formed with a first catalyst according to Formula (I) in a first reactor and with a different catalyst according to Formula (I) in a second reactor. In an illustrative embodiment where a double reactor in series configuration is used, the procatalyst used in the first reactor, such as a continuously stirred tank reactor (CSTR), can ML / IZ / ZUZO / U aoz I include a hafnium metal center (M) and the structures are shown in formula (V) below. tBu tBu (V) In this mode, the procatalyst used in the second reactor, such as the loop reactor, may include a hafnium metal center (M) and the structures are shown in formula (VI) below. (VI) Cocatating component The catalyst system comprising a metal-ligand complex of Formula (I) can be made catalytically active by any technique known in the technique for activating metal-based catalysts of polymerization reactions. For example, the system comprising a metal-ligand complex of Formula (I) can be made catalytically active by contacting, or combining, the complex with an activation cocatalyst. Suitable activation cocatalysts for use in the present description include alkyl aluminums; polymeric or oligomeric alumoxanes (also known as aluminoxanes); neutral Lewis acids; and non-polymeric, non-coordinating, ion-forming compounds (including the use of such compounds under oxidizing conditions). One suitable activation technique is bulk electrolysis. Combinations of one or more of the above cocatalysts and activation techniques are also contemplated.The term alkylaluminum means a monoalkylaluminum dihydride or monoalkylaluminum dihalide, a dialkylaluminum hydride or dialkylaluminum halide, or a trialalkylaluminum. Examples of polymeric or oligomeric alumoxanes include methylalumoxane, triisobutylaluminum-modified methylalumoxane, and isobutylaluminumoxane. Lewis acid activators (cocatalysts) include group 13 metal compounds containing 1 to 3 hydrocarbyl (C1-C20) substituents as described herein. In one embodiment, the compounds of Group 13 metals are tri(hydrocarbyl(C1-C20))-substituted aluminum or tri(hydrocarbyl(C1-C20))-boron compounds. In some embodiments, group 13 metal compounds are tri(hydrocarbyl)-substituted aluminum, tri(hydrocarbyl(C1-C20))-boron compounds, tri(alkyl(C1-C10))-aluminum compounds, tri(aryl(C1-C10))-boron compounds, and halogenated (including perhalogenated) derivatives thereof. In further embodiments, group 13 metal compounds are tris(fluoro-substituted phenyl)boranes and tris(pentafluorophenyl)borane. In some forms, the activation cocatalyst is a tris(hydrocarbyl(C1-C20)borate) (e.g., trityl tetrafluoroborate) or tri(hydrocarbyl(C1-C20)ammonium tetra(hydrocarbyl(C1-C20)borane) (e.g., bis(octadecyl)methylammonium tetrakis(pentafluorophenyl)borane).As used in the present description, the term ammonium means a nitrogen cation that is a (C1-C20) hydrocarbyl) 4N+, a (C1-C20) hydrocarbyl) 3N(H)+, a (C1-C20) hydrocarbyl) 2N(H) 2+, a (C1-C20) hydrocarbyl N(H) 3+ or N(H)4+, wherein each (C1-C20) hydrocarbyl, when two or more are present, may be the same or different. Combinations of neutral Lewis acid activators (cocatalysts) include mixtures comprising a combination of a tri(alkyl(C1-C4))aluminum compound and a halogenated tri(aryl(Ce-Cys))boron compound, especially a tris(pentafluorophenyl)borane. Modalities include combinations of such neutral Lewis acid mixtures with a polymeric or oligomeric alumoxane, and combinations of a single neutral Lewis acid, especially tris(pentafluorophenyl)borane, with a polymeric or oligomeric alumoxane. The mole number ratios of (metal-ligand complex): (tris(pentafluorophenylborane): (alumoxane) [e.g., (Group 4 metal-ligand complex): (tris(pentafluorophenylborane) : (alumoxane) ] are from 1:1:1 to 1:10:30, in the forms, from 1:1:1.5 to 1:5:10. The catalyst system comprising the metal-ligand complex of formula (I) can be activated to form an active catalyst composition by combination with one or more cocatalysts, for example, a cation-forming cocatalyst, a strong Lewis acid, or combinations thereof. Suitable activation cocatalysts include polymeric or oligomeric aluminoxanes, especially methyl aluminoxane, as well as inert, compatible, non-coordinating, and ion-forming compounds. Illustrative suitable cocatalysts include, but are not limited to: modified methyl aluminoxane (MMAO), bis(hydrogenated tallow alkyl)methyl, tetrakis(pentafluorophenyl)borate(1)amine, and combinations thereof. ML / IZ / ZUZO / U aoz I In some forms, one or more of the cocatalysts The six activation cocatalysts described above are used in combination with each other. A particularly preferred combination is a mixture of a tri((C1-C4)hydrocarbyl)aluminum, tri((C1-C4)hydrocarbyl)borane, or an ammonium borate with an oligomeric or polymeric alumoxane compound. The ratio of the total number of moles of one or more metal-ligand complexes of formula (I) to the total number of moles of one or more of the activation cocatalysts is from 1:10,000 to 100:1. In some embodiments, the ratio is at least 1:5000, in some embodiments at least 1:1000; and 10:1 or less, and in some embodiments, 1:1 or less. When an alumoxane is used alone as the activation cocatalyst, the molar amount of alumoxane used is preferably at least 100 times the molar amount of the metal-ligand complex of Formula (I).When tris(pentafluorophenyl)borane is used alone as an activation cocatalyst, in some embodiments, the molar number of tris(pentafluorophenyl)borane employed with respect to the total molar number of one or more metal-ligand complexes of Formula (I) is 0.5:1 to 10:1, 1:1 to 6:1, or 1:1 to 5:1. The remaining activation cocatalysts are generally employed in molar amounts approximately equal to the total molar amounts of one or more metal-ligand complexes of Formula (I). Multilayer films The following section will refer to the types of multilayer films described herein. ML / IZ / ZUZO / U aoz I The multilayer films described herein may include at least two layers and up to three, four, five, six, seven, nine, eleven, thirteen, or more layers. The number of layers in the multilayer film may depend on several factors, including, for example, the composition of each layer, the desired properties of the film, the intended end-use application, the manufacturing process, and others. As described in more detail herein, the multilayer film configurations may include a first layer, as described later, and a second layer, as described later, and one or more sub-layers, as described later. The first layer, the second layer, or both may include the multimodal polyethylene composition described herein. The multilayer film may be a two-layer film designated as A / B, where the first layer may be designated as (A) and the second layer as (B). As used herein, direct contact means that there may be no other layers placed between the two layers that are in direct contact with each other. In some modalities, the first layer (A) may be in direct contact with the second layer (B). In different modalities, multilayer film can be a A three-layer film designated as A / B / C, where the first layer may be designated as (A), the second layer as (B), and the third layer as (C). In some forms, the second layer (B) may be placed between the first layer (A) and the third layer (C), and the second layer (B) may be called the intermediate layer or the middle layer. In some forms, one or both of the first layer (A) and the third layer (C) may be the outermost layers of the multilayer film, which may be called the outer layers. As used herein, it may be understood that the outermost layers of the multilayer film mean that there may be no other layer deposited on top of the outermost layer, so that the outermost layer is in direct contact with the surrounding air. In some forms, the first layer (A) may be in direct contact with the second layer (B). In some modalities, the second layer (B) may be in direct contact with the third layer (C). In some embodiments, multilayer films may include one or more additional layers besides the outer layers and the core layer. Such additional layers may include layers comprising polyethylene, which may or may not include the multimodal polyethylene composition described herein. In some embodiments, the additional polyethylene layers may ML / IZ / ZUZO / UZ aoz I include a mixture of LLDPE, LDPE, MDPE, HDPE, the selected multimodal polyethylene composition described herein, and combinations thereof. The various polyethylene components (e.g., LLDPE, LDPE, HDPE, and the multimodal polyethylene composition described herein) may be included in the additional polyethylene layer in any desired quantity according to the properties of the multilayer film to be achieved. Such additional layers may alternatively or additionally include one or more additional adhesive layers. It should be understood that any of the above layers may further comprise one or more additives known to those skilled in the art, for example, plasticizers, stabilizers including viscosity stabilizers, hydrolytic stabilizers, primary and secondary antioxidants, ultraviolet light absorbers, antistatic agents, dyes, pigments or other coloring agents, inorganic fillers, flame retardants, lubricants, reinforcing agents such as fiberglass and sheets, synthetic fiber or pulp (for example, aramid), foaming or blowing agents, processing aids, slip additives, antiblocking agents such as silica or talc, release agents, tack-enhancing resins, or combinations of two or more of these. Inorganic fillers, such as calcium carbonate and IVIA / t / ZUZÓ / UΊ aoz I similar additives may also be incorporated into one or more of the first layer, the second layer, the third layer, and combinations thereof. In some embodiments, each of the surface layers, sub-surface layers, adhesive layers, protective layer, and combinations thereof may include up to 5 percent by weight of such additional additives based on the total weight of the respective layer. All individual values ​​and sub-intervals from 0% by weight to 5% by weight are included and described herein. For example, the total amount of additives in the first layer, the second layer, or the third layer can be from 0.5% by weight to 5% by weight, from 0.5% by weight to 4% by weight, from 0.5% by weight to 3% by weight, from 0.5% by weight to 2% by weight, from 0.5% by weight to 1% by weight, from 1% by weight to 5% by weight, from 1% by weight to 4% by weight.%, from 1% by weight to 3% by weight, from 1% by weight to 2% by weight, from 2% by weight to 5% by weight, from 2% by weight to 4% by weight, from 2% by weight to 3% by weight, from 3% by weight to 5% by weight, from 3% by weight to 4% by weight, or from 4% by weight to 5% by weight based on the total weight of the respective layer. The incorporation of the additives can be carried out by any known process such as, for example, by dry mixing, by extrusion of a mixture of the various constituents, by the conventional master mix technique, or by a similar process. The multilayer films described herein can have a variety of thicknesses. The thickness of the multilayer film can depend on several factors, including, for example, the number of layers in the film, the composition of the layers, the desired properties of the film, the intended end-use application, the manufacturing process, and others. In some cases, the multilayer film can have a thickness of less than 205 micrometers (µm). In various forms, the multilayer film can have a thickness of 15 pm to 205 pm, 20 pm to 180 pm, 15 pm to 180 pm, 15 pm to 160 pm, 15 pm to 140 pm, 15 pm to 120 pm, 15 pm to 100 pm, 15 pm to 80 pm, 15 pm to 60 pm, 15 pm to 40 pm, 20 pm to 160 pm, 20 pm to 140 pm, 20 pm to 120 pm, 20 pm to 100 pm, 20 pm to 80 pm, 20 pm to 60 pm or 20 pm to 40 pm. The multilayer films described herein may have an overall density that depends on several factors, including, for example, the number of layers in the multilayer film, the composition of the layers in the multilayer film, the desired properties of the multilayer film, the intended end-use application of the film, the manufacturing process of the multilayer film, and others. In some embodiments, the multilayer film may have an overall density of at least 0.925 grams per cubic centimeter (g / cm³). In some embodiments, the overall density of the multilayer film ΜΛ / ΙΖ / ΖυΖΟ / υΊ aoz I can be from 0.925 g / cm3 to 0.970 g / cm3, from 0.925 g / cm3 to 0.940 g / cm3, from 0.925 g / cm3 to 0.935 g / cm3, from 0.925 g / cm3 to 0.930 g / cm3, from 0.930 g / cm3 to 0.940 g / cm3, from 0.930 g / cm3 to 0.935 g / cm3, from 0.935 g / cm3 to 0.940 g / cm3 or from 0.935 g / cm3 to 0.950 g / cm3. In one or more embodiments, the multilayer films of the present description may have a puncture strength of at least 1 newton per micrometer of film (N / pm), when measured in accordance with ASTM D 5748-95. In other embodiments, the multilayer films of the present description may have a puncture strength of 1 N / pm to 1.5 N / pm, 1 N to 1.25 N / pm, or 1.25 N / pm to 1.5 N / pm, when measured in accordance with ASTM D 5748-95. In one or more embodiments, the multilayer films of the present description may have a puncture resistance of more than 10 Joules per cubic centimeter (J / cm3), when measured in accordance with ASTM D 5748-95. In some embodiments, the multilayer films of the present description may have a puncture resistance greater than 8 J / cm3 or greater than 10 J / cm3, when measured in accordance with ASTM D 5748-95. The multilayer films described herein may have a perforation elongation of at least 55 millimeters (mm), when measured in accordance with ASTM D 5748-95. In some embodiments, the multilayer films described herein may have a perforation elongation of ΜΛ / ΙΖ / ΖυΖΟ / υΊ aoz I mm to 150 mm, from 55 mm to 100 mm from 55 mm to 80 mm, from 55 mm to 60 mm, from 60 mm to 150 mm, from 60 mm to 100 mm, from 60 mm to 80 mm, or from 80 mm to 100 mm, when It is measured in accordance with ASTM D 574895. Outer layers As previously stated, the multilayer films described herein may include one or more outer layers. The outermost layers of the multilayer film, which may be referred to as outer layers, mean that no other layer can be deposited on top of the outermost layer, so that the outermost layer is in direct contact with the surrounding air. The outer layers may impart properties to