POLYETHYLENE COMPOSITIONS

Abstract

Modalities of a polyethylene composition are provided, which may include a first polyethylene fraction comprising at least one peak in a temperature range of 35 °C to 70 °C in an elution profile by the enhanced comonomer composition distribution (iCCD) analysis method, wherein a first polyethylene area fraction is an area in the elution profile of 35 °C to 70 °C, and wherein the area of ​​the first polyethylene fraction comprises from 25% to 65% of the total area of ​​the elution profile; and a second polyethylene fraction comprising at least one peak in a temperature range of 85 °C to 120 °C in the elution profile, wherein a second polyethylene area fraction is an area in the elution profile of 85 °C to 120 °C, and wherein the area of ​​the second polyethylene fraction comprises at least 20% of the total area of ​​the elution profile.

Description

POLYETHYLENE COMPOSITIONS FIELD OF INVENTION This application is directed to polymer compositions and, more specifically, to polyethylene compositions and methods for producing them. BACKGROUND OF THE INVENTION The use of polyolefin compositions in industries such as packaging applications is well-established. A variety of conventional methods can be employed to produce such polyolefin compositions. Various polymerization techniques using different catalyst systems have been used to produce polyolefin compositions suitable for packaging applications. However, despite research efforts in developing compositions suitable for packaging applications, there is still a need for improved polyethylene compositions suitable for packaging applications that can achieve a good balance of phase properties and processability at desired polymer composition densities. BRIEF DESCRIPTION OF THE INVENTION This application describes polyethylene compositions suitable for packaging applications, films, multilayer structures, and packaging articles. Ref. 335473 manufactured from these. In certain forms, the polyethylene compositions described herein are suitable for use as heat sealer packaging applications. Conventional films, such as those using a sealing layer, typically experience a compromise between the heat adhesion initiation temperature, the heat sealing initiation temperature, or both, and the overall film density. The density of a composition can affect the film's processing characteristics. For example, films containing conventional polyethylene compositions with relatively lower densities tend to exhibit lower heat adhesion initiation temperatures, heat sealing initiation temperatures, or both, compared to films containing compositions with relatively higher overall densities.Polyethylene compositions with relatively lower densities can also be particularly difficult to process in conventional blown film applications due to their very low melting point and the material's sticky or small-bodied nature. Conversely, films with relatively higher overall density frequently exhibit higher hot adhesion initiation temperatures, heat sealing initiation temperatures, or both. MA / a / ZUZZ / UUOl 1 For packaging applications, lower heat adhesion and heat sealing initiation temperatures can be desirable polymer performance characteristics. Consequently, films with relatively higher densities are needed to provide lower heat adhesion initiation temperatures, heat sealing initiation temperatures, or both. The polyethylene compositions described herein can provide films with relatively high densities and relatively low heat adhesion initiation temperatures, heat sealing initiation temperatures, or both. As described in detail herein, polymer compositions can be evaluated by enhanced comonomer composition distribution (iCCD) analysis. Embodiments of this description can satisfy the requirements described above regarding heat-sealing initiation temperature, hot-adhesion initiation temperature, and polymer density by providing polyethylene compositions that, in some embodiments, include at least three polyethylene fractions at particular temperature ranges, as determined by iCCD analysis, each comprising a desired percentage of the total elution profile area. Such polyethylene compositions can have desirable hot-adhesion initiation temperatures, heat-sealing initiation temperatures, or both, with a density of, for example, at least 0.880 g / cm³.For example, the polyethylene compositions described herein may have, at relatively high densities, lower hot-bond initiation temperatures, heat-sealing initiation temperatures, or both, than conventional polymer compositions. Not limited to theory, it is believed that at least some of the polyethylene compositions described herein may have such properties due, at least in part, to a particular multimodal elution profile where a first polyethylene fraction and a second polyethylene fraction show peaks at 35 °C to 70 °C and 85 °C to 120 °C, respectively, in the iCCD elution profile. According to one or more embodiments, a polyethylene composition suitable for packaging applications may include (a) a first polyethylene fraction comprising at least one peak in a temperature range of 35 °C to 70 °C in an elution profile by means of the enhanced comonomer composition distribution (iCCD) analysis method, wherein a first polyethylene area fraction is an area in the elution profile of 35 °C to 70 °C, and wherein the area of ​​the first polyethylene fraction comprises from 25% to 65% of the total area of ​​the elution profile; (b) a second polyethylene fraction comprising at least one peak in a temperature range of 85 °C to 120 °C in the elution profile by means of the iCCD analysis method, wherein a second polyethylene area fraction is an area in the elution profile from 85 °C to 120 °C, and wherein the area of ​​the second polyethylene fraction comprises at least 20% of the total area of ​​the elution profile;and (c) a third polyethylene fraction in a temperature range of 70 °C to 85 °C in the elution profile by means of the iCCD analysis method, wherein the third polyethylene area fraction is an area in the elution profile from 70 °C to 85 °C, and wherein the area of ​​the third polyethylene fraction comprises less than 10% of the total area of ​​the elution profile. The polyethylene composition may have a density of 0.880 g / cm3 to 0.910 g / cm3, a melt index (I2) of 0.50 g / 10 mins to 6.0 g / 10 mins, and a zero shear viscosity ratio of the polyethylene composition of less than 2.0. According to one or more of the above embodiments, a film may comprise the polyethylene composition described above or any of the other embodiments described herein. According to one or more modalities, an article may comprise the polyethylene composition described above or in any of the other modalities described herein. BRIEF DESCRIPTION OF THE FIGURES The following detailed description of specific modalities in this description can be better understood when read in conjunction with the following figures, where a similar structure is indicated by similar reference numbers and in which: Figure 1 schematically represents an iCCD elution profile, according to one or more of the modalities described herein; and Figure 2 schematically represents a reactor system useful for producing polyethylene, according to one or more of the modalities described herein. DETAILED DESCRIPTION OF THE INVENTION This description outlines various polyethylene compositions. Such polyethylene compositions can be used, for example, in packaging applications. The polyethylene compositions may include a first polyethylene fraction, a second polyethylene fraction, and a third polyethylene fraction. The polyethylene composition may be incorporated into a film (including single-layer and multi-layer films) or other articles such as multi-layer structures and containers. As described herein, a polyethylene or ethylene-based polymer refers to polymers comprising a majority (>50 mol%) of units derived from the monomer ethylene. This includes polyethylene homopolymers or copolymers (i.e., units derived from two or more comonomers). Common forms of polyethylene known in the art include 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 polyethylene (m-LLDPE) resins; ethylene-based plastomers (POPs) and ethylene-based elastomers (POE); medium-density polyethylene (MDPE); and high-density polyethylene (HDPE).These polyethylene materials are generally known in the art; however, the following descriptions may be helpful in understanding the differences between some of these different polyethylene resins. The term composition, as used in the present description, refers to a mixture of materials comprising the composition, as well as reaction products and decomposition products formed from the composition materials. The term LDPE may also be called high-pressure ethylene polymer or highly branched polyethylene and can be defined as the polymer that is homopolymerized or partially or completely copolymerized in autoclaves or tubular reactors at pressures above 14,500 psi (100 MPa) with the use of free radical initiators, such as peroxides (see, for example, US 4,599,392, which is incorporated herein by reference). Typically, LDPE resins have a density in the range of 0.916 to 0.935 g / cm³. The term LLDPE includes resin prepared using traditional Ziegler-Natta catalyst systems and chromium-based catalyst systems, as well as 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), and includes linear, substantially linear, or heterogeneous polyethylene copolymers or homopolymers. LLDPEs contain less long-chain branching than LDPEs and include substantially linear ethylene polymers further defined in U.S. Patents 5,272,236, 5,278,272, 5,582,923, and 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 the U.S. Patent. ινΐΛ / a / zuzz / uuo 11 y 4,076,698; and / or mixtures thereof (such as those described in US 3,914,342 or US 5,854,045). LLDPEs may be manufactured by gas-phase, solution-phase, or suspension polymerization, or any combination thereof, using any type of reactor or reactor configuration known in the art. The term MDPE refers to polyethylenes that have densities of 0.924 to 0.936 g / 3. Typically, MDPE is manufactured using chromium or Ziegler-Natta catalysts or single-site catalysts that include, but are 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). The term HDPE refers to polyethylenes that have densities greater than approximately 0.935 g / cm3 and up to approximately 0.980 g / cm3, which are generally prepared with Ziegler-Natta catalysts, chromium catalysts or single-site catalysts which include, but are 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). ινΐΛ / a / zuzz / uuo 11 y The term ULDPE refers to polyethylenes with densities of 0.855 to 0.912 g / cm³, typically prepared using Ziegler-Natta catalysts, chromium 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). ULDPEs include, but are not limited to, polyethylene plastomers (ethylene-based) and polyethylene elastomers (ethylene-based). Polyethylene plastomers or elastomers (ethylene-based) generally have densities of 0.855 to 0.912 g / cm³. Blend, polymer blend, and similar terms mean a composition of two or more polymers. Such a blend may be miscible or immiscible. Such a blend may be phase-separated or not. Such a blend 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. Blends are not laminates, but one or more layers of a laminate may contain a blend. Such blends may be prepared as dry blends, formed in situ (e.g., in a reactor), melt blends, or by other techniques known to those skilled in the art. 0.908 g / cm3, 0.902 g / cm3a 0.906 g / cm3, 0.902 g / cm3a 0.904 g / cm3, 0.904 g / cm3a 0.910 g / cm3, 0.904 g / cm3a 0.908 g / cm3, 0.904 g / cm3a 0.906 g / cm3, 0.906 g / cm3a 0.910 g / cm3, 0.906 g / cm3a 0.908 g / cm3, 0.908 g / cm3a 0.910 g / cm3, or any combination of these intervals. In one or more embodiments, the polyethylene composition may have a melt index (I2) of 0.50 g / 10 minutes to 6.0 g / 10 minutes. For example, in one or more embodiments, the polyethylene composition may have a melt index (I2) of 0.5 g / 10 minutes. 4.0 g / 10 minutes, 0.5 g / 10 minutes 0.0 g / 10 minutes, 0.0 g / 10 minutes 0.0 g / 10 minutes, 0.0 g / 10 minutes 0.0 g / 10 minutes, 0.0 g / 10 minutes 0.0 g / 10 minutes, 0.0 g / 10 minutes 6.0 g / 10 minutes, According to)S to 5.0 g / 10 minutes, from 0.5 g / 10 minutes to 2.0 g / 10 minutes, from 1.0 g / 10 minutes to 5.0 g / 10 minutes, from 1.0 g / 10 minutes to 2.0 g / 10 minutes, from 2.0 g / 10 minutes to 4.0 g / 10 minutes, from 3.0 g / 10 minutes to 5.0 g / 10 minutes, from 4.0 g / 10 minutes to 5.0 g / 10 minutes, or any combination with modalities, from 0.5 g / 10 minutes to 3.0 g / 10 minutes, from 0.5 g / 10 minutes to 6.0 g / 10 minutes, from 1.0 g / 10 minutes to 3.0 g / 10 minutes, from 2.0 g / 10 minutes to 5.0 g / 10 minutes, from 2.0 g / 10 minutes to 6.0 g / 10 minutes, from 3.0 g / 10 minutes to 6.0 g / 10 minutes, from 5.0 g / 10 minutes to _on of these intervals. 