FIELD

This application relates to the art of polyethylene polymers.

INTRODUCTION

Plastics recycling is an important part of plastic waste management. Recycled plastics may not meet the physical property specifications that are needed for common end uses. As a result, recycled plastics are frequently blended with freshly made (“virgin”) plastic in order to provide a blend that can meet specifications needed for commercial use. Such blends desirably contain as much recycled plastic as practical, in order to maximize the amount of recycled plastic used and minimize the amount of virgin plastic needed.

Many common uses for high-density polyethylene (HDPE) require good melt strength, good mechanical properties (tensile strength and flexural strength) and resistance to cracking. Resistance to cracking is commonly measured by ASTM D1693, which measures environmental stress crack resistance (ESCR), and/or ASTM F2136, which measures notched constant ligament stress (NCLS) resistance. ESCR may be critically important for some uses, such as blow-molded bottles, whereas NCLS may be more important for other uses, such as corrugated pipe.

Recycled high-density polyethylene polymers may have ESCR and/or NCLS that is too low for desirable uses. This may be especially true for post-consumer recycled (“PCR”) high- density polyethylene polymers. Some virgin polymers that can be blended to improve crack resistance may also have the effect of reducing other desirable physical properties such as rigidity.

It is desirable to identify blends of virgin high-density polyethylene polymers with high levels of recycled high-density polyethylene polymers (and especially PCR high-density polyethylene polymers) that have a good balance of physical properties and high crack resistance.

SUMMARY

We have discovered that selection of a virgin bimodal high-density polyethylene with proper density and flow index can provide a blend with recycled high-density polyethylene that has both good rigidity and good ESCR and NCLS, as well as other desirable properties. We have also developed a species of virgin bimodal high-density polyethylene that is well-suited to this application.

One aspect of this invention is a high-density polyethylene (HDPE) blend comprising (a) from 25 to 90 weight percent recycled HDPE; and (b) from 10 to 75 weight percent virgin bimodal high-density polyethylene (virgin bimodal HDPE) having a density from 0.944 g/cc to 0.953 g/cc and a flow index (I21) from 8 g/10 min.to 12 g/10 min. The HDPE blend is a post-reactor blend of the recycled HDPE and the virgin bimodal HDPE.

Another aspect of the present invention is a shaped article comprising a high-density polyethylene blend of this invention.

Another aspect of this invention is a blow molding process comprising the steps of: (1) placing a quantity of molten high-density polyethylene blend in a mold cavity, (2) blowing a gas into the molten high-density polyethylene blend, causing it to expand and assume the approximate shape of the mold cavity, and (3) cooling the high-density polyethylene blend, wherein the high- density polyethylene blend is a high-density polyethylene blend of this invention.

Another aspect of this invention is a blow molded article made by the blow molding process.

Another embodiment is a virgin bimodal high-density polyethylene polymer comprising a higher molecular weight ethylene/1 -hexene copolymer component and a lower molecular weight ethylene/1 -hexene copolymer component wherein: the density of the virgin bimodal HDPE polymer is from 0.944 g/cc to 0.953 g/cc; the flow index (I21 ) of the virgin bimodal HDPE polymer is from 8 g/10 min.to 12 g/10 min.; and the melt flow ratio (I21/I2) of the virgin bimodal HDPE polymer is at least 125.

BRIEF DESCRIPTION OF THE DRAWINGS

Figure (Fig.) 1 illustrates the melt strength over a range of draw velocities from 1 to 120 millimeters per second (mm/s) for two virgin HDPE polymers: one virgin bimodal HDPE polymer within the scope of the invention and one virgin unimodal HDPE polymer that is comparative. Fig. 1 is melt strength of Virgin Bimodal HDPE 1 (or “Virgin HDPE 1” or “Virgin 1” for short) and Comparative HDPE (Marlex HXM 501 OOP). Figures 2 to 5 illustrate the melt strength under similar conditions for blends of the two virgin HDPE polymers with recycled HDPE, containing respectively 25 weight percent, 50 weight percent, 75 weight percent and 90 weight percent recycled HDPE. Fig. 2 is melt strength of blends containing 25 % post-consumer recycled (PCR) HDPE and 75% of a virgin HDPE (Virgin Bimodal HDPE 1 or Comparative Marlex HXM 50100P). Fig. 3 is melt strength of blends containing 50 % PCR HDPE and 50% of a virgin HDPE (Virgin Bimodal HDPE 1 or Comparative Marlex HXM 50100P). Fig. 4 is melt strength of blends containing 75 % PCR HDPE and 25% of a virgin HDPE (Virgin Bimodal HDPE 1 or Comparative Marlex HXM 50100P). Fig. 5 is melt strength of blends containing 90 % PCR HDPE and 10% Virgin HDPE (Virgin Bimodal HDPE 1 or Comparative Marlex HXM 501 OOP). Figure 6 illustrates the molecular weight profiles of the virgin bimodal HDPE polymer within the scope of the invention and the unimodal HDPE polymer that is comparative, as measured by Gel Permeation Chromatography.