the multilayer film that aid in stretchability, processability, and other characteristics. An outer layer may also be referred to as a surface layer. In some versions, one or both of the first layer (A) and the third layer (C) may be the outermost layers of the multilayer film, which may be referred to as outer layers. Outer layers may include sealing layers. A sealing layer is generally an outer layer of a film that can be used to adhere the film to other films, to rigid materials (e.g., trays), or to itself. Those skilled in the art will recognize that a variety of olefin-based polymers can be used as a sealing layer in various embodiments based on the teachings of this description. In some embodiments, to facilitate recyclability, a polyethylene may be the primary component of each sealing layer. A non-limiting example of a resin that can be used as a sealing layer according to some embodiments is SEALUTION™ 220. Other resins that can be used to form sealing layers include, but are not limited to, AFFINITY™, ELITE AT™, and ELITE™ resins, which are commercially available from The Dow Chemical Company. In some embodiments, at least one outer layer may include the multimodal polyethylene composition described herein. In some embodiments, the outer layer comprising the multimodal polyethylene composition described herein may be blended with a polyethylene having a density of 0.870 g / cm³ to 0.970 g / cm³. In some embodiments, at least one outer layer may include more than 20% by weight of the selected multimodal polyethylene composition described herein, based on the total weight of the respective layer. In one or more embodiments, each outer layer may include more than 20% by weight of the multimodal polyethylene composition described herein, based on the total weight of the respective layer. In some embodiments, each outer layer may include from 0% to 100% by weight, from 30% to 100% by weight, from 50% to 80% by weight, or from ML / IZ / ZUZO / UZ aoz I % by weight to 60% by weight, from 60% by weight to 100% by weight, from 60% by weight to 80% by weight, or from 80% by weight to 100% by weight of the multimodal polyethylene composition described herein, based on the total weight of the respective layer. In some embodiments, outer layers that do not comprise the multimodal polyethylene composition described herein may include a polyethylene having a density from 0.870 g / cm3 to 0.970 g / cm3. In some embodiments, each outer layer may include an LLDPE, an HDPE, the multimodal polyethylene composition described herein, an MDPE, an LDPE, and combinations thereof. In one or more forms, a linear low-density polyethylene (LLDPE) with a density of 0.905 g / cm3 to 0.930 g / cm3, each outer layer may include a density of 0.905 g / cm3 when measured according to the following specifications: ΜΛ / ΙΖ / ΖυΖΟ / υΊ aoz I with ASTM D792. In another embodiment, the density of linear low-density polyethylene may be 0.905 g / cm3a 0.925 g / cm3, 0.905 g / cm3a 0.920 g / cm3, 0.905 g / cm3a 0.915 g / cm3, 0.905 g / cm3a 0.910 g / cm3a 0.910 g / cm3a 0.915 g / cm3a 0.920 g / cm3a 0.925 g / cm3a 0.910 g / cm3, the 0.925 g / cm3, the 0.915 g / cm3, the 0.925 g / cm3, the 0.930 g / cm3, the 0.930 g / cm3. 0.910 g / cm3a 0.910 g / cm3a 0.915 g / cm3a 0.915 g / cm3a 0.920 g / cm3a 0.93 0 g / cm3, the 0.92 0 g / cm3, the 0.930 g / cm3, the 0.920 g / cm3, the 0.92 5 g / cm3, the In one or more modalities, each outer layer may include a linear low-density polyethylene (LLDPE) that has a melt index (I2) of 0.2 grams per 10 minutes (g / 10 min) to 6.0 g / 10 min when measured in accordance with ASTM D1238. It is also considered that the melting index (I2) of linear low-density polyethylene can be from 0.2 g / 10 min to 5.5 g / 10 min, from 0.2 g / 10 min to 5.0 g / 10 min, or from 0.2 g / 10 min to 4.5 g / 10 min, from 0.5 g / 10 min to 4.0 g / 10 min, from 0.5 g / 10 min to 3.5 g / 10 min, from 0.5 g / 10 min to 3.0 g / 10 min, from 1.0 g / 10 min to 2.0 g / 10 min, from 1.0 g / 10 min to 1.5 g / 10 min, or from 1.5 g / 10 min to 2.0 g / 10 min. According to some embodiments, linear low-density polyethylene can have a molecular weight distribution, expressed as the ratio of weight average molecular weight to number average molecular weight (Mw / Mn), in the range of 3.5 to 5.5. In additional embodiments, linear low-density polyethylene can have a molecular weight distribution in the range of 3.5 to 4.5 or 4.5 to 5.5. According to one or more additional embodiments, linear low-density polyethylene may have a zero shear viscosity ratio of 1.2 to 3.0, when measured according to the test methods described herein. In certain embodiments, linear low-density polyethylene may have a zero shear viscosity ratio of 1.2 to 2.5, 1.2 to 2.0, or 2.0 to 3.0. ΜΛ / ΙΖ / ΖυΖΟ / υΊ aoz I from 2.0 to 2.5 or from 2.5 to 3.0. Various methodologies are considered for producing linear low-density polyethylenes. For example, linear low-density polyethylene resins can be manufactured using Ziegler-Natta catalyst systems, resin produced using single-site catalysts including, but not limited to, bismetallocene catalysts and geometry-constrained catalysts, and resin produced using postmetallocene molecular catalysts. Linear low-density polyethylene resins may include linear, substantially linear, or heterogeneous polyethylene copolymers or homopolymers. Linear low-density polyethylene resins may contain fewer long-chain branches than LOPEs and include substantially linear polyethylenes as further defined in U.S. Patent No. 5,272,236, U.S. Patent No. 5,278,272, and U.S. Patent No. 5,582,923 and U.S. patent no.5,733,155; homogeneously branched linear ethylene polymer compositions, such as those in U.S. Patent No. 3,645,992; heterogeneously branched ethylene polymers, such as those prepared according to the process described in U.S. Patent No. 4,076,698; and mixtures thereof (such as those described in U.S. Patent No. 3,914,342 or in U.S. Patent No. ... IVIA / t / ZUZÓ / UI UOZ I no. 5,854,045). Linear low-density polyethylene resins can be manufactured by gas-phase, solution-phase, or suspension-phase polymerization, or any combination thereof, using any type of reactor or reactor configuration known in the art. In one or more embodiments, each outer layer may include more than 50% by weight of linear low-density polyethylene, based on the total weight of the respective layer. In some embodiments, the second layer, the third layer, or both may include from 50% to 100% by weight, from 50% to 80% by weight, from 50% to 60% by weight, from 60% to 100% by weight, from 60% to 80% by weight, or from 80% to 100% by weight of LLDPE, based on the total weight of the respective layer. In some models, each outer layer may include a high-density polyethylene (HDPE) that has a density of 0.935 g / cm3 and up to 0.980 g / cm3 when measured according to ASTM D792. In another modality, it can have 0.935 g / cm3a 0.935 g / cm3a 0.940 g / cm3a 0.940 g / cm3a 0.950 g / cm3a 0.960 g / cm3a. 0.960 g / cm3, of 0.940 g / cm3, of 0.970 g / cm3, of 0.950 g / cm3, of 0.970 g / cm3, of 0.980 g / cm3, of polyethylene 0.935 g / cm3a 0.935 g / cm3a 0.940 g / cm3a 0.940 g / cm3a 0.950 g / cm3a 0.950 g / cm3a 0.960 g / cm3a high density 0.970 g / cm3, the 0.95 0 g / cm3, the 0.980 g / cm3, the 0.960 g / cm3, the 0.98 0 g / cm3, the 0.9 60 g / cm3, the 0.970 g / cm3o 0.970 g / cm3a 0.980 g / cm3. In one or more embodiments, each outer layer may include a high-density polyethylene having a melt index (I2) of 0.1 grams per 10 minutes (g / 10 min) to 10.0 g / 10 min when measured in accordance with ASTM D1238 at a load of 2.16 kg and a temperature of 190 °C. It is also contemplated that the melt index (I2) of the high-density polyethylene may be from 0.1 g / 10 min to 5.0 g / 10 min, from 0.1 g / 10 min to 1.0 g / 10 min, or from 1.0 g / 10 min to 10.0 g / 10 min, from 1.0 g / 10 min to 5.0 g / 10 min, or from 5.0 g / 10 min to 10.0 g / 10 min. Various methodologies are considered for producing high-density polyethylene. For example, high-density polyethylene resins can be manufactured using Ziegler-Natta catalytic systems, chromium catalysts, or single-site catalysts, including, but not limited to, bis-metallocene catalysts and constrained geometry catalysts. In one or more embodiments, each outer layer may include up to 50% by weight of high-density polyethylene, based on the total weight of the respective layer. In some embodiments, each outer layer may include from 0% to 90% by weight, from 15% to 80% by weight, from 15% to 50% by weight, from 20% to 50% by weight, from 30% to 40% by weight, or from 35% to 50% by weight of high-density polyethylene, based on the total weight of the respective layer. ML / IZ / ZUZO / UZ yoz I In one or more configurations, each outer layer may include an MDPE. The term MDPE, when used alone, refers to polyethylenes with densities of 0.917 to 0.936 g / cm³. MDPEs are typically manufactured using chromium or Ziegler-Natta catalysts or single-site catalysts, including, but not limited to, substituted monocyclopentadienyl or biscyclopentadienyl catalysts (typically referred to as metallocene), restricted geometry catalysts, phosphinimine catalysts, and polyvalent aryloxy ether catalysts (typically referred to as bisphenyl phenoxy). It should be noted that MDPE may be used in one or more of the outer layers. In one or more configurations, each outer layer may include up to 50% by weight of MDPE, based on the total weight of the respective layer. In some configurations, each outer layer may include from 0% to 90% by weight, from 15% to 80% by weight, from 15% to 50% by weight, from 20% to 50% by weight, from 30% to 40% by weight, or from 35% to 50% by weight of MDPE, based on the total weight of the respective layer. In some models, each outer layer may include a low-density polyethylene (LDPE). In one or more models, the low-density polyethylene may have a melting index of 0.1 g / 10 min to 10.0 g / 10 min when measured according to ASTM D1238 at a load of 2.16 kg and a temperature of 190 °C. In some embodiments, low-density polyethylene may have a melting index of 0.1 g / 10 min to 5.0 g / 10 min, or from 0.5 g / 10 min to 5.0 g / 10 min, or from 0.5 g / 10 min to 2.0 g / 10 min. In some embodiments, low-density polyethylene may have a density of 0.916 g / cm³ to 0.935 g / cm³ when measured according to ASTM D792. In another embodiment, low-density polyethylene may have a density of 0.916 g / cm³ to 0.925 g / cm³. In one or more embodiments, each outer layer may include less than 50% by weight of low-density polyethylene, based on the total weight of the respective layer. In some embodiments, each outer layer may include from 0% to 50% by weight, from 0% to 40% by weight, from 0% to 35% by weight, from 5% to 35% by weight, from 10% to 35% by weight, or from 15% to 35% by weight of low-density polyethylene, based on the total weight of the respective layer. In some versions, the outer layers of the multilayer films described herein can have a variety of thicknesses. The thickness of each outer layer can depend on several factors, including, for example, the composition of each outer layer, the desired processability properties of the multilayer film, and others. In some versions, each outer layer can have a thickness from 1 micrometer (µm) to 40 µm. In some versions, each outer layer can have a thickness from 1 µm to 40 µm, from 1 µm to IVIA / t / ZUZÓ / UΊ aoz I μΐϊΐ, from 1 μιη to 2 0 pm, from 1 μσι to 10 μιη, from 10 pm to 4 0 pm, from 10 μιη to 3 0 μιη, from 10 μπι to 2 0 μπι, from 2 0 μπι to 4 0 μπι, from 2 0 μη to 3 0 μπι or from 3 0 μπι to 4 0 μπι. The thickness of each outer layer of the multilayer films described herein may constitute from 5% to 20% of the total thickness of the multilayer film. In some embodiments, the thickness of each outer layer may constitute from 5% to 15%, from 5% to 10%, from 10% to 20%, from 10% to 15%, or from 15% to 20% of the total thickness of the multilayer film. Subsurface layers As previously stated, the multilayer films described herein may include one or more subsurface layers. As used herein, a subsurface layer may refer to any layer placed between the outer layers of a multilayer film. The central subsurface layer of the multilayer film may also be referred to as the intermediate layer or core layer. In various embodiments, each subsurface layer may include one or more materials that impart improved darting and puncture properties to the multilayer film compared to conventional multilayer films. In formulations comprising multiple subsurface layers, each subsurface layer may include the same materials, or each subsurface layer may include different materials. For example, in a five-layer film designated A / B / C / D / E, layer (B) and layer (D) may include the same materials or different materials. In a seven-layer film designated A / B / C / D / E / F / G, one or more of layers (B), (C), (E), and (F) may include the same materials or different materials. In a nine-layer film designated A / B / C / D / E / F / G / H / I, one or more of layers (B), (C), (G), and (H) may include the same materials or different materials. In some embodiments, at least one subsurface layer may include the multimodal polyethylene composition described herein. In some embodiments, the subsurface layer comprising the multimodal polyethylene composition described herein may be blended with a polyethylene having a density of 0.870 g / cm³ to 0.970 g / cm³. In some embodiments, at least one subsurface layer may include more than 20% by weight of the multimodal polyethylene composition described herein, based on the total weight of the respective layer. In one or more embodiments, each subsurface layer may include more than 20% by weight of the multimodal polyethylene composition described herein, based on the total weight of the respective layer.In some embodiments, each subsurface layer may include from wt% to 100 wt%, from 50 wt% to 80 wt%, from 50 wt% to 60 wt%, from 60 wt% to 100 wt%, from 60 wt% to 80 wt% or from 80 wt% to 100 wt% of the multimodal polyethylene composition described herein, based on the total weight of the respective layer. In some embodiments, each subsurface layer may include LLDPE, HDPE, the multimodal polyethylene composition described herein, MDPE, LDPE, and combinations thereof. In