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 6.0. For example, the composition of polyethylene can have a molecular weight distribution of 2.0 to 5.5, 2.0 to 5.0, 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 6.0, 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, or 5.5 to 6.0, 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 additional embodiments, the polyethylene composition may have a zero shear viscosity ratio of less than 2.0. For example, the polyethylene composition may have a zero shear viscosity ratio of less than 1.9, less than 1.8, less than 1.7, less than 1.6, less than 1.5, less than 1.4, less than 1.3, less than 1.2, or even less than 1.1. In one or more embodiments, the polyethylene composition may have a zero shear viscosity ratio of at least 1.0. In various forms, the polyethylene composition can have a zero shear viscosity ratio of 1.0 to 2.0, 0.0 to 1.8, 1.0 to 1.6, 1.0 to 1.4, 1.0 to 1.2, 1.2 to 2.0, 1.2 to 1.8, 1.2 to 1.6, 1.2 to 1.4, 1.4 to 2.0, 1.4 to 1.8, 1.4 to 1.6, 1.6 to 2.0, 1.6 to 1.8, or 1.8 to 2.0. Tangent delta (tan δ) refers to a measure of how close a material is to a perfectly elastic solid (where d = 0°, tangent delta = 0) or how close a material is to a perfectly Newtonian liquid (where d = 90°, tangent delta ≠ infinity). Therefore, lower tangent delta values ​​reflect greater elasticity. Tangent delta is a function of long-chain branching (LCB) and molecular weight distribution (MWD) at the same total molecular weight. Higher tangent delta values ​​indicate a lower LCB. In some cases, polyethylene compositions can have a tangent delta of 0.1 radianes / s y 190 °C, de 10 a 100, 10 a 90, 10 a 80, 10 a 70, 10 a 60, 10 a 50, 10 a 40, 10 a 30, 10 a 20, 20 a 100, 20 a 90, 20 a 80, 20 a 70, 20 a 60, 20 a 50, 20 a 40, 20 a 30, 30 a 100, 30 a 90, 30 a 80, 30 a 70, 30 a 60, 30 a 50, 30 a 40, 40 a 100, 40 a 90, 40 a 80, 40 a 70, 40 a 60, 40 a 50, 50 a 100, 50 a 90, 50 a 80, 50 a 70, 50 a 60, 60 a 100, 60 a 90, 60 a 80, 60 a 70, 70 a 100, 70 a 90, 70 a 80, 80 a 100, 80 a 90, o 90 a 100. As described herein, a polyethylene fraction refers to a portion of the total polyethylene composition. The modalities described herein may include at least a first polyethylene fraction and a second polyethylene fraction. Modalities may also include a third polyethylene fraction and a fourth polyethylene fraction. The various fractions included in the polyethylene composition can be defined by their temperature range in an elution profile using the enhanced comonomer composition distribution (iCCD) analysis method. For example, a polyethylene fraction can be defined by a range from a lower to a higher temperature. It is understood that two or more polyethylene fractions may overlap. The polyethylene fractions, in one or more modalities, can generally be correlated with peaks or valleys in the iCCD data.In one or more configurations, a particular polyethylene fraction may include a specified percentage of the total area of ​​the polyethylene composition defined by the iCCD elution profile. Unless otherwise specified, any elution profile mentioned herein is the elution profile observed by iCCD. Examples of such fractions will be better understood by examining the accompanying examples. In general, the first fraction may include at least one peak within the temperature range of the first fraction. The second fraction may include at least one peak within the temperature range of the second fraction. The fourth fraction may include at least one peak within the temperature range of the fourth fraction. The polyethylene compositions described herein may be termed multimodal, meaning that they include at least two peaks in their elution profile. In modalities, the polyethylene compositions described herein may include two peaks (bimodal), three peaks (trimodal), or more than three peaks in their elution profile. The first polyethylene area fraction, the second polyethylene fraction, the third polyethylene fraction, and the fourth polyethylene fraction, respectively, may each include a portion of the total mass of the polyethylene composition. With reference to the described iCCD distribution, Figure 1 schematically represents a sample iCCD 100 distribution. Figure 1 generally represents various characteristics of the iCCD profiles of the polyethylene compositions described herein, such as the first fraction, second fraction, third fraction, fourth fraction, etc., which are analyzed in detail in this description. As such, Figure 1 can be used as a reference with respect to the iCCD profile descriptions provided herein. Specifically, the first fraction 102, the second fraction 104, the third fraction 106, and the fourth fraction 108 are represented. The first fraction 102 has a peak 112, and the second fraction 104 has a peak 114. The fourth fraction 108 may have a peak 118. 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 characteristics of an iCCD elution profile. In one or more embodiments, one or more of the first polyethylene fraction, the second polyethylene fraction, and the fourth polyethylene fraction may have a single peak. As used herein, a single peak refers to an iCCD where a particular fraction includes only one peak. That is, in some embodiments, the iCCD of one or more of the first polyethylene fraction, the second polyethylene fraction, and the fourth polyethylene fraction includes only an upsloping region followed by a downsloping region to form the single peak. It is understood that a peak in one or more of the first, second, and fourth polyethylene fractions 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 of a single polyethylene fraction. For example, if a single peak followed by a single trough 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. In one or more embodiments, the first polyethylene 102 fraction may be an area in the elution profile from 35 °C to 70 °C. In additional embodiments, the first polyethylene 102 fraction may be an area in the elution profile in the temperature range of 35 °C to 60 °C, 35 °C to 50 °C, 40 °C to 70 °C, 40 °C to 60 °C, 40 °C to 50 °C, 50 °C to 70 °C, 50 °C to 60 °C, 60 °C to 70 °C, or any combinations thereof in the elution profile by means of iCCD. According to one or more modalities, the area of ​​the first polyethylene fraction may comprise at least 25% of the total area of ​​the elution profile (e.g., at least 30%, at least 40%, at least 50%, or even at least 60% of the total area of ​​the elution profile). For example, the area of ​​the first polyethylene fraction may comprise 25% to 65%, 25% to 55%, 25% to 45%, 25% to 35%, 35% to 65%, 35% to 55%, 35% to 45%, 45% to 65%, 45% to 55%, 55% to 65%, or any combination thereof, of the total area of ​​the elution profile. In one or more embodiments, the first polyethylene fraction 102 may have at least one peak 112 in the temperature range of 35 °C to 70 °C in the iCCD elution profile. In one or more embodiments, the first polyethylene fraction 102 may have at least one peak 112 in the temperature range of 35 °C to 60 °C, 35 °C to 50 °C, 40 °C to 70 °C, 40 °C to 60 °C, 40 °C to 50 °C, 50 °C to 70 °C, 50 °C to 60 °C, 60 °C to 70 °C, or any combination thereof in the iCCD elution profile. The temperature range of the first polyethylene fraction, from 35°C to 70°C, may be desirable because it could correspond to a low-density component in the polyethylene composition. In some cases, the low-density component can provide lower hot bond initiation temperatures, heat sealing initiation temperatures, or both. Therefore, increasing the first polyethylene fraction 102, which may include the low-density component, can thus lower the hot bond initiation temperatures, heat sealing initiation temperatures, or both of the polyethylene composition and improve the hot bond strength and hot bond window. In one or more embodiments, the second polyethylene 104 fraction may be an area in the elution profile from 85 °C to 120 °C. In additional embodiments, the second polyethylene 104 fraction may be an area in the elution profile in the temperature range of 85 °C to 110 °C, 85 °C to 100 °C, 85 °C to 90 °C, 90 °C to 120 °C, 90 °C to 110 °C, 90 °C to 100 °C, 100 °C to 120 °C, 100 °C to 110 °C, 110 °C to 120 °C, or any combinations thereof in the elution profile by means of iCCD. According to one or more of the modalities, the area of ​​the second polyethylene fraction may comprise at least 20% of the total area of ​​the elution profile (e.g., at least 30%, at least 35%, at least 40%, or at least 45% of the total area of ​​the elution profile). For example, the area of ​​the second polyethylene fraction may comprise 20% to 60%, 20% to 50%, 20% to 40%, 20% to 30%, 30% to 60%, 30% to 50%, 30% to 40%, 40% to 60%, 40% to 50%, 50% to 60%, or any combination thereof, of the total area of ​​the elution profile. In one or more embodiments, the second polyethylene fraction 104 may have at least one peak 114 in the temperature range of 85 °C to 120 °C in the iCCD elution profile. In one or more embodiments, the second polyethylene fraction 104 may have at least one peak 114 in the temperature range of 85 °C to 110 °C, 85 °C to 100 °C, 85 °C to 90 °C, 90 °C to 120 °C, 90 °C to 110 °C, 90 °C to 100 °C, 100 °C to 120 °C, 100 °C to 110 °C, 110 °C to 120 °C, or any combination thereof in the iCCD elution profile. The temperature range of the second polyethylene fraction, from 85°C to 120°C, may be desirable because it can correspond to a high-density component. In some cases, increasing the high-density component can increase the overall density of the polyethylene composition. Therefore, increasing the second polyethylene fraction (104) can thus increase the high-density component and provide a polyethylene composition with a higher overall density. Furthermore, increasing the second polyethylene fraction (104) can improve the blocking properties of the polyethylene composition. Beyond theory, it is believed that larger crystals form in the high-density fraction, which provides a rough surface. This rough surface can reduce the contact area and thus improve the blocking properties of the polyethylene composition. In one or more configurations, the polyethylene composition may have a local minimum in an iCCD elution profile within a temperature range of 65 °C to 85 °C. This local minimum may be between peak 112 of the first polyethylene 102 fraction and peak 114 of the second polyethylene 104 fraction. In one or more embodiments, the third fraction of polyethylene 106 area may be an area in the elution profile from 70 °C to 85 °C. In additional embodiments, the third fraction of polyethylene 106 may be an area in the elution profile in the temperature range of 70 °C to 80 °C, 70 °C to 75 °C, 75 °C to 85 °C, 75 °C to 80 °C, 80 °C to 85 °C, or any combinations thereof in the elution profile by means of iCCD. According to one or more of the modalities, the area of ​​the third polyethylene fraction may comprise less than 10% of the total elution profile area (e.g., less than 8%, less than 6%, or less than 4% of the total elution profile area). For example, the area of ​​the third polyethylene fraction may comprise 4% to 10%, 4% to 8%, 4% to 6%, 6% to 10%, 6% to 8%, 8% to 10%, or any combination thereof, of the total elution profile area. In the embodiments described herein, the third area fraction of polyethylene 106 may be the area in the elution profile from 70 °C to 85 °C. In one or more embodiments, the third area fraction of polyethylene 106 may be in the area in the elution profile from 70 °C to 85 °C, 70 °C to 80 °C, 70 °C to 75 °C, 75 °C to 85 °C, 75 °C to 80 °C, 80 °C to 85 °C, or any combinations thereof in the elution profile by means of iCCD. It may be desirable to minimize the third polyethylene 106 fraction in the 70°C to 85°C temperature range, which would otherwise shift the higher-density component of the second polyethylene 104 fraction to a lower temperature range within the elution profile. While not limited to theory, it is believed that shifting the high-density component to a lower temperature range within the elution profile may prevent the polyethylene composition from achieving the desired blocking properties. In one or more embodiments, the fourth fraction of polyethylene 108 area may be an area in the elution profile from 20 °C to 35 °C. In additional embodiments, the fourth fraction of polyethylene 104 may be an area in the elution profile in the temperature range of 20 °C to 30 °C, 20 °C to 25 °C, 25 °C to 35 °C, 25 °C to 30 °C, 30 °C to 35 °C, or any combinations thereof in the elution profile by means of iCCD. Depending on one or more of the modalities, the area of ​​the fourth polyethylene fraction may comprise less than 35% of the total elution profile area (e.g., less than 30%, less than 20%, less than 10%, less than 5%, or even less than 2% of the total elution profile area). For example, the area of ​​the fourth polyethylene fraction may comprise 0% to 35%, 0% to 20%, 0% to 10%, 0% to 5%, or 5% to 35%, from 5% to 20%, from 5% to 10%, from 10% to 35%, from 10% to %, from 20% to 35%, or any combinations of the total elution profile area. In the embodiments described herein, the fourth polyethylene 108 area fraction is the area in the elution profile below at least one peak 118 of the fourth polyethylene 108 fraction from 20 °C to 35 °C. In one or more embodiments, the fourth polyethylene 108 fraction may have at least one peak 118 in the temperature range of 20 °C to 30 °C, 20 °C to 25 °C, 25 °C to 35 °C, 25 °C to 30 °C, 30 °C to 35 °C, or any combinations thereof in the iCCD elution profile. It may be desirable to minimize the fourth fraction of polyethylene 108 in the temperature range of 20 °C to 35 °C. Beyond theory, it is believed that a high amount of the fourth fraction of polyethylene 108 can prevent the polyethylene composition from achieving the desired blocking properties. In one or more configurations, the polyethylene composition may have a local minimum in an iCCD elution profile within a temperature range