some embodiments, the subsurface layers that do not comprise the selected multimodal polyethylene composition described herein may include a polyethylene having a density of 0.870 g / cm³ to 0.970 g / cm³. In one or more ways, each subsurface cap can include low density linear polyethylene (LLDPE) which has a density of 0.905 g / cm3 to 0.930 g / cm3 when tested with ASTM D792. In another way, the density of the IVIA / t / ZUZÓ / UI UOZ Low density linear polyethylene can be used 0.905 g / cm3 0.925 g / cm3de 0.905 g / cm:g / cm:de 0.905 g / cm: 0.915 g / cm3de 0.905 g / cm3 0.910 g / cm3de 0.910 g / cm3 0.930 g / cm3de 0.910 g / cm3g / cm3de 0.910 g / cm3 0.920 g / cm3de 0.910 g / cm3g / cm3de 0.915 g / cm3 0.930 g / cm3de 0.915 g / cm3g / cm3de 0.915 g / cm3 0.920 g / cm3de 0.920 g / cm3g / cm3de 0.920 g / cm: 0.925 g / cm3, from 0.925 g / cm3 to 0.930 g / cm3. In one or more modalities, each subsurface layer may include a linear low-density polyethylene (LLDPE) that has a melt index (la) of 0.2 grams per 10 minutes (g / 10 min) to 6.0 g / 10 min when measured in accordance with ASTM D1238. It is also considered that the melting index (I2) of linear low-density polyethylene can be from 0.2 g / 10 min to 5.5 g / 10 min, from 0.2 g / 10 min to 5.0 g / 10 min, or from 0.2 g / 10 min to 4.5 g / 10 min, from 0.5 g / 10 min to 4.0 g / 10 min, from 0.5 g / 10 min to 3.5 g / 10 min, from 0.5 g / 10 min to 3.0 g / 10 min, from 1.0 g / 10 min to 2.0 g / 10 min, from 1.0 g / 10 min to 1.5 g / 10 min, or from 1.5 g / 10 min to 2.0 g / 10 min. According to some embodiments, linear low-density polyethylene can have a molecular weight distribution, expressed as the ratio of weight average molecular weight to number average molecular weight (Mw / Mn), in the range of 3.5 to 5.5. In additional embodiments, linear low-density polyethylene can have a molecular weight distribution in the range of 3.5 to 4.5 or 4.5 to 5.5. According to one or more additional embodiments, linear low-density polyethylene may have a zero shear viscosity ratio of 1.2 to 3.0, when measured according to the test methods described herein. In certain embodiments, linear low-density polyethylene ML / IZ / ZU / ZU / U aoz I density can have a zero shear viscosity ratio of 1.2 to 2.5, 1.2 to 2.0, 2.0 to 3.0, 2.0 to 2.5 or 2.5 to 3.0. Various methodologies are considered for producing linear low-density polyethylenes. For example, linear low-density polyethylene resins can be manufactured using Ziegler-Natta catalyst systems, resin produced using single-site catalysts including, but not limited to, bismetallocene catalysts and geometry-constrained catalysts, and resin produced using postmetallocene molecular catalysts. Linear low-density polyethylene resins may include linear, substantially linear, or heterogeneous polyethylene copolymers or homopolymers. Linear low-density polyethylene resins may contain fewer long-chain branches than LDPEs and include substantially linear polyethylenes as further defined in U.S. Patent No. 5,272,236, U.S. Patent No. 5,278,272, and U.S. Patent No. 5,582,923 and U.S. patent no.5,733,155; homogeneously branched linear ethylene polymer compositions, such as those in U.S. Patent No. 3,645,992; heterogeneously branched ethylene polymers, such as those prepared according to the process described in U.S. Patent No. 4,076,698; ML / IZ / ZUZO / UOZ I and mixtures thereof (such as those described in U.S. Patent No. 3,914,342 or U.S. Patent No. 5,854,045). Linear low-density polyethylene resins may be manufactured by gas-phase, solution-phase, or suspension-phase polymerization, or any combination thereof, using any type of reactor or reactor configuration known in the art. In one or more modalities, each subsurface layer may include from 0% by weight to 80% by weight, from 0% by weight to 60% by weight, from 0% by weight to 40% by weight, from 0% by weight to 20% by weight, from 20% by weight to 80% by weight, from 20% by weight to 60% by weight, from 20% by weight to 40% by weight, from 40% by weight to 80% by weight, from 40% by weight to 60% by weight or from 60% by weight to 80% by weight of LLDPE, based on the total weight of the respective layer. In some embodiments, each subsurface layer may include a low-density polyethylene (LDPE). In one or more embodiments, the low-density polyethylene may have a melt strength index of 0.1 g / 10 min to 10.0 g / 10 min when measured in accordance with ASTM D1238 at a load of 2.16 kg and a temperature of 190 °C. In some embodiments, the low-density polyethylene may have a melt strength index of 0.1 g / 10 min to 5.0 g / 10 min, or of 0.5 g / 10 min to 5.0 g / 10 min, or of 0.5 g / 10 min to 2.0 g / 10 min. In some embodiments, the low-density polyethylene may have a density of 0.916 g / cm³ to 0.935 g / cm³. MA / t / ZUZÓ / U 1 yoz I when measured according to ASTM D7 92. In another form, low-density polyethylene may have a density of 0.916 g / cm3 to 0.925 g / cm3. In one or more configurations, each subsurface layer may contain less than 50% by weight of LDPE, based on the total weight of the respective layer. In some configurations, each subsurface layer may contain from 0% to 50% by weight, from 0% to 40% by weight, from 0% to 35% by weight, from 5% to 35% by weight, from 10% to 35% by weight, or from 15% to 35% by weight of LDPE, based on the total weight of the respective layer. In one or more configurations, each subsurface layer may include an MDPE. Typically, the MDPE is manufactured using chromium or Ziegler-Natta catalysts or single-site catalysts, including, but not limited to, substituted mono- or bis-cyclopentadienyl catalysts (typically referred to as metallocene), restricted geometry catalysts, phosphinimine catalysts, and polyvalent aryloxy ether catalysts (typically referred to as bisphenyl phenoxy). It should be noted that the MDPE may be used in one or more subsurface layers. In one or more configurations, each subsurface layer may include more than 20% by weight of MDPE, based on the total weight of the respective layer. In some configurations, each subsurface layer may include from 30% to 100% by weight. ML / IZ / ZUZO / UZ aoz I from 50% by weight to 80% by weight, from 50% by weight to 60% by weight, from 60% by weight to 100% by weight, from 60% by weight to 80% by weight or from 80% by weight to 100% by weight of MDPE, based on the total weight of the respective layer. In some models, each subsurface layer may include a high-density polyethylene (HDPE) that has a density of g / cm3 and up to 0.980 g / cm3 when measured according to ASTM D792 . In another form, HDPE can have a density of 0.935 g / cm3a g / cm3de 0.935 g / cm3 0.960 g / cm3, g / cm3, g / cm3, g / cm3 0.940 g / cm3, of 0.940 g / cm3 0.970 g / cm3, of 0.940 g / cm3 0.960 g / cm3 0.940 g / cm3 0.950 g / cm3, of 0.950 g / cm3 0.980 g / cm3 of g / cm3 0.970 g / cm3, of 0.950 g / cm3 0.980 g / cm3, of g / cm3 0.970 g / cm3 or g / cm3 0.980 g / cm3. In one or more configurations, each subsurface layer may include HDPE having a melt strength index (I2) of 0.1 grams per 10 minutes (g / 10 min) to 10.0 g / 10 min when measured in accordance with ASTM D1238 at a load of 2.16 kg and a temperature of 190 °C. It is also contemplated that the melt strength index (I2) of the high-density polyethylene may be from 0.1 g / 10 min to 5.0 g / 10 min, from 0.1 g / 10 min to 1.0 g / 10 min, or from 1.0 g / 10 min to 10.0 g / 10 min, from 1.0 g / 10 min to 5.0 g / 10 min, or from 5.0 g / 10 min to 10.0 g / 10 min. Various methodologies are considered for producing high-density polyethylene. For example, HDPE resins can be manufactured using Ziegler-Natta catalyst systems, chromium catalysts, or single-site catalysts, including, but not limited to, bis-metallocene catalysts and geometry-constrained catalysts. In one or more configurations, each subsurface layer may include up to 50% by weight of HDPE, based on the total weight of the respective layer. In some configurations, each subsurface layer may include from 0% to 90% by weight, from 15% to 80% by weight, from 15% to 50% by weight, from 20% to 50% by weight, from 30% to 40% by weight, or from 35% to 50% by weight of HDPE, based on the total weight of the respective layer. In some versions, each subsurface layer of the multilayer films described herein may have a variety of thicknesses. The thickness of each subsurface layer may depend on several factors, including, for example, the composition of the subsurface layer, the desired overall dart and puncture properties of the multilayer film, and others. In some versions, each subsurface layer may have a thickness of 1 µm to 85 µm. In some versions, each outer layer may have a thickness of 1 µm to 80 µm, 1 µm to 60 µm, 1 µm to 40 µm, 1 µm to 20 µm, 20 µm to 80 µm, 20 µm to 60 µm, 20 µm to 40 µm, 40 µm to 80 µm, or 40 µm to 80 µm. IVIA / t / ZUZÓ / UI UOZ I pm or from 60 pm to 8 0 pm. When subsurface layers are present in multilayer film configurations, the thickness of each subsurface layer of the multilayer films described herein may constitute from 5% to 40% of the total thickness of the multilayer film. In some configurations, each subsurface layer may constitute from 5% to 20% by weight, from 5% to 15%, from 5% to 10%, from 10% to 40%, from 10% to 20%, from 10% to 15%, from 15% to 40%, from 15% to 20%, or from 20% to 40% of the total thickness of the multilayer film. Protective layer In some models, the multilayer film may include a protective layer. The term "protective layer," as used herein, refers to a layer that reduces the diffusion of vapor or gas into and out of the multilayer film. For example, a protective layer may reduce the diffusion of fragrance, water, or oxygen into and out of the multilayer film. In some embodiments, the protective layer may include a polar material. The term "polar material," as used herein, refers to a polymer formed from at least one monomer comprising at least one heteroatom. Examples of heteroatoms include O, N, P, and S. In various embodiments, the polar material may be selected from an ethylene vinyl alcohol (EVOH) polymer. ML / IZ / ZUZO / U aoz I English) (such as Eval H171B marketed by Kuraray) or a combination of EVOH and polyamide (PA) (such as Nylon 6, Nylon 66, and Nylon 6 / 66 marketed by DuPont). In various embodiments, the protective layer consists of ethylene vinyl alcohol (EVOH). In some embodiments, the protective layer does not include polyamide or is substantially free of polyamide. As used herein, substantially free may mean that the protective layer includes less than 1% by weight of polyamide, based on the total weight of the protective layer. In some embodiments, the protective layer may include less than 0.5% by weight or less than 0.1% by weight of polyamide. It is to be understood that, in some embodiments, the protective layer that includes the fleece material may comprise or consist of the fleece material.In embodiments where the layer comprising polar material comprises polar material, the polar material may be blended with any polymer, including polyethylene, such as, for example, LLDPE, LDPE, ULDPE, MDPE, HDPE, and the multimodal polyethylene composition described herein. In various embodiments, the polar material has a melting index (I2) (2.16 kg, 190 °C) of 0.1 g / 10 min to 0.2 g / 10 min to 20 g / 10 min, or 0.5 g / 10 min to 10 g / 10 min. In various embodiments, the polar material has a density of 1.00 g / cm³ to 1.30 g / cm³ or 1.10 g / cm³ to 1.20 g / cm³ (1 cm³ = 1 cc). In different modalities, the protective layer of the films The multilayer film described herein may have a variety of thicknesses. The thickness of the protective layer may depend on several factors, including, for example, the composition of the protective layer, the desired overall recyclability and insulation properties of the multilayer film, and others. In different modalities, the protective layer can have a thickness of 0.1 pm to 20 pm, 0.1 pm to 15 pm, 0.1 pm to 10 pm, 0.1 pm to 5 pm, 0.1 pm to 1 pm, 0.1 pm to 0.5 pm, 0.5 pm to 20 pm, 0.5 pm to 15 pm, 0.5 pm to 10 pm, 0.5 pm to 5 pm, 0.5 pm to 1 pm, 1 pm to 20 pm, 1 pm to 15 pm, 1 pm to 10 pm, 1 pm to 5 pm, 5 pm to 20 pm, 5 pm to 15 pm, 5 pm to 10 pm, 10 pm to 20 pm, 10 pm to 15 pm or 15 pm to 20 pm. The thickness of the protective layer of the multilayer films described herein may constitute from 1% to 10%, from 1% to 8%, from 1% to 6%, from 1% to 4%, from 1% to 2%, from 2% to 10%, from 2% to 8%, from 2% to 6%, from 2% to 4%, from 4% to 10%, from 4% to 8%, from 4% to 6%, from 6% to 10%, from 6% to 8% or from 8% to 0% of the total thickness of the multilayer film. Adhesive layers In some forms, a multilayer film may include one or more adhesive layers. The term adhesive layer, as used herein, refers to a layer that bonds two layers together. For example, an adhesive layer can bond materials ML / IZ / ZUZO / U aoz I polar to one or more layers that do not include polar materials. For example, an adhesive layer can be placed adjacent to a layer comprising a polar material to adhere the layer comprising the polar material to a layer comprising polyethylene. In embodiments, an adhesive layer can be placed adjacent to the protective layer to adhere the protective layer, comprising the polar material, to one or more layers including polyethylene, such as one or more subsurface layers or outer layers. In various embodiments, a wide variety of polymers known to those skilled in the art as useful for bonding a layer comprising polar material (such as, for example, EVOH or polyamide) to layers including polyethylene for the adhesive layers can be used, based on the teachings of the present description. In some embodiments, the adhesive layers may include ethylene and acid copolymers. In one or more embodiments, the adhesive layers may include an anhydride-grafted ethylene / alpha-olefin interpolymer. The term anhydride-grafted ethylene / alpha-olefin interpolymer, as used herein, refers to an ethylene / alpha-olefin interpolymer comprising at least one anhydride group linked by a covalent bond. The anhydride-grafted ethylene / alpha-olefin interpolymer may be an ethylene-based polymer with a monomer of ML / IZ / ZUZO / UOZ I anhydride grafted to this. Suitable ethylene-based polymers for low-melt viscosity maleic anhydride grafted polyolefin include, but are not limited to, polyethylene