of 30 °C to 40 °C. This local minimum may be between peak 118 of the fourth polyethylene fraction 108 and peak 112 of the first polyethylene fraction 102. It is understood that two or more polyethylene fractions may overlap. In one or more embodiments, the first polyethylene area fraction 102 and the fourth polyethylene area fraction 108 may overlap. In one or more embodiments, the 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 configurations, the weighted average molecular weight of the first polyethylene fraction may be less than or equal to 225,000 g / mol, such as from 30,000 g / mol to 225,000 g / mol, 60,000 g / mol to 150,000 g / mol, or from 90,000 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 iCCD results, as described below. In one or more configurations, the weighted average molecular weight of the second polyethylene fraction may be less than or equal to 225,000 g / mol, such as from 25,000 g / mol to 225,000 g / mol, 50,000 g / mol to 150,000 g / mol, from 75,000 g / mol to 125,000 g / mol, or any combination of these ranges. The molecular weight of the polyethylene fractions can be calculated based on the iCCD results, as described below. In one or more embodiments, the 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 CaCO3, 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. The polyethylene compositions may contain from approximately 0.1 to approximately 10 percent by combined weight of such additives, depending on the weight of the polyethylene composition including such additives. In some models, the ratio between the molecular weight of the first polyethylene area fraction and the molecular weight of the total elution profile area is 0.5 to 1.5. In some models, the ratio can be 0.5 to 1.5, 0.5 to 1.0, or 1.0 to 1.5. Polymerization To produce the polyethylene compositions described herein, any conventional polymerization processes may be employed. Such conventional polymerization processes include, but are not limited to, gas-phase polymerization processes, suspension polymerization processes, and solution polymerization processes, using one or more conventional reactors, e.g., loop reactors, isothermal reactors, stirred-tank reactors, pipe flow reactors, plug flow reactors, batch reactors in parallel, in series, and / or any combination thereof. The polyethylene composition may be produced, for example, by a solution-phase polymerization process with one or more loop reactors, isothermal reactors, and combinations thereof. In general, the solution-phase polymerization process can occur in one or more well-mixed reactors, such as one or more isothermal loop reactors or one or more adiabatic reactors, at temperatures in the range of 115 °C to 250 °C (e.g., 115 °C to 210 °C) and pressures in the range of 300 psi to 3000 psi (e.g., 400 psi to 800 psi). In some embodiments, in a double reactor, the temperature in the first reactor is in the range of 115 °C to 190 °C (e.g., 150 °C to 180 °C), and the temperature in the second reactor is in the range of 150 °C to 250 °C (e.g., 180 °C to 220 °C). In other configurations, in a single reactor, the temperature in the reactor is in the range of 115 to 250 °C (e.g., from 115 °C to 225 °C). The residence time in the 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 polyethylene and solvent is then removed from the reactor, and the polyethylene is isolated. Typically, the solvent is recovered using 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 polyethylene composition can be produced by solution polymerization in a double-reactor system, for example, a double-loop reactor system, where ethylene is polymerized in the presence of one or more catalyst systems and one or more comonomers. In some embodiments, only ethylene is polymerized. In addition, one or more cocatalysts may be present. In another embodiment, the 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 and one or more comonomers. Catalytic systems Specific embodiments of catalyst systems that, in one or more embodiments, can be used to produce the polyethylene compositions described herein will now be described. It is understood that the catalyst systems in this description can be incorporated in different forms and should not be interpreted as being limited to the specific embodiments set forth herein. Rather, embodiments are provided to make this description comprehensive and complete, and to fully convey the scope of the subject matter to those skilled in the art.Not limited to theory, it is believed that the catalyst systems produce a mixture of a low-density component in the temperature range of 35°C to 70°C, which may therefore allow the polyethylene composition to achieve the hot bonding initiation temperature, the heat sealing initiation temperature, or both, and a high-density component in the temperature range of 35°C to 70°C, which may therefore allow the polyethylene composition to achieve the desired locking properties. 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 containing carbon atoms, a parenthetical expression 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 by the parenthetical expression (Cx-Cy) may contain more than y carbon atoms, depending on the identity of any of the Rs groups. For example, a (C1-C40) alkyl group substituted with exactly one Rs group, where Rs is phenyl (-CgHs), may 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 total minimum and maximum 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 every 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 otherwise 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 substituted by one or more Rs. In this description, a (C1-C40) hydrocarbyl can be an unsubstituted or substituted (C1-C40) alkyl, (C3-C40) cycloalkyl, (C3-C20) alkylene, (C1-C20) aryl, or (C6-C40) aryl alkylene. In some embodiments, each of the above-mentioned (C1-C40) hydrocarbyl groups has a maximum of 20 carbon atoms (i.e., C1-C20 hydrocarbyl), and in other embodiments, a maximum of 12 carbon atoms. The terms alkyl (C1-C40) and alkyl (Ci-Cig) 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-C4) alkyl include substituted (C1-C20) alkyl, substituted (C1-C10) alkyl, trifluoromethyl, and [C45] alkyl. The term [C45] alkyl (in brackets) means that there are 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-C4o) means a mono-, bi-, or tricyclic aromatic hydrocarbon radical of 6 to 40 carbon atoms, either 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 aryl (Cg-C4o) include unsubstituted aryl (C6-C2o), unsubstituted aryl (C6-C18), 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 (Cg-Co) include substituted aryl (Ci-C20); substituted aryl (C6-Ci8); 2,4-bis[alkyl(C2q)]-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-C20), unsubstituted cycloalkyl (C3-C10), cyclopropyl, cyclobutyl, cyclopentyl, cyclohexyl, cycloheptyl, cyclooctyl, cyclononyl, and cyclodecyl. Examples of substituted cycloalkyl(C3-C40) are substituted cycloalkyl(C3-C20), substituted cycloalkyl(C3-C10), cyclopentanon-2-yl, and 1-fluorocyclohexyl. Examples of hydrocarbylenes (C1-C40) include unsubstituted or substituted arylene (C6-C40), cycloalkylene (C3-C40), and alkylene (C1-C40) (e.g., alkylene (C1-C20)). 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 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 that has 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 (Cg-Cs0) include phenyl-1,4-diyl, naphthalene-2,6-diyl, and naphthalene-3,7-diyl. The term alkylene (C1-C40) means a saturated linear-chain or branched-chain diradical (i.e., the 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 unsubstituted -CH2CH2-, -(CH2)3-, -(CH2)4-, -(CH2)5-, -(CH2)6-, -(CH2)7-, -(CH2)8-, -CH2C*HCH3 and -(CH2)4C*(H)(CH3), where 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 (Ci—C2o) alkylene, -CF2-, -C (O) - and - (CH2)44C (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)-7,7-dimethylbicyclo[2.2.1]heptane, and 2,3-bis(methylene)bicyclo. [2.2.2]octane. The term cycloalkylene (C3-C4o) 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 -Si(Rc)-, where each Rc, each RN, and each Rp is an unsubstituted hydrocarbyl (Ci-Cig) 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 with 1 to 40 carbon atoms, and the term heterohydrocarbylene (C1-C40) means a heterohydrocarbon diradical with 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 the diradicals of heterohydrocarbyl 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 heterohydrocarbyl (C1-C40) can be heteroalkyl (C1-C40) , hydrocarbyl (C1-C40) -O-, hydrocarbyl (C1-C40) -S-, hydrocarbyl (C1-C40) -S (O) , hydrocarbyl (C1-C40) -S (O) 21 hydrocarbyl (C1-C40) -Si (Rc) 2, hydrocarbyl (C1-C40) -N (RN) , hydrocarbyl (C1-C40) -P (Rp) , heterocycloalkyl (C2-C40) , heterocycloalkyl (C2-C19) alkylene© (C1-C20) , cycloalkyl (C3-C20) -heteroalkylene (C1-C19) , heterocycloalkyl (C2-C19) -heteroalkylene (C1-C20) ¡ ινΐΛ / a / zuzz / uuo 11 and 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 (C3-C40) means an unsubstituted or substituted (by one or more Rs) mono-, bi-, or tricyclic heteroaromatic hydrocarbon radical with 4 to 40 total carbon atoms 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 heteroaromatic hydrocarbon radicals with a 5-membered ring 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; tetrazol-l-yl; tetrazol-2-yl; and tetrazol-5-yl. The 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 fused 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. Tricyclic heteroaromatic hydrocarbon radicals can be 5,6,5, 5,6,6, 6,5,6, or 6,6,6 ring systems. An example of a 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]indol-l-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 9H-carbazol9-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-C4q) heterocycloalkyl include unsubstituted (C2-C2o) heterocycloalkyl, unsubstituted (C2-Cio) 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 optionally be present or absent 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, excluding 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): ινΐΛ / a / zuzz / uuo 11 y In formula (I), M is a metal selected from titanium, zirconium, or hafnium, and the metal is in a formal oxidation state of +2, +3, or +4; n is 0 or 2; when n is 1, X is 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 has an overall neutral charge; each Z is independently selected from -O-, -S-, -N(RN)-, or -P(RP)-; L is hydrocarbylene (Ci-Co) or heterohydrocarbylene (Ch-Co), 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 heteroatom, wherein each heteroatom is independently O, S, S(O), S(O)2, Si(Rc)2, Ge(Rc)2, P(RC) or N(Rc) , wherein each Rces independently hydrocarbyl (C1-C30) or heterohydrocarbyl (C1-C30) ;R1 and R8 are independently selected from the group consisting of -H, hydrocarbyl (C1-C40) λ heterohydrocarbyl (Ci-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=N-, RcC(O)O-, RcOC(O)-, RcC (0)N(RN)-, (Rn)2NC(O)-, halogen and radicals having formula (II), formula (III) or formula (IV):; In formulas (II), (III) and (IV), each R31~35, R41-48 or R5159 is chosen independently of 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) —, (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, R5-7 and R9-16 is independently selected from hydrocarbyl (C1-C40), heterohydrocarbyl (C1-C40), -Si(Rc)3, -Ge(Rc)3, -P(R?)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 polyethylene composition is formed by a first catalyst according to formula (I) in a first reactor and a different catalyst according to formula (I) in a second reactor. In an illustrative embodiment using a double-loop reactor, the procatalyst used in the first loop is [[2,2^^^-[[bis[1-methylethyl)germilen]bis(methylenexikO) ]bis[3'',5,5''-tris(1,1-dimethylethyl)-5'-octyl[l,l' :3',1,,_terphenyl]-2'-olate-κθ]](2-)]dimethyl zirconium, which has the chemical formula C86Hi28F2GeO4Zr and the following structure (V): In this embodiment, the procatalyst used in the second loop is [[2,2'' '-[1,3-propanediylbis(oxy-κθ)]bis[3-[2,7bis(1,1-dimethylethyl)-9H-carbazol-9-yl]]-5' (dimethyloctylsilyl)-3'-methyl1-5-(1,1,3,3-tetramethylbutyl)[1,1]-biphenyl]-2-olate-KO]](2-)]dimethyl zirconium, which has the chemical formula Ci07Hi54N2O4Si2Zr and the following structure (VI): 1 1(VI) In another embodiment, the procatalyst used in the second loop is [ [2,2'''-[1,3-propanediylbis(oxy-κθ)]bis[3-[2,7bis(1,1-dimethylethyl)-9H-carbazol-9-yl]]-5'(dimethyloctylsilyl)-3'-methyl1-5-(1,1,3,3-tetramethylbutyl)[1,1]-biphenyl]-2-olate-KO]](2-)]dimethyl hafnium, which has the chemical formula C107H154N2O4Si2Zr and the following structure (VII): (VII) Cocatating component The catalyst system comprising a metal-ligand complex of formula (I) can be made catalytically active by any technique known in the art of activating metal-based catalysts for polymerization reactions of definites. 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 potentiostatic coulometry. 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, modified triisobutylaluminum methylalumoxane, and isobutylaluminumoxane. Lewis acid activators (cocatalysts) include group 13 metal compounds containing one to three (C1-C20) hydrocarbyl substituents, as described herein. In one embodiment, the group 13 metal compounds are tri(hydrocarbyl(C1-C20))-substituted aluminum or tri(hydrocarbyl(C1-C20))-boron compounds. In other embodiments, the group 13 metal compounds are tri(hydrocarbyl)-substituted aluminum, tri(hydrocarbyl(C1-C20))-boron, tri(alkyl(C1-C10))-aluminum, tri(aryl(Cg-Cs))-boron compounds, and halogenated (including perhalogenated) derivatives thereof. In further embodiments, the 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 ινΐΛ / a / zuzz / uuo 11 and tetrafluoroborate) or tri(hydrocarbyl(C1-C20)ammonium tetra(hydrocarbyl(C1-C20)borate) (e.g., bis(octadecyl)methylammonium tetrakis(pentafluorophenyl)borate). As used in the present description, the term ammonium means a nitrogen cation that is a (hydrocarbyl(C1-C20))4N+, a (hydrocarbyl(C1-C20))3N(H)+, a (hydrocarbyl(C1-C20))2N(H)2+, or a hydrocarbyl(C1-C20)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(Ci-C4))aluminum compound and a halogenated tri(aryl(Cg-Cis))boron, especially a tris(pentafluorophenyl)borane. Other embodiments are 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 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 cocatalysts include, but are not limited to: modified methyl aluminoxane (MMAO), bis(hydrogenated tallow alkyl)methyl, tetrakis(pentafluorophenyl)borate(1)amine, and combinations thereof. In some embodiments, one or more of the above activation cocatalysts are used in combination with each other. A particularly preferred combination is a mixture of a tri(hydrocarbyl(Ci-C4))aluminum, tri(hydrocarbyl(Ci-C4))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 1:5,000; in some other embodiments, at least 1:1,000; and 10:1 or less, and in some other embodiments, 1:1 or less. When an alumoxane is used alone as an activation cocatalyst, the number of moles of aluminum employed is at least 10 times the number of moles of the metalligand complex of formula (I).For example, when tris(pentafluorophenyl)borane can be used alone as an activation cocatalyst, in some other embodiments, the number of moles of tris(pentafluorophenyl)borane employed with respect to the total number of moles of one or more metal-ligand complexes of formula (I) is from 0.5:1 to 10:1, from 1:1 to 6:1, or from 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). Movies In some embodiments, the embodiments described herein relate to films formed from any of the polyethylene compositions described herein, as described herein. In some embodiments, the film may be a blown film or a cast film. In some embodiments, the film may be an extrusion-coated film. In some embodiments, the film may be machine-oriented blown film or a retaining-frame-oriented cast film. In some embodiments, the film may be a single-layer film. In some embodiments, the film may be a multi-layer film. In some embodiments of multi-layer films that include the polyethylene compositions described herein, a multi-layer film may include a polyethylene composition of the description herein in a surface layer and / or in an inner layer.In certain embodiments, the polyethylene compositions described herein may be in a sealing layer of a multilayer film, wherein the application of the polyethylene composition described herein to at least one surface of a substrate layer thereby forms a sealing layer associated with that at least one surface of the substrate layer. The sealing layer may be applied to the substrate layer of a blown film or a cast film, for example, by a coextrusion process. In certain embodiments, the sealing layer may be applied directly to the substrate layer as an extrusion coating. A sealing layer may provide a heat-sealable surface. As used herein, a heat-sealable surface is a surface that allows the film surface to be heat-sealed to another surface of the same film or to the surface of another film or substrate. In one or more embodiments, the polyethylene compositions described herein may be blended with other polymers, such as other polyethylenes or even other polymers that are not polyethylene-based. For example, the polyethylene compositions described herein may be blended with conventional polyethylene compositions such as, but not limited to, LDPE, LLDPE, and / or HDPE, known to those skilled in the art. The amount of polyethylene composition to be used in films of the present modalities may depend on several factors including, for example, whether the film is a single-layer or multi-layer film, the other layers in the film if it is a multi-layer film, the end-use application of the film, and others. The films described herein may have a variety of thicknesses. The film thickness may depend on several factors, including, for example, whether the film is a single-layer or multi-layer film, the other layers in the film if it is a multi-layer film, the desired properties of the film, the film's end-use application, the equipment available for manufacturing the film, and others. In some embodiments, a film described herein has a thickness of up to 10 mils. For example, the film may have a thickness from a lower limit of 0.25 mils, 0.5 mils, 0.7 mils, 1.0 mil, 1.75 mils, or 2.0 mils to an upper limit of 4.0 mils, 6.0 mils, 8.0 mils, or 10 mils. In different versions, the film can have a thickness of 0.25 mils to 2.0 mils, 0.25 mils to 1.75 mils, 0.25 mils to 1.0 mils, 0.25 mils to 0.7 mils, 0.25 mils to 0.5 mils, 0.5 mils to 2.0 mils, 0.5 mils to 1.75 mils, 0.5 mils to 1.0 mils, 0.5 mils to 0.7 mils, from 0.7 mils to 2.0 mils, from 0.7 mils to 1.75 mils, from 0.7 mils to 1.0 mils, from 1.0 mils to 2.0 mils, from 1.0 mils to 1.75 mils, from 1.75 mils to 2.0 mils, or any combinations. In formulations where the film comprises a multilayer film, the number of layers can depend on several factors, including, for example, the desired film properties, the desired film thickness, the content of the other film layers, the film's end-use application, the equipment available for film manufacturing, and others. A multilayer blown film can comprise up to 2, 3, 4, 5, 6, 7, 8, 9, 10, or 11 layers in various formulations. The polyethylene compositions, in some embodiments, can be used in more than one layer of the film. Other layers within a multilayer film of the present description may comprise, in various embodiments, a polymer selected from the following: the polyethylene compositions described herein, an LLDPE, a VLDPE (very low-density polyethylene), an MDPE, an LDPE, an HDPE, an HMWHDPE (high molecular weight HDPE), a propylene-based polymer, a polyolefin plastomer (POP), a polyolefin elastomer (POE), an olefin block copolymer (OBC), ethylene vinyl acetate, ethylene acrylic acid, ethylene methacrylic acid, ethylene methyl acrylate, ethylene ethyl acrylate, ethylene butyl acrylate, isobutylene, a polyolefin grafted with maleic anhydride, an ionomer of any of the foregoing, or a combination thereof.In some embodiments, a multilayer film of the present description may comprise one or more bonding layers known to those skilled in the art. In additional embodiments of the polyolefin films described herein, other layers may be bonded, for example, to a polyethylene film by means of a bonding layer (sometimes in addition to an insulating layer). A bonding layer may be used to bond layers of different materials. For example, an insulating layer comprising ethylene vinyl alcohol (EVOH) may be bonded to a polyethylene material by means of a bonding layer (i.e., a bonding layer comprising polyethylene grafted with maleic anhydride). For example, the polyolefin film may further comprise other layers typically included in multilayer structures depending on the application, including, for example, other insulating layers, structural or strength layers, sealing layers, other bonding layers, other polyethylene layers, polypropylene layers, etc.In additional versions, a printed layer, which can be a layer of ink applied to the film, may be included to display product details and other packaging information in various colors. It is understood that any of the above layers may further comprise one or more additives known to those skilled in the art, such as, for example, antioxidants, ultraviolet light stabilizers, heat stabilizers, slip agents, antiblocking agents, pigments or colorants, processing aids, crosslinking catalysts, flame retardants, fillers, and foaming agents. In some embodiments, polyethylene compositions comprise up to 5 percent by weight of such additional additives. All individual values ​​and sub-ranges from 0 to 5 percent by weight are included and described herein; for example, the total amount of additives in the polymer blend may be from a lower limit of 0, 0.5, 1, 1.5, 2, or 2.5 percent by weight to an upper limit of 1.5, 2, 2.5, 3, 3.5, 4, 4.5, or 5 percent by weight.In various formulations, the total amount of additives in the polymer mixture can be from 0% to 5% by weight, 0% to 4.5% by weight, 0% to 4% by weight, 0% to 3.5% by weight, 0% to 3% by weight, 0% to 2.5% by weight, 0% to 2% by weight, 0% to 1.5% by weight, 0% to 1% by weight, 0% to 0.5% by weight, 0.5% to 5% by weight, 0.5% to 4.5% by weight, 0.5% to 4% by weight, 0.5% to 3.5% by weight, 0.5% to 3% by weight, 0.5% to 2.5% by weight, 0.5% by weight 2% by weight, 0.5% by weight to 1.5% by weight, 0.5% by weight to 1% by weight, 1% by weight to 5% by weight, 1% by weight to 4.5% by weight, 1% by weight to 4% by weight, 1% by weight to 3.5% by weight, 1% by weight to 3% by weight, 1% by weight to 2.5% by weight, 1% by weight to 2% by weight, 1% by weight to 1.5% by weight, 1.5% by weight to 5% by weight, 1.5% by weight to 4.5% by weight, 1.5% by weight to 4% by weight, 1.5% by weight to 3.5% by weight. 1.5% by weight to 3% by weight, 1.5% by weight to 2.5% by weight, 1.5% by weight to 2% by weight, 2% by weight to 5% by weight, 2% by weight to 4.5% by weight, 2% by weight to 4% by weight, 2% by weight to 3.5% by weight, 2% by weight to 3% by weight, 2% by weight to 2.5% by weight, 2.5% by weight to 5% by weight, 2.5% by weight to 4.5% by weight, 2.5% by weight to 4% by weight, 2.5% by weight to 3.5% by weight, 2.5% by weight to 3% by weight, 3% by weight to 5% by weight, 3% by weight to 4.5% by weight, 3% by weight to 4% by weight, 3% by weight to 3.5% by weight weight, 3.5% by weight to 5% by weight, 3.5% by weight to 4.5% by weight, 3.5% by weight to 4% by weight, 4% by weight to 5% by weight, 4% by weight to 4.5% by weight or 4.5% by weight to 5% by weight, or any combination of these ranges. Being polyethylene compositions, the polyethylene compositions described herein, according to certain embodiments, can be incorporated into multilayer films and articles composed primarily, if not substantially or entirely, of polyolefins or, more preferably, of polyethylene, to provide a film and article that are more readily recyclable. The polyethylene-based compositions described herein are particularly advantageous for providing films where the film is formed primarily from polyethylene. For example, a single-layer or multilayer film where the film comprises primarily polyethylene may have an improved recyclability profile, in addition to other advantages that the use of such polymers may provide. In some embodiments, the film comprises 90% by weight or more of polyethylene based on the total weight of the film.In other forms, the film comprises 91% by weight or more, 92% by weight or more, 93% by weight or more, 94% by weight or more, 95% by weight or more, 96% by weight or more, 97% by weight or more, 98% by weight or more, or 99% by weight or more of polyethylene depending on the total weight of the film. In some embodiments, the film comprising a layer formed from the polyethylene compositions described herein may be laminated to another film substrate. The substrates may include films comprising polyester, nylon, polypropylene, polyethylene, and combinations thereof. For preferred recyclability substrates, the laminated structure may include a biaxially oriented polyethylene (BOFE) substrate, a machine-oriented polyethylene (MDO) substrate, or a coextruded polyethylene film. The films described herein, in some forms, can be corona-treated and / or printed (e.g., reverse or surface printing) using techniques known to those skilled in the art. In some forms, the films of the present description can be oriented uniaxially (e.g., in the direction of the machine) or biaxially by means of techniques known to those skilled in the art. In certain forms, films including the polyethylene compositions of the present description prepared according to the method described below can be sealed in accordance with ASTM F88 and have a heat seal initiation temperature of 40°C to 80°C, for example, at a dwell time of 0.5 seconds, a sealing bar pressure of 40 psi, after at least 24 hours, and peel off at a rate of 10 inches / min.The maximum load measured during peeling can be determined at multiple sealing temperatures and the temperature at which an average maximum load of 2 lb is reached, which is defined as the heat-sealing initiation temperature. For example, in various forms, multilayer films including the polyethylene compositions of the present description prepared according to the method described below may have a heat-sealing initiation temperature of 40°C to 80°C, 40°C to 70°C, 40°C to 60°C, 40°C to 50°C, 50°C to 80°C, 50°C to 70°C, 50°C to 60°C, 60°C to 80°C, 60°C to 70°C, 70°C to 80°C, or any combinations thereof. Similar methods can be used to observe the initiation temperature of heat sealing of monolayer films and other multilayer films.In some cases, single-layer and other multi-layer films may have lower heat-sealing initiation temperatures than comparable films that do not use the polyethylene compositions described herein. The polyethylene compositions described herein may provide films with relatively high densities and relatively low heat-sealing