homopolymers and copolymers with α-olefins, ethylene-vinyl acetate copolymers, and ethylene-one or more alkyl (meth)acrylate copolymers. In specific embodiments, the anhydride-grafted ethylene / α-olefin interpolymer may comprise a linear low-density polyethylene (LLDPE) grafted with maleic anhydride. In one or more embodiments, the anhydride-grafted ethylene / alpha-olefin interpolymer comprises up to 10 wt%, up to 5 wt%, or 1 to 4 wt% of the maleic anhydride graft monomer, based on the total weight of the anhydride-grafted ethylene / alpha-olefin interpolymer. The weight percentage of the ethylene-based polymer is complementary to the amount of maleic anhydride graft monomer, such that the sum of the weight percentages of the ethylene-based polymer and the maleic anhydride graft monomer is 100 wt%. Therefore, the ethylene / alpha-olefin interpolymer grafted with anhydride comprises up to 90 wt%, up to 95 wt%, or 96 to 99 wt%, based on the total weight of the polyolefin grafted with maleic anhydride, of the ethylene-based polymer. Examples of anhydride graft portions may include, but are not limited to, maleic anhydride, citraconic anhydride, 2-methylmaleic anhydride, 2-chloromaleic anhydride, 2,3-dimethylmaleic anhydride, bicyclo[2,2,1]-5-heptene-2,3-dicarboxylic anhydride, 4-methyl-4-cyclohexene-1,2-dicarboxylic anhydride, bicyclo(2.2.2)oct-5-ene-2,3-dicarboxylic acid anhydride, 1-octahydronaphthalene-2,3-dicarboxylic acid anhydride, 2-oxa-1,3-diketoespiro(4.4)non-7-ene, and acid anhydride. bicyclo(2.2.1)hept-5-ene-2,3-dicarboxylic acid, tetrahydrophthalic anhydride, norbom-5-ene-2,3-dicarboxylic acid anhydride, nadic anhydride, methylnadic anhydride, himic anhydride, methylhimic anhydride, and x-methyl-bicyclo(2.2.1)hept-5-ene-2,3-dicarboxylic acid anhydride. In one embodiment, the anhydride graft portion comprises maleic anhydride. In additional embodiments, the anhydride-grafted ethylene / alpha-olefin interpolymer has a density less than 0.940 grams per cubic centimeter (g / cm3) or from 0.855 g / cm3 to 0.940 g / cm3, as measured according to ASTM method no. D792-91. Other density ranges may be 0.855 g / cm3 to 0.900 g / cm3, 0.855 g / cm3 to 0.880 g / cm3, 0.855 g / cm3 to 0.860 g / cm3, 0.860 g / cm3 to 0.940 g / cm3, 0.860 g / cm3 to 0.910 g / cm3, from 0.860 g / cm3 to 0.880 g / cm3, from 0.880 g / cm3 to 0.910 g / cm3 or from 0.880 g / cm3 to 0.900 g / cm3. In one or more embodiments, the anhydride-grafted ethylene / alpha-olefin interpolymer can have a melt index (I2) of 300 grams per 10 minutes (g / 10 min) to 1500 g / 10 min, or from 300 g / 10 min to 1000 g / 10 min, from 500 g / 10 min to 800 g / 10 min, from 500 g / 10 min to 600 g / 10 min, from 600 g / 10 min to 1000 g / 10 min, from 600 g / 10 min to 800 g / 10 min, or from 800 g / 10 min to 1000 g / 10 min, as determined according to ASTM D1238 at 190 °C and 2.16 kg. In one or more embodiments, the anhydride-grafted ethylene / alpha-olefin interpolymer may have a melt viscosity less than 200,000 cP when measured at 177 °C according to the test methods described later in this description. In various embodiments, the anhydride-grafted ethylene / alpha-olefin interpolymer can have a melt viscosity of 2,000 cP to 200,000 cP, 2,000 cP to 100,000 cP, 2,000 cP to 50,000 cP, 2,000 cP to 10,000 cP, 10,000 cP to 200,000 cP, 10,000 cP to 100,000 cP, 10,000 cP to 50,000 cP, 50,000 cP to 200,000 cP, 50,000 cP to 100,000 cP, or 100,000 cP to 200,000 cP when It measures at 177 °C according to the test methods described later in this description. Several commercial forms are considered suitable. For example, anhydride-grafted ethylene / alphaolefin interpolymers may be commercially available through The Dow Chemical Company under the trademark BYNEL® 41E710. MA / t / ZUZÓ / UΊ aoz I Various amounts of ethylene-acid copolymer or anhydride-grafted ethylene / alphaolefin interpolymer are considered suitable within the adhesive layers of the multilayer films described herein. In some embodiments, the adhesive layer may include 20% by weight or less of ethylene-acid copolymer or anhydride-grafted ethylene / alphaolefin interpolymer, based on the total weight of the adhesive layer. In other embodiments, the adhesive layer may include 5% to 15% by weight or 10% to 15% by weight of ethylene-acid copolymer or anhydride-grafted ethylene / alphaolefin interpolymer, based on the total weight of the adhesive layer. The remainder of the adhesive layer may be a polyethylene, such as LDPE, HDPE, MDPE, or the multimodal polyethylene composition described herein. Not limited to theory, it is believed that the anhydride-grafted ethylene / alpha-olefin interpolymer can be positioned adjacent to a layer comprising polar material to bond the polar layer to a non-polar layer. In certain embodiments, an adhesive layer can be positioned in direct contact with a polar layer. In certain embodiments, an adhesive layer can be positioned between, and in direct contact with, a polar layer and a layer comprising the multimodal polyethylene composition described herein. In some models, each adhesive layer of the multilayer films described herein may have a variety of thicknesses. The thickness of each adhesive layer may depend on several factors, including, for example, the adhesive properties of the adhesive layer. In some models, each adhesive layer may have a thickness from 0.1 µm to 20 µm. In different modalities, each adhesive layer can have a thickness of 0.1 pm to 15 pm, 0.1 pm to 10 pm, 0.1 pm to 5 pm, 0.1 pm to 1 pm, 0.1 pm to 0.5 pm, 0.5 pm to 20 pm, 0.5 pm to 15 pm, 0.5 pm to 10 pm, 0.5 pm to 5 pm, 0.5 pm to 1 pm, 1 pm to 20 pm, 1 pm to 15 pm, 1 pm to 10 pm, 1 pm to 5 pm, 5 pm to 20 pm, 5 pm to 15 pm, 5 pm to 10 pm, 10 pm to 20 pm, 10 pm to 15 pm or 15 pm to 20 pm. The thickness of each adhesive layer of the multilayer films described herein may constitute from 1% to 10%, from 1% to 8%, from 1% to 6%, from 1% to 4%, from 1% to 2%, from 2% to 10%, from 2% to 8%, from 2% to 6%, from 2% to 4%, from 4% to 10%, from 4% to 8%, from 4% to 6%, from 6% to 10%, from 6% to 8% or from 8% to 0% of the total thickness of the multilayer film. Methods for producing the films described in this description Various methodologies are considered for producing multilayer films. In one or more of these methods, the manufacturing process for multilayer films may include melt film extrusion or blown film extrusion. In some embodiments, the manufacturing process of multilayer film may include forming a blown film bubble. In some embodiments, the blown film bubble may be a multilayer blown film bubble. Furthermore, according to this embodiment, the multilayer blown film bubble may include at least two, three, five, seven, nine, or more layers, and the layers may be bonded together. During the blown film process, an extruded film is formed (blown) from an extrusion die and pulled by a tower over a clamping point. The film can then be wound onto a core. Before the film is wound onto the core, the film ends can be cut and folded using folding equipment. This can make the film layers difficult to separate, which can be important for mailing applications, in general, or for heavy-duty mailing bag applications. In other embodiments, the blown film bubble can be formed by a blown film extrusion line having a length-to-diameter (L / D) ratio of 30 to 1. In some embodiments, the extrusion line may have a blowing ratio of 1 to 5, 1 to 3, 2 to 5, or 2 to 3. In some embodiments, the extrusion line may use a die with internal bubble cooling. In some embodiments, the die space may be 1 millimeter (mm) to 5 mm, 1 mm to 3 mm, 2 mm to 5 mm, or 2 mm to 3 mm. In some configurations, the extrusion line can use a film thickness calibration scanner. In some configurations, during the extrusion process, the thickness of the multilayer film can be maintained from 15 µm to 115 µm. In other configurations, the thickness of the multilayer film can be maintained from 15 µm to 100 µm, from 15 µm to 75 µm, from 15 µm to 50 µm, from 15 µm to 25 µm, from 25 µm to 115 µm, from 25 µm to 100 µm, from 25 µm to 75 µm, from 25 µm to 50 µm, from 50 µm to 115 µm, from 50 µm to 100 µm, from 50 µm to 75 µm, from 75 µm to 115 µm, from 75 µm to 100 µm, or from 100 µm to 115 µm. In some modalities, the multilayer blown film bubble formation stage can occur at a temperature of 350 to 500 °F, or 375 to 475 °F. The output speed can be from 5 Ib / h / in to 25 Ib / h / in, from 5 Ib / h / in to 20 Ib / h / in, from 5 Ib / h / in to 15 Ib / h / in, from 5 Ib / h / in to 10 Ib / h / in, from 10 Ib / h / in to 25 Ib / h / in, from 10 Ib / h / in to 20 Ib / h / in, from 10 Ib / h / in to 15 Ib / h / in, from 15 Ib / h / in to 25 Ib / h / in, from 15 Ib / h / in to 20 Ib / h / in or from 20 Ib / h / in to 25 Ib / h / in. Articles The forms described herein also relate to articles, such as containers, formed from the multilayer films described herein. Such containers ML / IZ / ZUZ / UOZ I can be formed with any of the multilayer films described herein. The multilayer films described herein are particularly useful in articles where good piercing properties are desired. Examples of such items may include flexible packaging, pouch bags, pouch bags with a base, and pre-made pouch bags or containers. Experts in the technique would be familiar with various methods for producing article modalities from the multilayer films described in the present description. Testing methods Testing methods include the following: fusion index The melting indices I2 (or 12) and lio (or 110) of polymer samples were measured according to ASTM D-1238 (Method B) at 190 °C and loadings of 2.16 kg and 10 kg, respectively. Their values ​​are reported in g / 10 min. Fractions of the polymer samples were measured by collecting the polymer product from the reactor that produces that specific fraction or portion of the polymer composition. For example, the first polyethylene fraction can be collected from the reactor that produces the low-density, higher-molecular-weight component of the polymer composition. The polymer solution is vacuum-dried before measuring the melting index. Density Samples for density measurement were prepared in accordance with ASTM D4703. Measurements were performed in accordance with ASTM D792, Method B, within one hour of sample pressing. ASTM D1709, dart drop The dart drop test on film determines the energy required to cause a plastic film to fail under specified impact conditions with a free-falling dart. The test result is the energy, expressed in terms of the weight of the dart falling from a specified height, that would cause 50% of the tested samples to fail. After the film was produced, it was conditioned for at least 40 hours at 23°C (+ / - 2°C) and 50% RH (+ / - 5), in accordance with ASTM standards. The standard test conditions are 23°C (+ / - 2°C) and 50% RH (+ / - 5), in accordance with ASTM standards. The test result is reported using Method B, which employs a 2-inch diameter dart head and a 60-inch drop height. The sample thickness is measured at the sample center, and the sample is then held in place by an annular sample holder with an inside diameter of 12.7 cm (5 inches). The dart is loaded above the sample center. ΜΛ / ΙΖ / ΖυΖΟ / υΊ aoz I and is released by a pneumatic or electromagnetic mechanism. The test is conducted using the step-down method. If the sample fails, the test is performed with a new sample with the dart weight reduced by a known and fixed amount. If the sample does not fail, the test is performed with a new sample with the dart weight increased by a known amount. After 20 samples have been evaluated, the number of failures is determined. If this number is 10, then the test is complete. If the number is less than 10, then the test continues until 10 failures are recorded. If the number is greater than 10, the test continues until a total of 10 failure-free cases are reached. Dart drop resistance is determined from this data according to ASTM D1709 and is expressed in grams as the Type B dart drop impact. Impact from instrumented dart The instrumented dart impact method is measured according to ASTM D7192 on plastic film samples using an Instron CEAST 9350 impact tester. The test is performed with a 12.7 mm diameter impact cell with a 75 mm diameter clamping assembly and a hemispherical head with rubber-coated grips. The instrument is equipped with an environmental chamber for testing at low or high temperatures. The typical sample size is 125 mm x 125 mm. The standard test speed is 200 m / min. The film thickness is 2 mil. Method for measuring viscosity at zero shear using flow Zero-shear viscosities were obtained by creep tests performed on an AR-G2 controlled-stress rheometer (TA Instruments; Newcastle, DEL) with parallel 25-mm diameter plates at 190 °C. The rheometer oven was set to the test temperature for at least 30 minutes before zeroing the fixtures. At the test temperature, a compression-molded sample disc was inserted between the plates and allowed to equilibrate for 5 minutes. The top plate was then lowered to 50 µm above the desired test gap (1.5 mm). The excess material was trimmed, and the top plate was lowered to the desired gap. Measurements were performed under nitrogen purging at a flow rate of 5 L / min. The predetermined creep time was set to 2 hours. A constant low shear stress of 20 Pa is applied to all samples to ensure that the steady-state shear rate is sufficiently low to be in the Newtonian region. For the samples in this study, the resulting steady-state shear rates are in the range of 10⁻³ to 10⁻⁴ s⁻¹. The steady state is determined by performing a linear regression on all data in the last time window of The yield strain is calculated as the percentage of the linear regression slope of the graph of log(J(t)) vs. log(t), where J(t) is the yield strain and t is the yield time. If the slope of the linear regression is greater than 0.97, steady state is considered to have been reached, and the yield test is then stopped. In all cases in this study, the slope meets the criterion within 2 hours. The steady-state shear rate is determined from the slope of the linear regression of all data points in the last 10% time window of the graph of ε vs. t, where ε is the strain. The zero-shear viscosity is determined from the ratio of the applied stress to the steady-state shear rate. To determine if the sample degrades during the flow test, a small-amplitude oscillatory shear test is performed before and after the flow test on the same sample at 0.1 to 100 rad / s. The complex viscosity values ​​from the two tests are compared. If the difference in viscosity values ​​at 0.1 rad / s is greater than 5%, the sample is considered to have degraded during the flow test, and the result is discarded. Gel permeation chromatography (GPC) The chromatographic system consisted of a PolymerChar (Valencia, Spain) high-temperature GPC-IR chromatograph equipped with an internal IR5 infrared detector (IR5). IVIA / t / ZUZÓ / U 1 UOZ I The autosampler oven compartment was set to 160° Celsius and the column compartment to 150° Celsius. The columns used were four 30-cm Agilent Mixed A linear mixed-bed columns with a 20-µm thickness and one 20-µm pre-column. The chromatographic solvent used was 1,2,4-trichlorobenzene containing 200 ppm butylated hydroxytoluene (BHT). The solvent source was sprayed with nitrogen. The injection volume was 200 microliters, and the flow rate was 1.0 milliliter / minute. The calibration of the GPC column array was performed using 21 narrow molecular weight distribution polystyrene standards with molecular weights ranging from 580 to 8,400,000. These standards were arranged in six cocktail mixtures with at least a decade's separation between individual molecular weights. The standards were purchased from Agilent Technologies. The polystyrene standards were prepared at a ratio of 0.025 grams in 50 milliliters of solvent for molecular weights equal to or greater than 1,000,000, and 0.05 grams in 50 milliliters of solvent for molecular weights less than 1,000,000. The polystyrene standards were dissolved at 80 degrees Celsius with gentle stirring for 30 minutes. The maximum molecular weights of the polyethylene standard were converted to polyethylene molecular weights using Equation 1 (as described in Williams and Ward, J. Polym. ML / IZ / ZUZO / U aoz I Sci., Polym. Let., 6, 621 (1968)).: ^polyethylene ~ AX (Mp0uest:iren0) (EC. 1) IVIA / t / ZUZÓ / UΊ aoz I where M is the molecular weight, A has a value of 0.4315 and B is equal to 1.0. A fifth-order polynomial was used to adjust the respective polyethylene-equivalent calibration points. To correct for column resolution and band-broadening effects in order to obtain the linear polyethylene homopolymer standard at an Mw of 120,000, a small adjustment to A (from approximately 0.375 to 0.445) was made. The total plate count of the GPC column array was performed using decane (prepared at a rate of 0.04 g in 50 mL of TCB and dissolved for 20 minutes with gentle stirring). The plate count (Equation 2) and symmetry (Equation 3) were measured in a 200-microliter injection according to the following equations: (\2 -----(RVmaxvic°------) (EC . 2 ) Peak width to height J where RV is the retention volume in milliliters, peak width is in milliliters, peak maximum is the maximum peak height and height is the peak maximum height. n. z (Rear peak RVurldécimo of height-RVMax.of peak') Symmetry - --------------.-------:----------------£—¿(EC. 3) (R^Peak Max~PlC0anterior RV1 / 10 of height) where RV is the retention volume in milliliters and the peak width is in milliliters, peak max is the maximum position of the peak, 1 / 10 of height is 1 / 10 of the peak max height, and where trailing peak refers to the tail of the peak at retention volumes after the peak max and where leading peak refers to the front of the peak at retention volumes before the peak max. The plate count for the chromatographic system must be greater than 18,000 and the symmetry must be between 0.98 and 1.22. The samples were prepared semi-automatically using PolymerChar's Instrument Control software, where the target sample weight was 2 mg / ml and the solvent (containing 200 ppm of BHT) was added to a septum-capped vial previously sprayed with nitrogen, using PolymerChar's high-temperature autosampler. The samples were dissolved for 2 hours at 160° Celsius with low-speed stirring. Mn calculations <GPC), Mwjgpo y Mz <gpc) se basaron en los resultados de GPC mediante el detector interno IR5 (canal de medición) del cromatógrafo GPC-IR de PolymerChar de acuerdo con las Ecuaciones 4-6, mediante el software PolymerChar GPCOne™, el cromatograma de IR en el que se restó la línea de base en cada punto de recolección de datos (i) igualmente espaciado, y el peso molecular equivalente de polietileno obtenido de la curva de calibración estrecha de estándares para el punto (i) de la Ecuación 1. Σ'*. Mn(GPC) —IR' / / / tv'polyethylene¡y(EC. 4) i / X Polyethylene ¡ / Mw(GPC) =-------:---------(EC. 5) ΜΛ / ΙΖ / ΖυΖΟ / υΊ UOZ I Σ * ^polyethylene¡ Mz(gpc) — —--------------Σ', * ^polyethylene ¡ (EC. 6) To monitor deviations over time, a flow rate marker (decane) was introduced into each sample using a micropump controlled by the PolymerChar GPC-IR system. This flow rate marker (FM) was used to linearly correct the pump flow rate (Flow Rate (nominal)) for each sample by aligning the RV of the respective decane peak within the sample (RV (FM sample)) with that of the decane peak within the narrow calibration of standards (RV (FM calibrated)). It was assumed that any change over time in the decane marker peak corresponded to a linear change in the flow rate (Flow Rate (effective)) throughout the entire run.To facilitate maximum accuracy in a flow marker peak RV measurement, a least-squares fitting routine is used to fit the flow marker concentration chromatogram peak to a quadratic equation. The first derivative of the quadratic equation is then used to determine the true peak position. After calibrating the system based on a flow marker peak, the effective flow rate (with respect to the tight calibration of standards) is calculated as Equation 7. Flow marker peak processing was performed using PolymerChar's GPCONe™ software. The acceptable flow rate correction is such that the effective flow rate must be within + / -0.5% of the nominal flow rate. Effective flow rate = Nominal flow rate * (RV(FM calibrated) / RV(FM sample)) (Eq. 7) Improved method for comonomer content analysis (iCCD) In 2015, an improved method for comonomer content analysis (iCCD) was developed (Cong and Parrott et al., W02017040127A1). The iCCD assay was performed using crystallization elution fractionation (CEF) instrumentation (PolymerChar, Spain) equipped with an IR-5 detector (PolymerChar, Spain) and a model 2040 dual-angle light scattering detector (Precisión Detectors, IVIA / t / ZUZÓ / UΊ aoz I (currently Agilent Technologies). A 20-27 micrometer glass-filled shielding column (MoSCi Corporation, USA) was installed in a 5 cm or 10 cm (length) x 1 / 4 in (ID) stainless steel tube just before the IR-5 detector in the detector furnace. Ortho-dichlorobenzene (ODCB, 99% anhydrous or technical grade) was used. Silica gel 40 (particle size 0.2–0.5 mm, catalog number 10181-3) was obtained from EMD Chemicals (it can be used to dry the ODCB solvent beforehand). The CEF instrument is equipped with an autosampler with N2 purge capability. The ODCB is sprayed with dry nitrogen (N2) for one hour before use. Sample preparation was performed using an autosampler at 4 mg / ml (unless otherwise specified) with shaking at 160 °C for 1 hour. The injection volume was 300 pL.The iCCD temperature profile was: crystallization at 3 °C / min from 105 °C to 30 °C, thermal equilibrium at 30 °C for 2 minutes (including the 2-minute elution time of the soluble fraction), and elution at 3 °C / min from 30 °C to 140 °C. The flow rate during crystallization was 0.0 mL / min. The flow rate during elution was 0.50 mL / min. Data were collected at a rate of one data point per second. The iCCD column was packed with gold-coated nickel particles (Bright 7GNM8-N1S, Nippon Chemical Industrial Co.) in a 15 cm (length) x stainless steel tube MA / t / ZUZÓ / U 1 UOZ I 1 / 4 (DI). The column packing and conditioning were done using a suspension method according to the reference (Gong, R; Parrott, A.; Hollis, C.; Cheatham, M. WO2017040127A1). The final pressure with the TCB suspension packing was 150 bar. The column temperature calibration was performed using a mixture of the linear polyethylene homopolymer of the reference material (which has a comonomer content of zero, a melting index (I) of 1.0, and a polydispersity M„ / MΓ of approximately 2.6 by conventional gel permeation chromatography, 1.0 mg / ml) and eicosane (2 mg / ml) in ODCB. The iCCD temperature calibration consisted of four steps: (1) calculating the lag volume, defined as the temperature shift between the measured peak elution temperature of eicosane and 30.00 °C; (2) subtracting the temperature shift from the elution temperature of the raw iCCD temperature data. This temperature shift is a function of experimental conditions, such as the elution temperature and elution flow rate; (3) creating a linear calibration line that transforms the elution temperature over a 30.00 °C interval. and 140.00 °C so that the linear polyethylene homopolymer reference has a peak temperature at 101.0 °C, and eicosane has a peak temperature of 30.0 °C; (4) For the soluble fraction measured isothermally at 30 °C, the elution temperature below 30.0 °C is extrapolated linearly using the elution heating rate of 3 °C / min according to the reference (Cerk and Gong et al., US 9,688,795). Comonomer content versus iCCD elution temperature was plotted using 12 reference materials (an ethylene homopolymer and a random ethylene-octene copolymer fabricated with a single-site metallocene catalyst, with average molecular weights in ethylene equivalents ranging from 35,000 to 128,000). All of these reference materials were analyzed as previously specified at 4 mg / mL. The reported peak elution temperatures were linearly fitted to the linear equation y = -6.3515x + 101.00, where y represented the iCCD elution temperature and x represented the mol% octene, and R² was 0.978. The molecular weight of the polymer and the molecular weight of the polymer fractions were determined directly from the LS detector (90-degree angle) and the concentration detector (IR-5) according to the Rayleigh-Gans-Debys approximation (Striegel and Yau, Modern Size Exclusion Liquid Chromatogram, page 242 and page 263) by assuming a shape factor of 1 and all virial coefficients equal to zero. The integration windows are configured to integrate all chromatograms within the temperature range of ΜΛ / ΙΖ / ΖυΖΟ / υΊ aoz I elution (temperature calibration was specified above) from 23.0 to 120 °C. The calculation of molecular weight (Mw) from iCCD includes the following four steps: (1) Interdetector displacement measurement. The displacement is defined as the geometric volume displacement between the LS detector and the concentration detector. It is calculated as the difference in the elution volume (mi) of the polymer peak between the concentration detector and the LS chromatograms. It is converted to temperature compensation using the thermal elution rate and the elution flow rate. A linear high-density polyethylene is used (having zero comonomer content, a melting index (I2) of 1.0, and a polydispersity Mw / Mnde of approximately 2.6 by conventional gel permeation chromatography).The same experimental conditions as the standard iCCD method described above are used, except for the following parameters: crystallization at a rate of 10 °C / min from 140 °C to 137 °C, thermal equilibrium at 137 °C for 1 minute as the elution time of the soluble fraction, soluble fraction (SE) elution time of 7 minutes, and elution at 3 °C / min from 137 °C to 142 °C. The flow rate during crystallization is 0.0 mL / min. The flow rate during elution is 0.80 mL / min. The sample concentration is 1.0 mg / mL. IVIA / t / ZUZÓ / UI UOZ I (2) Each LS data point in the LS chromatogram is changed to correct for interdetector offset before integration. (3) The LS chromatograms with the baseline subtracted and concentration are integrated over the entire elution temperature range of step (1). The MW detector constant is calculated using a known MW HDPE sample in the range of 100,000 to 140,000 Mw and the area ratio of the integrated LS and concentration signals. (4) The MW of the polymer was calculated using the ratio between the integrated light scattering detector (90-degree angle) and the concentration detector and using the MW detector constant. The half-width calculation is defined as the temperature difference between the front temperature and the rear temperature at half the maximum peak height; the front temperature at half the maximum peak is looked up from 35.0 °C, while the rear temperature at half the maximum peak is looked up from 119.0 °C. Zero Shear Viscosity Ratio (ZSVR) ZSVR is defined as the ratio of the zero shear viscosity (ZSV) of the branched polyethylene material to the ZSV of the linear polyethylene material at the weight average molecular weight equivalent (Mw-gpc) according to the following Equations (EC) 8 and 9: ZSVR = ^(Eq. 8) ^-2.29x10(Eq.9) The ZSV value is obtained from the creep test at 190 °C using the method described above. The Mw-gpc value is determined using the conventional GPC method (Equation 5 in the description of the conventional GPC method). The correlation between the ZSV of linear polyethylene and its Mw-gpc was established based on a series of linear polyethylene reference materials. A description of the ZSV-Mw relationship can be found in the ANTEC proceedings: Karjala, Teresa P., Sammler, Robert L., Mangnus, Marc A., Hazlitt, Lonnie G., Johnson, Mark S., Hagen, Charles M. Jr., Huang, Joe W.L., Reichek, Kenneth N., Detection of low levels of long-chain branching in polyolefins, Annual Technical Conference Society of Plastics Engineers (2008), 66th, 887–891. MD Tear The MD tear was measured in accordance with ASTM D-1922. The force in grams required to propagate the tear through a film sample is measured using an Elmendorf tear tester. Acting by gravity, the pendulum swings through an arc, tearing the sample from a pre-cut slit. The tear propagates in the transverse direction. Samples are conditioned for a minimum of 40 hours at room temperature prior to testing. Dynamic rheological analysis To characterize the rheological behavior of substantially linear ethylene polymers, S Lai and GW Knight