initiation temperatures. In certain applications, films containing the polyethylene compositions described herein, prepared according to the methods described below, may have a hot adhesion initiation temperature of 50°C to 90°C, measured according to ASTM F1921 (Method B), for example, by creating a seal 0.5 inches deep and 1 inch wide and applying 0.275 N / mm² of pressure for 0.5 seconds. After, for example, a dwell time of 0.18 seconds, the sealed region may peel off at a speed of 200 mm / s. The maximum load measured during peeling may be determined at multiple sealing temperatures, and the temperature at which an average maximum load of 4 N is reached is defined as the hot adhesion initiation temperature.In certain embodiments, films incorporating the polyethylene compositions described herein, prepared according to the method described below, may have a hot bond initiation temperature of 50°C to 90°C, 50°C to 80°C, 50°C to 70°C, 50°C to 60°C, 60°C to 90°C, 60°C to 80°C, 60°C to 70°C, 70°C to 90°C, 70°C to 80°C, 80°C to 90°C, or any combination thereof. Similar methods may be used to determine the hot bond initiation temperature of single-layer and other multi-layer films. In certain embodiments, single-layer and other multi-layer films may have lower hot bond initiation temperatures than comparable films not using the polyethylene compositions described herein.The polyethylene compositions described herein can provide films with relatively high densities and relatively low hot bond initiation temperatures. In some versions, films incorporating the polyethylene compositions described herein may have a blocking strength of less than 40 mN / in or less than 35 mN / in, measured according to the methods described below. Similar methods may be used to determine the blocking strength of single-layer and other multi-layer films. In some versions, single-layer and other multi-layer films may have a blocking strength comparable to or less than that of comparable films not using the polyethylene compositions described herein. Articles The forms described herein also apply to articles, such as containers, formed from or incorporating polyethylene compositions of this description (i.e., through films incorporating polyethylene compositions of this description). Such containers may be formed from any of the polyethylene compositions of this description (i.e., through films incorporating polyethylene-based compositions of this description) described herein. Such containers formed from any of the polyethylene compositions of this description may be sealed by various sealing methods known in the art, such as heat-sealing methods. Examples of such articles may include flexible packaging, pouches, bottom-lined bags, and pre-made pouches or containers. In some embodiments, the multilayer films or laminates described herein may be used for food packaging. Examples of foods that may be included in such packaging include meats, cheeses, cereals, nuts, snacks, juices, sauces, and others. Such packaging may be formed using techniques known to those skilled in the art, based on the teachings herein and the specific use of the packaging (e.g., type of food, quantity of food, etc.). Low heat-sealing initiation temperatures, such as those provided by the polyethylene compositions of the present invention, can be particularly desirable for automated packaging systems where the item to be packaged is loaded into the package as it is manufactured. Lower heat-sealing initiation temperatures can be advantageous for increasing packaging productivity by minimizing the time and energy required to heat and cool a sealer. In the case of recyclable polyethylene, packaging with an inner sealing layer that seals at a significantly lower temperature than the outer polyethylene layer can allow for a wider temperature range for producing heat-sealed packages, which may often be referred to as the packaging heat-sealing window.Some examples of such automated packaging equipment are called vertical form fill and seal (VFFS) machines or horizontal form fill and seal (HFFS) machines. TEST METHODS Unless otherwise stated in this description, the following analytical methods are used to describe aspects of this description: fusion index The melting indices I2(o 12) and lio(o 110) of polymeric samples were measured according to ASTM D-1238 (method B) at 190 °C and a load of 2.16 kg and 10 kg, respectively. Their values ​​are reported in g / 10 min. 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. Method for measuring viscosity at zero shear using creep 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. Steady state is determined by performing a linear regression on all data within the last 10% time window of the log(J(t)) vs. log(t) plot, 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 be reached, and the yield test is 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 ε vs. t plot, 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 creep test, a small-amplitude oscillatory shear test is performed on the same sample before and after the creep test 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 creep 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. The autosampler oven compartment was set at 160° Celsius, and the column compartment at 150° Celsius. The columns used were four 30-cm Agilent Mixed A linear mixed-bed columns, each 20 µm thick, 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 assembly was performed using 21 narrow molecular weight distribution polystyrene standards with molecular weights ranging from 580 to 8,400,000 were distributed into 6 cocktail mixtures with at least a decade's separation between individual molecular weights. The standards were purchased from Agilent. Technologies. Polystyrene standards were prepared at a rate 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 11°C 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. Sci., Polym. Let., 6, 621 (1968)): ^polyethylene X ^Mpolystyrene) (Eq. 1) 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 was made (from approximately 0.375 to 0.445). 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 Plate count = 5.54* (|----RVMax.of peak----j (Eq.2) \ Peak width to-height / 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. e-. ' Posterior peak RTwelfth in height-^Max peaky Symmetry = (---------—------:--------------—) (Eq. 3) Ü^Max. of peak~PlC0(interior RVeleventh of height where RV is the retention volume in milliliters and the peak width is in milliliters, peak maximum is the maximum position of the peak, one-tenth of height is 1 / 10 of the peak maximum height, and where trailing peak refers to the tail of the peak at retention volumes after the peak maximum and where leading peak refers to the front of the peak at retention volumes before the peak maximum. 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. The calculations of Mn(GpC), Mw(GPG) and Mz(GPG) were based on GPC results using the internal IR5 detector (measurement channel) of the PolymerChar GPC-IR chromatograph according to Equations 4-6, using PolymerChar GPCONe™ software, the IR chromatogram in which the baseline was subtracted at each equally spaced data collection point (i), and the equivalent molecular weight of polyethylene obtained from the narrow calibration curve of standards for point (i) of Equation 1. Mn^GPC) (Eq. 4) Mw(gpc) = (Eq. 5) 'in polyethylene^ Mz(gpc) . * M polyethylene^ (Eq. 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 measuring the flow rate (VR) of the flow marker peak, a least-squares fitting routine was used to fit the flow marker concentration chromatogram peak to a quadratic equation. The first derivative of this quadratic equation was then used to determine the true peak position. After calibrating the system against a flow marker peak, the effective flow rate (relative to the tight calibration of standards) was calculated using Equation 7. Processing of the flow marker peak 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(Calibrated FM) / RV(Sample FM)) (Eq. 7) Improved method for comonomer content distribution analysis (iCCD) In 2015, an improved method for comonomer content analysis (iCCD) was developed (Cong and Parrott et al., WO2017040127A1). 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 (Precision Detectors, now Agilent Technologies). A 20–27 µm 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 upstream of 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 was 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 equilibration at 30 °C for 2 minutes (including the soluble fraction elution time, set at 2 minutes), 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 1 / 4 (ID) stainless steel tube. The column was packed and conditioned 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 (l2) of 1.0, and a polydispersity Mw / Mnde 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. It should be noted that this temperature shift is a function of experimental conditions such as elution temperature, elution flow rate, etc.; (3) Creating a linear calibration line that transforms the elution temperature across a range of 30.00 °C to 140 °C.00 °C, such that the linear polyethylene homopolymer reference has a peak temperature of 101.0 °C, and the 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 Cong et al., US9,688,795). Comonomer content versus iCCD elution temperature was plotted using 12 reference materials (ethylene homopolymer and ethylene-octene random copolymer prepared with a single-site metallocene catalyst, having an equivalent weighted average molecular weight of ethylene ranging from 35,000 to 128,000). All of these reference materials were analyzed as specified above 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% of 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 (Strieggel 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 were set to integrate all chromatograms within the elution temperature range (temperature calibration specified above) of 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 displacement of the volume between the LS and the concentration detector. It is calculated as the difference in the elution volume (mL) of the polymer peak between the concentration detector and the LS chromatograms. It is converted to a temperature displacement 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 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 (SF) 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. ML / a / ZUZZ / UUO 11 a (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 sample of HDPE with known MW 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 calculation of half the width is defined as the temperature difference between the temperature before and after the half height of the peak; the temperature before the half height of the peak is looked up from 35.0 °C, while the temperature after the half height of the peak is looked up from 119.0 °C. Zero Shear Viscosity Ratio (ZSVR) The ZSVR is defined as the ratio between the zero shear viscosity (ZSV) of the branched polyethylene material and the ZSV of the linear polyethylene material at the equivalent weighted average molecular weight (Mw-gpc) according to the following Equations 8 and 9: ZSVR =ηο1- (Eq. 8) ηη. = 2.29x1015M365 / °í «-gpc(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 WL, Reichek, Kenneth N., Detection of low levels of long-chain branching in polyolefins, Annual Technical Conference - Society of Plastics Engineers (2008), 66th 887891. Locking force Locking strength measurements are sensitive to the thermal history of the film samples. The films were produced on a Labtech 5-ply blown film line (as further described in Example 5 below). The blown films collapsed at the grip point after the bubble and were not separated and were cut into two strips. The samples tested for locking strength were manufactured, stored, and tested at a temperature of 23 ± 2 °C. First, 6-in. x 1-in. strips were punched from the collapsed bubble of film, with the longer dimension along the machine direction. Lengths of approximately one inch from the two layers were separated by hand at one edge. The separated layers were clamped in the grips of an Instron frame (initial grip separation = 1.5 in.) and separated at a rate of 1 in. / min (180° peel).The test continued until an additional 4 inches of the layers separated. The force-displacement curve was recorded during the test. Initially, the force increased rapidly and then stabilized. The stabilizing force is a measure of the locking force. A few force peaks may be observed as the layers separated. These peaks may be due to improper cutting of the films, leaving random spots along the sample length that stuck together. To avoid falsely exaggerating the locking force due to these peaks, the most frequent force value in the stabilizing region (Mode) was taken as the locking measure instead of the average (Mean). At least five samples of each collapsed bubble were evaluated. The results are reported as the mean ± standard deviation of the measured locking force of all samples. Hot bonding initiation temperature Hot adhesion refers to the strength of a heat seal formed between films after the seal has been made and before it cools to room temperature. The hot adhesion test can be used to determine the seal strength and appropriate sealing parameters for a heat-sealing process. The hot adhesion initiation temperature was measured in accordance with ASTM F1921 (Method B). Heat sealing start temperature The heat seal test can be used to determine the appropriate sealing parameters (such as sealing temperature, dwell time, and pressure) for a film. The heat seal initiation temperature was measured in accordance with ASTM F-88 (Technique A). Dynamic shear rheology The samples were compression molded at 190 °C for 6.5 minutes at a pressure of 25,000 lb in air, and the plates were then cooled on a laboratory bench. The plate thickness was approximately 3 mm. Constant-temperature frequency sweep measurements were performed on an ARES (TA Instruments) controlled-strain parallel-plate rheometer equipped with 25 mm parallel plates under nitrogen purge. For each measurement, the rheometer was thermally equilibrated for at least 30 minutes before zeroing the space. The sample was placed on the plate and allowed to melt for five minutes at 190 °C. The plates were then closed to 2 mm, the sample was trimmed, and the test was initiated. The method had an additional five-minute delay to allow for temperature equilibration. Experiments were performed at 190 °C over a frequency range of 0.1–100 rad / s at five points per decade interval.The strain amplitude was constant at 10%. The stress response was analyzed in terms of amplitude and phase, from which the storage modulus (G'), loss modulus (G), complex modulus (G*), dynamic complex viscosity (η*) and tan (δ) or tangent delta were calculated. Examples Example 1: Preparation of polyethylene compositions 1-3 Polyethylene Compositions 1-3, which are described according to one or more of the detailed descriptions, were prepared using a method and with the catalysts and reactors described below. All raw materials (monomer and comonomer) and the process solvent (a high-purity, narrow-boiling-range isoparaffinic solvent, isopar-E) were purified using molecular sieves before being introduced into the reactor. The catalyst components were injected into the reactor at two injection sites with approximately equal reactor volumes between them. The fresh feed was controlled so that each injector received half of the total fresh feed mass flow. The catalyst components were injected into the polymerization reactor through injection needles. The catalyst feed was computer-controlled to maintain each monomer conversion within the reactor at the specified targets. The cocatalyst components were fed according to specified molar ratios calculated with respect to the primary catalyst component.Immediately after each reactor feed injection point, the feed streams were mixed with the circulating polymerization reactor contents using static mixing elements. The contents of each reactor were continuously circulated through heat exchangers responsible for removing much of the heat of reaction, while the coolant temperature on the coolant side maintained an isothermal reaction environment at the specified temperature. A pump provided circulation around each reactor loop. The effluent from the first polymerization reactor (containing solvent, monomer, comonomer, hydrogen, catalyst components, and polymer) came out of the first reactor loop and was added to the second reactor loop. The effluent from the second reactor entered a zone where it was deactivated by the addition of, and reaction with, a suitable reagent (water). At this same reactor outlet, other additives were added for polymer stabilization (typical antioxidants suitable for stabilization during extrusion and film manufacturing such as octadecyl 3,5-di-tert-butyl-4-hydroxyhydrocinnamate, tetrakis(methylene(3,5-di-tert-butyl-4-hydroxyhydrocinnamate))methane, and tris(2,4-di-tert-butylphenyl)phosphite). After catalyst deactivation and additive addition, the reactor effluent entered a devolatilization system where the polymer was removed from the non-polymer stream. The isolated polymer melt was pelletized and collected. The non-polymer stream passed through various pieces of equipment, which separated most of the ethylene, removing it from the system. Most of the unreacted solvent and comonomer was recycled back to the reactor after passing through a purification system. A small amount of solvent and comonomer was purged from the process. The reactor feed stream data flows correspond to the values ​​in Table 1. The data are presented in a way that takes into account the complexity of the solvent recycling system and allows the reaction system to be treated more simply as a one-step flow diagram. Table 2 shows the catalysts mentioned in Table 1. ινΐΛ / a / zuzz / uuo 11 a Table 1 Polyethylene Composition Polyethylene Composition 1 Polyethylene Composition 2 Polyethylene Composition 3 Reactor Configuration Type Twin Series Twin Series Twin Series Comonomer Type Type 1-octene 1-octene 1-octene Solvent / ethylene feed mass flow ratio of first reactor g / g 3.7 3.7 3.8 Comonomer / ethylene feed mass flow ratio of first reactor g / g 0.86 0.86 0.75 Hydrogen / ethylene feed mass flow ratio of first reactor g / g 1.5E-04 1.8E-04 1.8E-04 Temperature of first reactor °c 165 165 165 Pressure of first reactor barg 50 50 50 Ethylene conversion of first reactor % 86.1 87.1 91.5 Catalyst type of the first reactor Type Catalyst component B Catalyst component B Catalyst component B Catalyst metal of the first reactor Type Zr Zr Zr Cocatalyst type 1 of the first reactor Type Cocatalyst A Cocatalyst A Cocatalyst A Cocatalyst type 2 of the first reactor Type Cocatalyst B Cocatalyst B Cocatalyst B. Molar ratio between cocatalyst 1 and catalyst of the first reactor (ratio between B and metal) Ratio 1.2 1.2 1.2 Molar ratio between cocatalyst 2 and catalyst of the first reactor (ratio between Al and metal) Ratio 12.7 14.6 153.0 Residence time of the first reactor min 10.6 10.8 11.7 Mass flow ratio of solvent / ethylene feed of the second reactor g / g 1.9 1.9 2.0 Mass flow ratio of comonomer / ethylene feed of the second reactor g / g 0.271 0.268 0.194 Mass flow ratio of hydrogen / ethylene feed of the second reactor g / g 0.2E-04 4.1E-05 3.6E-04 Temperature of the second reactor °C 190 190 190 Pressure of the second reactor barg 50 50 50 Ethylene conversion of the second reactor % 84.4 84.3 85.6 Catalyst type of the second reactor Type Catalyst component C Catalyst component C Catalyst component E Catalyst metal of the second reactor Type Hf Hf Zr Cocatalyst type 1 of the second reactor Type Cocatalyst A Cocatalyst A Cocatalyst A Cocatalyst type 2 of the second reactor Type Cocatalyst B Cocatalyst B Cocatalyst B. Molar ratio between cocatalyst 1 and catalyst of the second reactor (ratio between B and metal) Molar ratio between cocatalyst 2 and catalyst of the second reactor (ratio between Al and metal) mol / mol mol / mol 6.2 235.0 6.6 243.0 6.0 101.0 Residence time of the second reactor min 7.5 7.5 7.7 Table 2 Catalyst compound B 5 | 65 o ° V £ yy XX y 65 65 c J c Catalyst component C χ τ XX / X / ' xs X / 7 Me Me t-Bu λ—k ? J—λ t-Bu \\ X X7 ¿X XA .If If Me 1 1 Me x-—' Me Me Component catalyst E ^X .t-Bu t-Bu Jij XX\ Cjy Me Me \X t-Bu^^ í-k VJ—x t-Bu J1 Χ'θ,ι'χΖ'Γ'Γ'X\'°X\'X\'X\'. j^. / 'Me Me Me 1 | 'Me Me Me Cocatalyst A fF. F MHB-V iF If Cocatalyst B Modified methyl aluminoxane ινΐΛ / a / zuzz / uuo 11 y Example 2: comparative compositions AG Table 3 identifies the commercially available polyethylene compositions of the AG Comparative Polyethylene Compositions. Table 3 Comparative Polyethylene Composition Trade Name (Manufacturing Company) A EXCEED 1012 (ExxonMobil) B ELITE™ AT 6101 (Dow Chemical Co.) C ELITE™ AT 6202 (Dow Chemical Co.) D AFFINITY™ PL 1880G (Dow Chemical Co.) E AFFINITY™ PF 1140G (Dow Chemical Co.) F ELITE™ 5500G (Trade number 1) (Dow Chemical Co.) G ELITE™ 5500G (Trade number 2) (Dow Chemical Co.) Example 3: Analysis of Polyethylene Compositions 1-3 from Example 1 and Comparative AG Polyethylene Compositions from Example 2 Polyethylene compositions 1-3 from Example 1 and comparative polyethylene compositions AG from Example 2 were analyzed using iCCD. The iCCD data generated for all samples (polyethylene composition 1 from Example 1 and comparative polyethylene compositions AG) are provided in Tables 4A and 4B. Specifically, Table 4A includes the analysis of the iCCD data at 5 °C temperature increments. ινΐΛ / a / zuzz / uuo 11 y Table 4A Sample ID 25 °C-70 °C 70 °C-85 °C 85 °C-120 °C Comp. comparative PE A 30.19% 57.67 % 12.14% Comp. comparative PE B 45.79 % 53.42 % 0.79 % Comp. comparative PE C 39.91 % 57.71 % 2.39 % Comp. comparative PE D 70.79 % 28.68 % 0.52 % Comp. comparative PE E 86.99% 11.75% 1.25% Comp. comparative PE F 46.52 % 22.11 % 31.37% Comp. comparative PE G 45.83 % 23.15% 31.02% Comp. of PE 1 60.29 % 3.15% 36.56 % Comp. of PE 2 60.15% 2.70 % 37.16% Comp. of PE 3 59.55% 4.65% 35.80% Table 4B further outlines the iCCD data to include the areas of the respective polyethylene fractions (25 °C35 °C, 35 °C-70 °C, 70 °C-85 °C and 85 °C-120 °C). Table 4B Weight percentage (% wt) in each temperature zone Sample ID 20 °C-35 °C 35 °C-70 °C 70 °C-85 °C 85 °C-120 °C Comparative Comparison of PE A 0.27% 29.93% 57.67% 12.14% Comparative Comparison of PE B 2.38% 43.40% 53.42% 0.79% Comparative Comparison of PE C 0.60% 39.30% 57.71% 2.39% Comp. comparative PE D 0.46 % 70.34 % 28.68 % 0.52 % Comp. comparative PE E 4.47 % 82.52 % 11.75% 1.25% Comp. comparative PE F 1.85% 44.67 % 22.11 % 31.37% Comp. comparative PE G 1.68% 44.15% 23.15% 31.02% Comp. of PE 1 10.08% 50.21 % 3.15% 36.56 % Comp. of PE 2 11.88% 48.27% 2.70% 37.16% Comp. of PE 3 25.92% 33.63% 4.65% 35.80% As shown in Tables 4A and 4B, the samples of Polyethylene Compositions 1–3 showed the highest percentage in the 85–120 °C range and the lowest percentage in the 70–85 °C range. Furthermore, none of the samples of Comparative Polyethylene Compositions A, B, C, F, or G showed a polyethylene fraction from 70–85 °C comprising less than 10% of the total elution profile area. Additionally, Comparative Polyethylene Compositions D and E did not show a polyethylene fraction from 85–120 °C comprising at least 20% of the total elution profile area. Table 5 provides additional data for each sample of the AG Comparative Polyethylene Compositions and the 1-3 Polyethylene Compositions, including total density, melt index, ZSVR, and the ratio of the molecular weight of the first fraction to the total molecular weight. These properties were measured according to the test methods described herein. Table 5. PE Sample Density (g / cm3) Melting Index (g / w min) ZSVR Total Mw (LS90) (g / mol) Mw of the first fraction Mw of the highest density fraction Ratio between the molecular weight of the first fraction and the total molecular weight Mw / Mn A 0.912 1.0 - 117,773 117,854 - 1.00 2.43 B 0.905 0.80 - 107,188 109,408 - 1.02 3.15 C 0.910 0.85 - 120,142 126,839 104,834 1.06 2.45 D 0.902 1.0 4.58 107,073 107,246 - 1.00 2.34 E 0.896 1.6 - 101,413 104,718 - 1.03 2.09 F 0.914 1.5 - 107,994 115,834 90,110 1.00 3.03 G 0.914 1.5 - 111,730 111,817 97,210 1.07 2.98 0.9033 1.0 1.38 119,555 127,135 125,491 1.06 2.22 0.9035 1.0 1.27 119,224 109,963 - 0.92 2.18 0.904 3.0 1.08 90,590 95,944 99,409 1.06 2.32 As mentioned earlier in this description, tangent delta (tan δ) is a measure of how close a material is to a perfectly elastic solid (where d = 0°, tangent delta = 0) or how close a material is to a perfectly Newtonian fluid (where d = 90°, tangent delta ~ infinity). Therefore, lower tangent d values ​​reflect greater elasticity. Tangent d is a function of LCB and MWD at the same total molecular weight. Higher tangent d values ​​indicate lower LCB. Table 6. Sample Tan δ (at 0.1 radians / s, 190 °C) Comp. comparison of PE A 50.3 Comp. comparison of PE B 5.9 Comp. comparison of PE C 4.9 Comp. comparison of PE D 6.3 Comp. comparison of PE E 6.04 Comp. comparison of PE F 10.4 Comp. comparison of PE G 10.4 Comp. of PE 1 27.3 Comp. of PE 2 22.3 Comp. of PE 3 80.9 As shown in Table 6, Polyethylene Compositions 1 and 2 had a tangent δ of 27.3 and 22.3, respectively. Polyethylene Composition 3 had a tangent δ of 80.9. In comparison, Comparative Polyethylene Compositions A had a tangent δ of 50.3, and Comparative Polyethylene Compositions BG had relatively lower tangent δ values ​​(5.9, 4.9, 6.3, 6.04, 10.4, 10.4, respectively). Example 4: Analysis of the heat sealing start temperature and the hot bond start temperature In Example 4, the heat sealing initiation temperature and the hot bonding initiation temperature were analyzed for films comprising the polyethylene compositions described herein. To analyze these properties, multilayer films were coextruded on a 7-layer Alpine blown film line. This line was equipped with seven 50 mm single-screw extruders with a 30 L / D and a 250 mm die. Three-layer films (surface / core / sealer) with a total thickness of 2 mils were produced. The surface / core / sealer layer thickness ratio was set at 1 / 3 / 1. The surface layer comprised an 80 / 20 (by weight) blend of DOWLEX™ 2045G / LDPE 611A, both commercially available from The Dow Chemical Company. The core layer base resin comprised the same mixture as the surface layer, but additionally with 500 ppm of 10090 Slip PE MB (erucamide, commercially available through Ampacet Corporation) and 10063 Antiblock PE MB (commercially available through Ampacet Corporation), which were added by dry mixing.The polyethylene composition used in the sealing layer varied, as detailed in Table 7. The sealing layer consisted of 750 ppm of 10090 Slip PE MB and 2500 ppm of 10063 Antiblock PE MB, introduced by dry blending. The matrix clearance was set at 78.7 mils, the blow ratio at 2.5, the