introduced (ANTEC '93 Proceedings, Insite (TM) Technology Polyolefins (ITP)-New Rules in the Structure / Rheology Relationship of Ethylene-10Efin Copolymers, New Orleans, LA, May 1993) a new rheological measurement, the Dow Rheology Index (DRI), which expresses the normalized relaxation time of a polymer as a result of long-chain branching.Lai et al; (ANTEC '94, Dow Rheology Index (DRI) for Insite(TM) Technology Polyolefins (ITP): Unique Structure Processing Relationships, pages 1814-1815) defined the DRI as the extent to which the rheology of ethyleneoctene copolymers known as ITP (Dow's Insite Technology Polyolefins) incorporating long-chain branching in the polymer backbone deviates from the rheology of conventional linear homogeneous polyolefins that reportedly do not have long-chain branching (LCB) according to the following normalized equation:. DRI = [3650000 X (το / ηο) - 1] / 10 (Eq. 10) where το is the characteristic relaxation time of the material and η is the zero shear rate complex viscosity of the material. The DRI is calculated by least squares fitting of the rheological curve (complex dynamic viscosity η* (ω) versus applied frequency (ω) , e.g., 0.01 - 100 rads / s) as described in U.S. Patent No. 6,114,486 with the following generalized cross equation, i.e., η* (ω) = ηο / [1+ (ω τ0)η] (Eq. 11) where n is the power law index of the material, η* (ω) and ω are the measured complex viscosity and applied frequency data, respectively. Dynamic rheological measurements were performed, according to ASTM D4440, on a dynamic rheometer (e.g., the TA Instruments ARES rheometer) with 25 mm diameter parallel plates in dynamic mode and an inert atmosphere. For all experiments, the rheometer was thermally stable at 190 °C for at least 30 minutes before inserting the appropriately stabilized (with antioxidant additives) and compression-molded sample into the parallel plates. The plates were then closed with a positive normal force recorded on the meter to ensure good contact. After approximately 5 minutes at 190 °C, the plates were lightly compressed, and excess polymer was trimmed from the circumference of the plates. A further 10 minutes were allowed for thermal stability to occur and for the normal force to decrease back to zero. ML / IZ / ZUZO / UZ yoz I 100 All measurements are carried out after the samples have been equilibrated at 190 °C for approximately 15 minutes and are performed under full nitrogen cover. Initially, two strain sweep (SS) experiments are performed at 190 °C to determine the linear viscoelastic strain that would generate a torque signal greater than 10% of the transducer's lower scale across the entire frequency range (e.g., 0.01 to 100 rad / s). The first SS experiment is performed with a low applied frequency of 0.1 rad / s. This test is used to determine the low-frequency torque sensitivity. The second SS experiment is performed with a high applied frequency of 100 rad / s. This ensures that the selected applied stress is well within the linear viscoelastic region of the polymer, so that oscillatory rheological measurements do not induce structural changes in the polymer during the test. Additionally, a time sweep (TS) experiment is performed with a low applied frequency of 0.1 rad / s at the selected voltage (as determined by SS experiments) to verify the stability of the sample during the test. The values ​​of storage modulus (or elastic modulus), loss modulus (or viscous modulus) (G), complex modulus (G*), complex viscosity (η*) and tan δ (the ratio of the modulus of ML / IZ / ZUZO / U aoz I 101 loss and storage module, G'VG') were obtained as a function of frequency (ω) at a given temperature (e.g., 190 °C). Elmendorf type B tear in MD (machine direction) and CD (transverse direction) according to ASTM D1922 The Elmendorf tear test determines the average force required to propagate tearing through a specified length of a plastic film or non-rigid laminate, after tearing has begun, using an Elmendorf-type tear tester. After the film was produced from the sample to be evaluated, it was conditioned for at least 40 hours at 23 °C (+ / - 2 °C) and 50% RH (+ / - 5), in accordance with ASTM standards. The standard test conditions were 23 °C (+ / - 2 °C) and 50% RH (+ / - 5), in accordance with ASTM standards. The force, in grams, required to propagate tearing through a film or laminate sample was measured using a precisely calibrated pendulum device. In the test, acting under gravity, the pendulum swung across an arc, tearing the sample along a pre-cut slit. The sample was held on one side by the pendulum and on the other by a stationary member. Energy loss by the pendulum was indicated by a pointer or an electronic balance. The balance reading was a ML / IZ / ZUZO / U aoz I 102 function of the force required to tear the sample. The sample geometry used in the Elmendorf tear test was the constant radius geometry, as specified in ASTM D1922. The test is generally performed on samples that have been cut in both the MD and CD directions of the film. Before the test, the thickness of the film sample was measured at the sampling center. A total of 15 samples were evaluated per film direction, and the average tear strength and average thickness were reported. The average tear strength was normalized to the average thickness. ASTM D882 MD and CD, secant modulus at 1% and 2% The secant modulus of the MD (machine direction) and CD (cross direction) of the film was determined according to ASTM D882. The reported secant modulus value was the average of five measurements. Puncture resistance The puncture test determines a film's resistance to penetration by a probe at a standard low speed, a single test speed. The puncture test method is based on ASTM D5748. After film production, the film was conditioned for at least 40 hours at 23°C (±2°C) and 50% RH (±5%), in accordance with ASTM standards. The standard test conditions are 23°C (±2°C) and 50% RH (±5%), in accordance with the ML / IZ / ZUZO / U aoz I 103 ASTM standards. Puncture was measured on a tensile testing machine. Square specimens were cut from sheet to a size of 15.24 cm by 15.24 cm (6 in. by 6 in.). The specimen was clamped in a circular specimen holder 10.16 cm (4 in. diameter), and a puncture probe was pushed toward the center of the clamped film at a crosshead speed of 25.40 cm / min (10 in. / min). The internal test method is based on ASTM D5748, with one modification. It deviated from the ASTM D5748 method in that the probe used was a polished steel ball 1.27 cm (0.5 in.) in diameter on a support rod 0.63 cm (0.25 in.) (instead of the pear-shaped probe 1.9 cm (0.75 in.) in diameter specified in D5748). There was a maximum travel length of 19.56 cm (7.7 in) to avoid damage to the test device. There was no calibration length; before the test, the probe was as close as possible to, but not touching, the sample. A single thickness measurement was taken at the center of the sample. For each sample, the maximum force, breaking force, penetration distance, and breaking energy were determined. A total of five samples were evaluated to determine the average penetration value. The drilling probe was cleaned with a Kim-wipe after each MA / t / ZUZÓ / UΊ aoz I sample. 104 Examples The following examples illustrate features of this description, but are not intended to limit its scope. The following experiments analyzed the performance of the modalities of the multimodal polyethylene compositions described herein. Example 1: Preparation of the Multimodal Polyethylene Compositions 1 The Multimodal Polyethylene Composition 1, which is described according to one or more of the detailed description modalities, was prepared using a method that used the catalysts and reactors described below. A bimodal ethylene-1-octene copolymer sample was produced using a liquid complete solution polymerization process in a double reactor in series configuration, as shown in Figure 2. For the production of this sample, the first reactor was a continuously stirred tank reactor (CSTR), and the second reactor was a loop reactor (LR). The feed to each reactor comprised recycled solvent (consisting of Isopar E, ethylene, 1-octene, and hydrogen) as well as fresh ethylene, 1-octene, and hydrogen. The recycled solvent, ethylene, and 1-octene were measured using industry-standard Coriolis measurement technology, and the hydrogen flow rate was measured using a standard thermal mass flow meter. 105. Industry. Standard industry-standard rising-stem plug valves were used to control the flow rate of each reactor feed component. A proprietary digital control system (DCS) automatically manipulated the position of each rising-stem plug valve to control the mass flow of each reactant to its target value. The recycled solvent pressure was supplied to each reactor using industry-standard single positive displacement pump technology. The recycled solvent flow rate to each reactor was measured to maintain the Isopar E to polymer production ratio indicated in the table below. Ethylene pressure was supplied using industry-standard gas compressor technology. A single compressor was used to supply ethylene to both reactors. The ethylene flow rate to each reactor was measured to maintain the Isopar E to ethylene production ratio indicated in the table below. The ethylene was combined with the recycled solvent downstream of the recycled solvent flow meter and the 1-octene injection point. The 1-octene pressure was supplied using industry-standard positive displacement pump technology.The flow of 1-octene to the reactor system was measured to maintain the 1-octene to ethylene ratio indicated in Table 1 below. All of the ML / IZ / ZUZ / UOZ I 106. Fresh 1-octene was injected into the first reactor feed downstream of the recycle solvent metering system. No fresh 1-octene was injected with the second reactor feed. Hydrogen was supplied from 105.46 kg / cm² (1,500 psig) gas cylinders. The target hydrogen-to-production ratio for each reactor was automatically manipulated by the DCS to maintain the respective reactor solution viscosity at the target. The target hydrogen-to-production ratio was converted to hydrogen flow rate, and the DCS manipulated the rising stem plug valve position to control the flow at the target value. The target hydrogen-to-production ratio and solution viscosity targets for each reactor are shown in the table below. The hydrogen was combined with ethylene gas downstream of the ethylene flow controller.For the first reactor, the combined gas stream was mixed with the combined liquid stream downstream of the 1-octene injection point in the recycling solvent, and for the second reactor, the combined gas stream was combined with the combined liquid stream downstream of the recycling solvent flow controller. The combined feed streams for each reactor were routed through heat exchanger systems 107 separate heat exchangers were used to cool the stream to the target feed temperatures indicated in the table below. From the heat exchanger systems, the flow was directed to each reactor where it was injected into the polymerization liquor. The feed pressure was not directly controlled. The control point was the reactor pressure. Therefore, the measured feed pressure was a result of the pressure drop in the feed system for the given total flow rate. The pressure required to inject each catalyst component into each reactor was delivered using industry-standard positive displacement pump technology. Flow was measured using Coriolis flow meters. Each component was pumped and measured separately. The catalyst complex was injected into the reactor separate from the cocatalysts. Cocatalyst 2 (MMAO) was combined with Cocatalyst 1 downstream of Cocatalyst 1's flow meter, and the combined stream was injected into the reactor through a second injector. As a result of this configuration, the catalyst complex in each reactor was activated in the polymerization solution. The flow of the catalyst complex to each reactor was manipulated using the DCS to control the ethylene conversion to the value indicated in Table 1 below. The flows to Cocatalyzer 1 and Cocatalyzer 2 were ML / IZ / ZUZO / U aoz I 108 were manipulated to maintain a constant molar ratio of each component with respect to the catalyst, and these values ​​are also shown in the table. As a result, controlling the target cocatalyst-to-catalyst ratios led to automatic adjustment of the flow rate of each component for each adjustment of the catalyst complex flow rate. The conversion of 1-octene was not directly controlled. Instead, it resulted from the selected catalyst complex and its relative reactivity of ethylene to 1-octene for the reference ethylene conversion value and the selected reactor temperature, as shown in the table. In addition to the recycle and fresh feed injected into the second reactor, unreacted ethylene, 1-octene, and hydrogen in the effluent from the first reactor were injected into the second reactor. The viscosity of the solution was not measured directly. Instead, the friction pressure drop was measured, and the Fanning equation was used to calculate the viscosity of the polymer solution. To calculate the viscosity, the tube dimensions, total mass flow rate, density, and pressure drop across the tube of known dimensions (internal diameter, surface roughness, and length) must be known. An industry-standard Coriolis flow meter was used to measure both the mass flow rate and density of the reactor effluent. A pressure transmitter was also used. 109. An industry-standard diaphragm-style differential was used to measure the pressure drop across the tube of known dimensions. Viscosity was then calculated by inserting these measurements into the rearranged Fanning equation to solve for viscosity according to the following equations: L dP - 4fp~—— '0 2 < / cl44 / =Γ(13) fíe =p—(14) μ (Ibsm / ft - s) =28Mp^p27(15) donde μ = viscosidad (Ibsm / pies-s) , dP = caída de presión de fricción (psi), d = diámetro interior del tubo (pies), f = factor de fricción de Fanning, p = densidad (libras / pie3) , v — velocidad (pies / s) , 1 = longitud del tubo (pies) y ge = conversión unitaria (lbsm-pie / lbsf-s2). For each reactor, the DCS manipulated the hydrogen-to-production ratio and converted it into a target hydrogen flow to control the solution viscosity within the targets indicated in Table 1. Multimodal polyethylene composition 1 was prepared using a bis-biphenylphenoxy catalyst as described above. The bis-biphenylphenoxy catalyst complex with the structure described and shown above can be activated by combination 110 with one or more cocatalysts, for example, a cation-forming cocatalyst, a strong Lewis acid, or a combination thereof. Suitable activation cocatalysts include polymeric or oligomeric aluminoxanes, especially methyl aluminoxane, as well as inert, compatible, non-coordinating, and ion-forming compounds. Illustrative suitable cocatalysts include, but are not limited to: modified methyl aluminoxane (MMAO), bis(hydrogenated tallow alkyl)methyl tetrakis(pentafluorophenyl)borate(l<->)amine (i.e., [HNMe(C18H37)2][B(CeFs)4]), and combinations thereof. Two different bis-biphenylphenoxy catalyst complexes were used to produce Multimodal Polyethylene Composition 1. Catalyst A was used to produce the first reactor fraction, while Catalyst B was used to produce the second reactor fraction. Both catalysts contained a hafnium (M) metal center, and their structures are shown below. ML / IZ / ZUZO / U aoz I 111 Catalyst A Catalyst B The catalysts were activated by contacting the metal-ligand complex with the activating cocatalysts bis(hydrogenated tallow alkyl)methyl tetrakis(pentafluorophenyl)borate (l<->)amine (Cocatalyst 1) and MMAO (Cocatalyst 2) and their structures as shown below: Cocatator 1 Cocatator 2 For the first reactor, the exothermic heat of polymerization was removed by adiabatically raising the temperature of the feed solvent and reactants to the reactor temperature. For the second reactor, a portion of the heat was also removed by adiabatically raising the temperature of the feed reactants and solvent to the reactor temperature. The remaining heat of polymerization was removed non-adiabatically from the second reactor using heat exchangers within the loop reactor. The target temperatures for each reactor are shown in the table below. 112 Polymer splitting is defined as the weight percentage of polymer produced in each reactor. Polymer splitting was not directly controlled during the preparation of Multimodal Polyethylene Composition 1. Instead, the target polymer splitting was achieved by controlling the feed rate of the reagents and the ethylene conversion for each reactor to the targets indicated in Table 1. Along with the selected catalyst complex and its ethylene-to-1-octene reactivity ratio, these factors determine the amount of polymer produced and the density of that fraction. Minor adjustments were made to the 1-octene to ethylene ratio to ensure the overall polymer density was within the target range shown in the table below. To decrease the polymer density, the 1-octene to ethylene ratio was increased, resulting in a higher flow of 1-octene to the reactor. To decrease the polymer density, the 1-octene to ethylene ratio was reduced, resulting in a lower flow of 1-octene to the reactor. As mentioned previously, the polymer viscosity was controlled by manipulating the hydrogen-to-polymer ratio. To reduce the polymer viscosity, the hydrogen-to-polymer ratio was increased, resulting in a higher hydrogen flow to the reactor. To decrease the viscosity of the 113 polymer, the ratio of hydrogen to polymer was reduced, resulting in a lower flow of hydrogen to the reactor. Water was injected into the reactor effluent to terminate the polymerization reaction. A stoichiometric amount of water relative to the sum total of the three catalyst components is sufficient to neutralize the catalyst and terminate the activity, but a molar excess of 20% or greater was used to ensure complete hydrolysis and deactivation of the catalyst. Antioxidant was injected into the reactor effluent to protect the polymer from oxidation during the devolatilization portion of the plant, as well as during storage and subsequent processing at the converter facility. The antioxidant container for each run was mixed with solvent in a mechanically stirred vessel. An industry-standard positive displacement pump was used to provide the delivery pressure for injecting the slurry container into the reactor effluent. The flow rate was measured, using Coriolis technology, at a rate that produced the antioxidant concentrations in the polymer indicated in the table below. After the reaction was complete and the protective antioxidant packaging was added, steam flowed through a heat exchanger to increase the temperature of the ML / IZ / ZUZ / UOZ I 114 stream in preparation for polymer separation. A rising stem plug valve, located downstream of the heat exchanger, was automatically operated (by the DCS) to control the pressure of the liquid-filled reactor system to the value indicated in the table below. After passing through the reactor pressure control valve, the solvent and unreacted ethylene, 1-octene, and hydrogen were separated from the polymer using standard solution polymerization / devolatilization technology. After separating the volatile components from the non-volatile ethylene-l-octene copolymer in the devolatilization system, the mass flow rate of the stream was measured using standard Coriolis flow measurement technology. Conventional gas chromatography technology was used to measure the composition of the polymer-free stream. This stream data was used with the feed flow data to calculate the conversion of ethylene and l-octene, as shown in the following equations: Ethylene conversion = 100 * (Ethylene flow to reactor - Ethylene flow leaving reactor) -------------------------------------------------- (lo) Ethylene flow to reactor 1-octene conversion (Octene flow to reactor - Octene flow leaving reactor) - 100 *-------------------—— ;---------;-------------------------Octene flow to reactor (17) 115 ASTM D4703 was used to prepare a polymer plate for density analysis. ASTM D792 was used to measure the density of each polymer sample listed in the table below. ASTM D1238 was used to measure the polymer melt index and melt flux ratio (Io / I2). The density and melt index values ​​for Reactor 1 and Reactor 2 are model estimates. The overall density, melt index, and melt flux ratio are measured values ​​of the bimodal polymer. Table 1. Reaction conditions to produce polyethylene composition 1. Parameter Units 1st reactor 2nd reactor General Feed temperature °C 10 35 Isopar E / Polymer lb. / lb 5.6 2.8 Isopar Ethylene lb. / lb 5.5 2.8 1-Octene / Ethylene lb. / lb 0.39 Hydrogen / Polymer Grams / ton 403 1,152 Reactor temperature °C 180 195 Reactor pressure Psig (x0.07=Kg / cm2) 575 575 Catalyst type — Catalyst A Catalyst B Catalyst metal — Hafnium Hafnium Cocatalyst type 1 — Cocatalyst-1 Cocatalyst-1 Cocatalyst type 2 — MMAO MMAO Ethylene conversion % by weight 82.4 81.1 89.4 1-Octene conversion % by weight 37.2 2.1 50.6 116 Solution viscosity cP 2,900 1,300 Polymer division % by weight 53 47 100 Catalyst efficiency MMIb. of polymer / lb of Hf 0.5 1.7 0.8 Cocatalyst 1 / Catalyst mol of Cocat 1 / mol of Hf 6.0 2.5 Cocatalyst 2 / Catalyst mol Al / mol Hf 1.4 40.0 Polymer density g / cc 0.8980* 0.9421* 0.9180 Polymer melt index dg / min 0.07* 2.45* 0.24 Polymer melt flow ratio — 8.55 Irgafos 168 in polymer ppmw 1,000 Irganox 1076 in poly ppmw 250 Irganox 1010 in poly ppmw 200 The composition of polyethylene 1 was analyzed using iCCD. The data generated from the iCCD tests of Polyethylene Composition 1 are provided in Table 2, which outlines the iCCD data to include the areas of the respective polyethylene fractions (25°C-35°C, 35°C-70°C, 70°C-85°C and 85°C-120°C). Table 2: iCCD of polyethylene composition 1 Weight percentage (% by weight) of the temperature range Molecular weight of the temperature range 25 °C—45 °C 0.46 % 201,556 117 45 °C-80 °C 54.22 % 171,452 80 °C-95 °C 5.99 % 126,099 95 °C-120 °C 39.33 % 91,208 Example 2: Comparative Polyethylene Composition A Comparative polyethylene composition A was a bimodal polyethylene composition that was generally prepared using the catalyst system and processes provided for preparing the First Compositions of the invention in PCT Publication No. WO 2015 / 200743. Example 3: Analysis of the composition of polyethylene 1 and the comparative composition A Polyethylene Composition 1 from Example 1 and Comparative Polyethylene Composition A were analyzed using iCCD. The data generated from the iCCD tests of both samples (Polyethylene Composition 1 from Example 1 and Comparative Polyethylene Composition A) are provided in Table 3. Table 3 provides additional data for each sample of Comparative Polyethylene Composition A and Polyethylene Composition 1, including total density, melt index, ZSVR, and the ratio of the molecular weight of the first fraction to the total molecular weight. These properties are 118 were measured based on the test methods described in this description. Table 3. Comparison of the composition of polyethylene 1 of Example 1 and comparative polyethylene composition A. MA / t / ZUZÓ / UΊ aoz I PE Sample Polyethylene Composition 1 Comparative Composition A Density (g / cc) 0.918 0.918 Melt Index (g / 10 min) 0.24 0.85 ZSVR 4.5 2.1 Mw / Mn 2.34 3.69 Total Mw (g / mol) 137,300 119,300 Area of ​​fraction 45°C-80°C 54% 53% Area of ​​fraction 80°C-95°C 6% 30% Area of ​​fraction 95°C-120°C 39% 17% Mw 45°C-80°C 171,452 154,889 Mw 80°C-95°C 126,099 62,885 Mw 95°C-120°C 91,208 109,822 Area ratio of fraction 45°C-80°C / area of ​​fraction at 80°C-95°C 9.05 1.79 Mwt. ratio of fraction 45°C-80°C / Mwt of 80°C-95°C 1.36 2.46 Fraction ratio 45°C-80°C / Total Mwt. ratio 1.25 1.30 119 Example 4: Preparation of the AF comparative films and film 1 Table 4 identifies the commercially available polyethylene compositions from the BE Comparative Polyethylene Compositions. Table 4. Comparative polyethylene compositions used in ΜΛ / ΙΖ / ΖυΖΟ / υΊ yoz I the comparative films AF. Comparative Polyethylene Composition Trade Name (Manufacturer) Density (g / cc) Melting Point (g / 10 min) Mw / Mn B AFFINITY™ 8100G (The Dow Chemical Co.) 0.870 1.0 2.1 C ENGAGE™ 7387 (The Dow Chemical Co.) 0.870 <0.5 2.3 D SUPERTOUGH 22ST05 (Total SA) 0.921 0.5 4.2 E 80% DOWLEX™ GM 8090 (The Dow Chemical Co.) 0.916 1.0 In this example, one film, comprising Polyethylene Composition 1, and six comparator films were prepared, each with a total thickness of 70 µm. Layer A of each film was 20% of the total film thickness, each Layer B was 60% of the total film thickness, and each Layer C was 20% of the total film thickness. The materials used to produce each of the film samples in Example 120 are provided in Table 5, and the extrusion conditions used to produce the AF Comparative Films and Film 1 are summarized in Table 6. Table 5. Layer distribution and composition of film 1 and the AF comparative films. Layer A (20%) Layer B (60%) Layer C (20%) Film 1 DOWLEX™ GM 8090 Polyethylene Composition 1 DOWLEX™ GM 8090 Film A DOWLEX™ GM 8090 AFFINITY™ 8100G DOWLEX™ GM 8090 Film B DOWLEX™ GM 8090 ENGAGE™ 7387 DOWLEX™ GM 8090 Film C DOWLEX™ GM 8090 20% of ENGAGE™ 7387 + 80% of DOWLEX™ GM 8090 DOWLEX™ GM 8090 Film D DOWLEX™ GM 8090 SUPERTOUGH 22ST05 DOWLEX™ GM 8090 Film E DOWLEX™ GM 8090 Comparative Polyethylene Composition A DOWLEX™ GM 8090 Film F DOWLEX™ GM 8090 20% AFFINITY™ 8100G + 80% DOWLEX™ GM 8090 DOWLEX™ GM 8090 Table 6. Extrusion conditions for film 1 and comparative AF films. Unit ABCDEF 1 Thickness (pm) 70 70 70 70 70 70 70 BUR 2.5:1 2.5:1 2.5:1 2.5:1 2.5:1 2.5:1 2.5:1 Corona treatment (dyne) 42 42 42 42 42 42 42 121 Matrix opening (mm) 2.5 2.5 2.5 2.5 2.5 2.5 2.5 Layer A extraction percentage (%) 20 20 20 20 20 20 20 Layer B extraction percentage (%) 60 60 60 60 60 60 60 of layer C (%) 20 20 20 20 20 20 20 Extrusion melt pressure A (bar) 269 257 257 262 262 257 262 Extrusion melt pressure B (bar) 349 556 430 421 379 356 562 Extrusion melt pressure C (bar) 283 266 262 270 270 266 215 Extrusion melt temperature A (°C) 226 225 221 223 224 225 215 Extrusion melt temperature B (°C) 231 238 233 228 229 240 242 Extrusion melt temperature C (°C) 230 229 236 230 230 236 236 Output speed (kg / h) 130 130 130 130 130 130 120 Extrusion screw speed A (rpm) 50 51 50 48 50 50 44 Extrusion screw speed B (rpm) 57 63 56 59 56 54 58 Extrusion screw speed C (rpm) 43 43 42 40 41 41 43 Output speed (m / min) 22.4 22.4 22 22.1 22.1 22 19.9 Example 5: Analysis of comparative films AF and film 1 To compare the performance of Film 1 and the AF Comparative Films, the piercing force was measured, 122 The puncture resistance, puncture elongation, puncture energy, dart drop impact, average Elmendorf tear on CD and average Elmendorf tear on MD were determined according to the test methods described above. The puncture and dart drop impact results for Film 1 and Comparative Films AF are provided in Table 7. ML / IZ / ZUZO / U aoz I Table 7. Dart drop and puncture measurements of film 1 and AF comparative films. Puncture Force (N) Puncture Resistance (J / cm3) Puncture Elongation (mm) Puncture Energy (J) Dart Drop Impact (g) CD Tear (g) MD Tear (g) Film 1 103.6 13.11 117.4 7.289 1150 1125 569.9 Film A 50.47 6.640 116.3 3.715 781 852.7 464.4 Film B 58.70 9.043 138.6 5.021 725 447.7 178.4 Film C 67.53 7.658 100.8 4.373 524 994.1 565.7 Film D 74.87 7.394 88.83 4.314 385 1140 573.7 Film E 65.56 5.691 79.05 3.334 781 1306 732.3 Film F 56.42 6.610 97.94 3.606 515 985 561.1 As shown in Table 7, Film 1 exhibited greater puncture properties (puncture strength, puncture resistance, puncture elongation, and puncture energy) than all other AF comparative film samples. For Films D and E, which used comparative polyethylene compositions that have 123 densities closer to the polyethylene compositions described in this description, Film 1 exhibited superior puncture properties, as well as dart drop impact (Method B). It will be evident that modifications and variations are possible without departing from the scope of the description defined in the appended claims. More specifically, although some aspects of the present description are identified herein as preferred or particularly advantageous, it is envisaged that the present description is not necessarily limited to these aspects. It is hereby stated that, as of this date, the best method known to the applicant for putting the aforementioned invention into practice is the one that is clear from the present ΜΛ / ΙΖ / ΖυΖό / υΊ UOZ I description of the invention.