melt temperature at 440–470°F, the exit rate at 350 lb / h, and the frost line height at approximately 37 inches. The multilayer film bubble was in-line cut and separated into two rolls. Table 7. Sample Sealing Layer Comparative Film A EXCEED 1012 (ExxonMobil) Comparative Film B ELITE™ AT 6101 (Dow Chemical Co.) Comparative Film C ELITE™ AT 6202 (Dow Chemical Co.) Comparative Film D AFFINITY™ PL 1880G (Dow Chemical Co.) Comparative Film E AFFINITY™ PF 1140G (Dow Chemical Co.) Film 1 Polyethylene Composition 1 (from Example 1) Film 2 Polyethylene Composition 2 (from Example 1) Film 3 Polyethylene Composition 3 (from Example 1) Next, each of Films 1-3 and Comparative Films AE was laminated onto 0.48 mil thick polyethylene terephthalate (PET) using a Nordmeccanica Super Combi 3000 laminator and an ADCOTE™ 577 / CR 87-124 solvent-based adhesive, where the ADCOTE™ 577 and CR 87-124 components were blended in a 100:7 weight ratio. Prior to applying the solvent-based adhesive, the surface side of each of Films 1-3 and Comparative Films AE was metered using a 1 kW corona discharge machine. The adhesive was applied using a 150-channel quad with an 11.5 bcm layer, producing a coating weight of 1.75 lb / rm via an etched roller, and subsequently cured at 180 °F. The films were cured at 25°C and 40% relative humidity for at least 5-7 days for complete chemical curing to produce Laminated Films 1-3 and Comparative Laminated Films AE. Hot adhesion measurements were performed on each of the laminated films 1-3 and comparative laminated films AE using a commercial Enepay testing machine in accordance with ASTM F-1921 (Method B). Prior to testing, the samples were conditioned for a minimum of 40 hours at 23°C and 50% RH according to ASTM D-618 (Procedure A). Sheets measuring 8.5 by 14 inches were cut from the film, with the longer dimension in the machine direction. Strips 1 inch wide and 14 inches long were cut from these sheets. Tests were performed on these samples at a range of temperatures, and the results were reported as maximum load as a function of temperature. The temperature stages were 5°C or 10°C, with six replicates performed at each temperature. The parameters used in the test were: a sample width of 25.4 mm (1.0 in); a sealing pressure of 0.275 N / mm²; a sealing dwell time of 0.5 s; a delay time of 0.18 s; a peel speed of 200 mm / s; and a sealing depth of 0.5 inches. A hot bond curve was created by linear interpolation of the average maximum load measured at each temperature.The minimum temperature at which an average maximum load of 4 N was reached (defined as the hot bond initiation temperature) was determined from this curve and is reported in Table 8. Heat sealing measurements were performed on each of the laminated films 1-3 and comparative laminated films AE using a commercial tensile testing machine in accordance with ASTM F-88 (Technique A). Prior to cutting, the films were conditioned for a minimum of 40 hours at 23°C (±2°C) and 50% (±10%) RH according to ASTM D-618 (Procedure A). Sheets were then cut from the film in the machine direction to a length of approximately 11 inches and a width of approximately 8.5 inches. The sheets were heat-sealed in the machine direction using a Kopp heat sealer within a specified temperature range under the following conditions: a sealing pressure of 0.275 N / mm²; a sealing dwell time of 1.0 s; and a sealing depth of 5 mm. The sealed sheets were conditioned for a minimum of 3 hours at 23°C (±2°C) and 50% (±10%) RH before being cut into one-inch strips. The samples were conditioned for a minimum of 24 hours after sealing at 23° (±2 °C) and 50% RH (±10%) before testing.For the test, the strips were loaded into the grips of a tensile testing machine at an initial separation of 2 inches and pulled at a grip separation rate of 10 inches / min at 23°C (±2°C) and 50% RH (±10%). The strips were tested without support. Five replicate tests were performed for each temperature. MA / a / ZUZZ / UUOl 1 to sealing. The maximum load measured during peel was determined at multiple sealing temperatures, and a heat-sealing curve was created by linear interpolation of the average maximum load measured at each temperature. The temperature at which an average maximum load of 2 lb was achieved (defined as the heat-sealing initiation temperature) was determined from this curve and is provided later in Table 8. ινΐΛ / a / zuzz / uuo iiy Table 8. Sample Hot adhesion initiation temperature (°C) Heat sealing initiation temperature (°C) Comparative laminated film A 100 82 Comparative laminated film B 96 82 Comparative laminated film C 98 83 Comparative laminated film D 89 76 Comparative laminated film E 81 72 Laminated film 1 74 67 Laminated film 2 74 63 Laminated film 3 76 73 As shown in Table 8, Laminated Films 13 exhibited the lowest hot bond initiation temperatures and heat seal initiation temperatures of Laminated Films 1-3 and Comparative Laminated Films AE. Example 5: Blocking force analysis In Example 5, the blocking strength was analyzed for films comprising the polyethylene compositions described herein. Blocking strength measurements can be sensitive to the thermal history of the samples. All samples tested for blocking strength were manufactured, then stored and tested at a temperature of 23 ± °C. In this example, the multilayer films were coextruded on a LabTech 5-layer blown film line. This line was equipped with two 25 mm single-screw extruders and three 20 mm or 30 L / D single-screw extruders and a 75 mm die. Two-layer films (surface and sealant) with a total thickness of 2 mils were produced. The surface / core / sealant layer thickness ratio was set at 4:1. The surface layer comprised an 80 / 20 (by weight) blend of DOWLEX™ 2045G / LDPE 611A. The polyethylene composition used in the sealant layer varied, as provided later in Table 9. ινΐΛ / a / zuzz / uuo 11 y Table 9. Sample Sealing Layer Comparative Film F AFFINITY™ PL 1880G (Dow Chemical Co.) Comparative Film G AFFINITY™ PF 1140G (Dow Chemical Co.) Comparative Film H AFFINITY™ VP 8770G (Dow Chemical Co.) Film 4 Polyethylene Composition 1 (from Example 1) Film 5 Polyethylene Composition 2 (from Example 1) The blow ratio was set to 3.0. The output speed was 40 lb / h, the distance between the gripper rollers and the die was 81 inches, the gripper roller pressure was 0.5 MPa, the outlet temperature of the sealing extruder was 230 °C, the mandrel and die outlet temperature was 230 °C, and no internal bubble cooling was used. Approximately 20 feet of the collapsed bubble was collected by hand. Six-inch by one-inch strips were then punched from a collapsed bubble of film, with the longer dimension running along the machine direction. Lengths of approximately one inch from the two layers were separated by hand at one edge. The separated layers were clamped in the grips of an Instron frame (initial grip separation = 1.5 inches) and separated at a rate of 1 inch / min (180° peel). The test continued until an additional 4 inches of the layers were separated. The force-displacement curve was recorded during the test. Initially, the force increased rapidly and then stabilized. The stabilizing force is a measure of the locking force. A few peaks in force can be observed as the layers separated.The peaks may be due to improper cutting of the films, leaving random spots along the length of the sample that adhered to one another. To avoid falsely exaggerating the blocking strength due to these peaks, the most frequent force value in the stabilization region (Mode) was taken as the blocking measure instead of the average (Mean). At least five samples were evaluated from each collapsed bubble. The results are reported in Table 10 as the mean ± standard deviation of the measured blocking strength of all samples. Table 10. Sample Locking Force (mN / in) Comparative Film F 17.511.7 Comparative Film G 32.914.0 Comparative Film H 219.3123.8 Film 4 31.9±1.4 Film 5 33.614.8 The results in Table 10 show that each of the Sample Films 4 and 5, which each include variations of the polyethylene compositions described herein, exhibit a blocking strength comparable to Comparative Film G and less than Comparative Film H. Example 6: In Example 6, the heat sealing initiation temperature and the hot bonding initiation temperature were analyzed for monolayer films comprising the polyethylene compositions described herein. To analyze these properties, monolayer films were coextruded on a LabTech 5-layer blown film line. Monolayer Film 1 was produced from Polyethylene Composition 1 of Example 1 described above. Monolayer Film 2 was produced from Polyethylene Composition 2 of Example 1 described above. Comparative Monolayer Film D was produced from Comparative Polyethylene Composition D (AFFINITY™ PL 1880G (Dow Chemical Co.)) of Example 2 described above. Comparative Monolayer Film E was produced from Comparative Polyethylene Composition E (AFFINITY™ PF 1140G (Dow Chemical Co.)) of Example 2 described above. This line was equipped with two 25 mm single-screw extruders and three 20 mm or 30 L / D single-screw extruders and a 75 mm die. Films with a total thickness of 2 mils were prepared. The die clearance was set at 78.7 mils, the blow ratio was 3.At 0, the melting temperature was 425°F-445°F, the output rate was 25-30 lb / h, and the frost line height was approximately 6-7 inches. The bubble of the monolayer film was cut in line and separated into two rolls. Hot adhesion measurements were performed on each of the Monolayer Films 1 and 2 and Comparative Monolayer Films D and E using a commercial Enepay testing machine in accordance with ASTM F-1921 (Method B). Prior to testing, the samples were conditioned for a minimum of 40 hours at 23 °C and 50% RH according to ASTM D-618 (Procedure A). Sheets measuring 8.5 by 14 inches were cut from the film, with the longer dimension running in the machine direction. Strips 1 inch wide and 14 inches long were cut from these sheets. Tests were performed on these samples at a range of temperatures, and the results were reported as maximum load as a function of temperature. The temperature stages were 5°C or 10°C, with six replicates performed at each temperature. The test parameters were as follows: a sample width of 25.4 mm (1.0 in.); a sealing pressure of 0.275 N / mm²; a sealing dwell time of 0.5 s; a delay time of 0.18 s; a peel speed of 200 mm / s; and a sealing depth of 0.5 inches. A hot bond curve was created by linear interpolation of the average maximum load measured at each temperature.The minimum temperature at which an average maximum load of 2 N was reached (defined as the hot bond initiation temperature) was determined from this curve and is reported in Table 11. Heat sealing measurements were performed on each of the Monolayer Films 1 and 2 and Comparative Monolayer Films D and E using a commercial tensile testing machine in accordance with ASTM F-88 (Technique A). Prior to cutting, the films were conditioned for a minimum of 40 hours at 23°C (±2°C) and 50% (±10%) RH according to ASTM D-618 (Procedure A). Sheets were then cut from the film in the machine direction to a length of approximately 11 inches and a width of approximately 8.5 inches. The sheets were heat-sealed in the machine direction using a Kopp heat sealer within a specified temperature range under the following conditions: a sealing pressure of 0.275 N / mm²; a sealing dwell time of 1.0 s; and a sealing depth of 5 mm. The sealed sheets were conditioned for a minimum of 3 hours at 23°C (±2°C) and 50% RH (+10%) before being cut into one-inch-wide strips. The samples were conditioned for a minimum of 24 hours after sealing at 23° (±2 °C) and 50% RH (±10%) before testing.For testing, strips were loaded into the grips of a tensile testing machine at an initial separation of 2 inches and pulled at a grip separation rate of 10 inches / min at 23°C (±2°C) and 50% RH (±10%). The strips were tested without support. Five replicate tests were performed for each sealing temperature. The maximum load measured during peeling was determined at multiple sealing temperatures, and a heat-sealing curve was created by linear interpolation of the average maximum load measured at each temperature. The temperature at which an average maximum load of 1 lb was achieved (defined as the heat-sealing initiation temperature) was determined from this curve and is provided below in Table 11. Table 11. Sample Hot adhesion initiation temperature (°C) Heat sealing initiation temperature (°C) Comparative single-layer film D 85 86 Comparative single-layer film E 70 73 Single-layer film 1 62 65 Single-layer film 2 61 65 As shown in Table 11, Monolayer Films 1 and 2 exhibited lower hot adhesion initiation temperatures and heat sealing initiation temperatures than Comparative Monolayer Films D and E. 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 this description are identified herein as preferred, illustrative, or particularly advantageous, it is envisaged that this description is not necessarily limited to these aspects. It should be noted that one or more of the following 100 claims use the term where as a transitional phrase. For the purpose of defining the present invention, it should be noted that this term is introduced in the claims as an open transitional phrase used to introduce a recitation of a series of features of the structure and should be interpreted similarly to the more commonly used open preamble expression comprising 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 description of the invention.