Claims

1. A polyethylene composition characterized in that it comprises: a first polyethylene fraction area in the temperature range of 45 °C to 80 °C of an elution profile by the enhanced comonomer composition distribution (iCCD) analysis method; a second polyethylene fraction area in the temperature range of 80 °C to 95 °C of the elution profile by the iCCD analysis method, wherein the second polyethylene fraction area comprises at least 5% of the total elution profile area; a third polyethylene fraction area in the temperature range of 95 °C to 120 °C of an elution profile by the iCCD analysis method, wherein the third polyethylene fraction area comprises at least 25% of the total elution profile area; wherein: the ratio of the first polyethylene fraction area to the second polyethylene fraction area is 6 to 15;and 125 the polyethylene composition has a density of 0.910 g / cm3 to 0.924 g / cm3 and a melt index (I2) of 0.1 g / 10 minutes to 0.5 g / 10 minutes.; 2. The polyethylene composition according to claim 1, characterized in that it has a molecular weight distribution, expressed as the ratio of the weighted average molecular weight to the number average molecular weight (Mw / Mn), in the range of 2.0 to 5.

0.

3. The polyethylene composition according to any of the preceding claims, characterized in that it has a zero shear viscosity ratio of 3 to 6.

4. The polyethylene composition according to any of the preceding claims, characterized in that a molecular weight ratio of the first polyethylene fraction to a molecular weight ratio of the second polyethylene fraction is from 0.75 to 1.

50.

5. The polyethylene composition according to any preceding claim, characterized in that the third polyethylene fraction comprises a peak, and the peak width at a peak height of 50 percent is 2°C to 10°C.

6. The polyethylene composition according to any of the preceding claims, characterized in that the area of ​​the first polyethylene fraction comprises from 45% to 60% of the total area of ​​the elution profile. ML / IZ / ZUZO / U aoz I 126 7. The polyethylene composition according to any of the preceding claims, characterized in that the area of ​​the second polyethylene fraction comprises from 5% to 15% of the total area of ​​the elution profile.

8. The polyethylene composition according to any of the preceding claims, characterized in that the area of ​​the third polyethylene fraction comprises from 25% to 50% of the total area of ​​the elution profile.

9. The polyethylene composition according to any of the preceding claims, characterized in that it has a tangent delta ratio of 2.0 to 5.0, when measured using the DMS frequency exchange test methods at 0.1 rad / s per 500 rad / s.

10. The polyethylene composition according to any of the preceding claims, characterized in that it has a tangent delta of 1.0 to 6.0, when measured using the DMS frequency exchange test methods at 0.1 rad / s and 190 °C.

11. A polyethylene composition characterized in that it comprises: an area of ​​the first polyethylene fraction in the temperature range of 45 °C to 80 °C of an elution profile by the enhanced comonomer composition distribution analysis (iCCD) method; an area of ​​the second polyethylene fraction in the temperature range of 80 °C to 95 °C of the elution profile by the iCCD analysis method, wherein the area of ​​the second polyethylene fraction comprises at least 5% of the total area of ​​the elution profile; an area of ​​the third polyethylene fraction in a temperature range of 95 °C to 120 °C of an elution profile by the iCCD analysis method, wherein the area of ​​the third polyethylene fraction comprises at least 25% of the total area of ​​the elution profile; and where the polyethylene composition has a density of 0.910 g / cm3 to 0.924 g / cm3, a melt index (I2) of 0.1 g / 10 minutes to 0.5 g / 10 minutes and a molecular weight distribution, expressed as the ratio of weighted average molecular weight to number average molecular weight (Mw / Mn), in the range of 2.0 to 5.

0.

12. A film characterized in that it comprises the polyethylene composition in accordance with any of the preceding claims.

13. The film according to claim 12, characterized in that it is a single-layer film.

14. The film according to claim 12, characterized in that it is a multilayer film.

15. The film according to claim 14, characterized in that one or more layers of the multilayer film comprise the composition of polyethylene.