Claims

CLAIMS MA / a / ZUZZ / UUOl 1 a Having described the invention as above, the contents of the following claims are claimed as property:

1. A polyethylene composition characterized in that it comprises: (a) a first polyethylene fraction comprising at least one peak in a temperature range of 35 °C to 70 °C in an elution profile by means of the enhanced comonomer composition distribution analysis (iCCD) method, wherein a first polyethylene area fraction is an area in the elution profile of 35 °C to 70 °C, and wherein the area of ​​the first polyethylene fraction comprises from 25% to 65% of the total area of ​​the elution profile;(b) a second polyethylene fraction comprising at least one peak in a temperature range of 85°C to 120°C in the elution profile by means of the iCCD analysis method, wherein a second polyethylene area fraction is an area in the elution profile from 85°C to 120°C, and wherein the area of ​​the second polyethylene fraction comprises at least 20% of the total area of ​​the elution profile; and (c) a third polyethylene fraction in a temperature range of 70°C to 85°C in the elution profile by means of the iCCD analysis method, wherein the third polyethylene area fraction is an area in the elution profile from 70°C to 85°C, and wherein the area of ​​the third polyethylene fraction comprises less than 10% of the total area of ​​the elution profile;and wherein the polyethylene composition has a density of 0.880 g / cm3 to 0.910 g / cm3, a melt index (I2) of 0.50 g / 10 minutes to 6.0 g / 10 minutes and a zero shear viscosity ratio of the polyethylene composition of less than 2.0; 2. The polyethylene composition according to claim 1, characterized in that it further comprises a fourth polyethylene fraction comprising at least one peak in a temperature range of 20 °C to 35 °C in an elution profile by means of the enhanced comonomer composition distribution analysis (iCCD) method, wherein a fourth polyethylene area fraction is an area in the elution profile from 20 °C to 35 °C, and wherein the area of ​​the fourth polyethylene fraction comprises from 0% to 35% of the total area of ​​the elution profile.

3. The polyethylene composition according to any of the preceding claims, characterized in that the area of ​​the first polyethylene fraction comprises from 30% to 55% of the total area of ​​the elution profile.

4. The polyethylene composition according to any of the preceding claims, characterized in that the area of ​​the second polyethylene fraction comprises from 20% to 103.45% of the total area of ​​the elution profile.

5. The polyethylene composition according to any of the preceding claims, characterized in that the area of ​​the third polyethylene fraction comprises from 4% to 10% of the total area of ​​the elution profile.

6. The polyethylene composition according to claim 1, characterized in that the polyethylene composition 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 6.

0.

7. The polyethylene composition according to claim 1, characterized in that the ratio of the molecular weight of the first polyethylene fraction to the molecular weight of the total elution profile area is from 0.5 to 1.

5.

8. The polyethylene composition according to claim 1, characterized in that the polyethylene composition has a tangent delta, measured at 0.1 radians / s and 190 °C, of ​​10 to 100.

9. A multilayer film characterized in that it comprises at least one layer comprising a polyethylene composition comprising: (a) a first polyethylene fraction comprising at least one peak in a temperature range of 35 °C to 70 °C in an elution profile by means of the enhanced comonomer composition distribution (iCCD) analysis method, wherein a first polyethylene area fraction is an area in the elution profile of 35 °C to 70 °C, and wherein the area of ​​the first polyethylene fraction comprises from 25% to 65% of the total area of ​​the elution profile;(b) a second polyethylene fraction comprising at least one peak in a temperature range of 85 °C to 120 °C in the elution profile by means of the iCCD analysis method, wherein a second polyethylene area fraction is an area in the elution profile from 85 °C to 120 °C, and wherein the area of ​​the second polyethylene fraction comprises at least 20% of the total area of ​​the elution profile; and (c) a third polyethylene fraction in a temperature range of 70 °C to 85 °C in the elution profile by means of the iCCD analysis method, wherein the third polyethylene area fraction is an area in the elution profile from 70 °C to 85 °C, and wherein the area of ​​the third polyethylene fraction comprises less than 10% of the total area of ​​the elution profile;and wherein the polyethylene composition has a density of 0.880 g / cm3 to 0.910 g / cm3, a melt index (I2) of 0.50 g / 10 minutes to 6.0 g / 10 minutes, and a zero shear viscosity ratio of the polyethylene composition of less than 2.0; 10. The multilayer film according to claim 9, characterized in that at least one layer comprising a polyethylene composition is a sealing layer.

11. The multilayer film according to claim 10, characterized in that it further comprises a substrate layer.

12. A method for producing an article characterized in that it comprises the steps of: applying the polyethylene composition according to claim 1 to at least one surface of a substrate layer, thereby forming an article comprising a sealing layer associated with the at least one surface of the substrate layer.