DETAILED DESCRIPTION

HDPE Polymer — General Characteristics

This invention uses high-density polyethylene (HDPE) polymers of both the virgin and recycled types. In general HDPE is a polymer that predominantly contains repeating units derived from ethylene, optionally with repeating units derived from one or more unsaturated comonomers, and that has a density from 0.93 g/cc to 0.98 g/cc. Both virgin and recycled HDPE are commercially available.

In some embodiments, the HDPE is a homopolymer containing no measurable remnants of comonomer. In some embodiments, the HDPE is a copolymer in which a minor amount of repeating units are derived from unsaturated comonomers.

Examples of suitable comonomers used to make HDPE may include alpha-olefins. Suitable alpha-olefins may include those containing from 3 to 20 carbon atoms (C3-C20). For example, the alpha-olefin may be a C4-C20 alpha-olefin, a C4-C12 alpha-olefin, a C3-C10 alphaolefin, a C3-C8 alpha-olefin, a C4-C8 alpha-olefin, or a Ce-Cs alpha-olefin. In some embodiments, the alpha-olefin is selected from the group consisting of propylene, 1-butene, 1-pentene, 1-hexene, 4-methyl-l -pentene, 1-heptene, 1-octene, 1-nonene and 1-decene. In other embodiments, the alpha-olefin is selected from the group consisting of propylene, 1-butene, 1-hexene, and 1-octene. In further embodiments, the alpha-olefin is selected from the group consisting of 1-hexene and 1- octene.

In some embodiments, an HDPE copolymer contains at least 95 weight percent repeating units derived from ethylene, or at least 96 weight percent or at least 97 weight percent or at least 98 weight percent or at least 99 weight percent or at least 99.5 weight percent, with the remaining repeating units derived from unsaturated comonomers. In some embodiments, an HDPE copolymer contains at least 4 weight percent repeating units derived from comonomers, or at least 3 weight percent or at least 2 weight percent or at least 1 weight percent or at least 99.5 weight percent, with the remaining repeating units derived from ethylene monomer. It is well known how to select comonomers and comonomer content to obtain the known molecular weight and other properties for an HDPE copolymer. In some embodiments, wherein the comonomer is a higher molecular weight comonomer such as 1-octene, the comonomer content may be in the higher part of the range listed above. In some embodiments, wherein the comonomer is a lower molecular weight comonomer such as 1-butene, the comonomer content may be in the lower part of the range listed above. Recycled HDPE

HDPE blends of the present invention contain recycled HDPE. In some embodiments, the recycled HDPE is pre-consumer recycled polyethylene, such as scraps and waste from HDPE manufacturing facilities or from HDPE fabricators. In some embodiments, the recycled HDPE polymer is post-consumer recycled (PCR) HDPE. In some embodiments, the recycled HDPE polymer is a post-industrial recycled HDPE.

The terms “pre-consumer recycled polyethylene” and “post-industrial recycled HDPE” refer to polymers, including blends of polyethylene polymers, recovered from pre-consumer material, as defined by ISO- 14021. The generic term pre-consumer recycled polyethylene thus includes blends of polyethylene and other polymers recovered from materials diverted from the waste stream during a manufacturing process. The generic term pre-consumer recycled polyethylene excludes the reutilization of polyethylene materials, such as rework, regrind, or scrap, generated in a process and capable of being reclaimed within the same process that generated it.

The term “post-consumer recycled” (or “PCR”) polyethylene, as used herein, refers to a polyethylene material, such as the PCR HDPE, that includes materials previously used in a consumer or industry application i.e., pre-consumer recycled polyethylene and post-industrial recycled HDPE. PCR polyethylene is typically collected from recycling programs and recycling plants. The PCR polyethylene may include one or more contaminants. The contaminants may be the result of the polyethylene material’s use prior to being repurposed for reuse. For example, contaminants may include paper, ink, food residue, or other recycled materials in addition to the polymer, which may result from the recycling process. PCR polyethylene is distinct from virgin polyethylene. A virgin polyethylene does not include materials previously used in a consumer or industry application, whereas the PCR polyethylene does include them. Virgin polyethylene material has not undergone, or otherwise has not been subject to, a heat process or a molding process, after the initial polymer manufacturing process. The physical, chemical, and flow properties of PCR polyethylene polymers differ when compared to virgin polyethylene, which in turn can present challenges to incorporating PCR polyethylene into blends for commercial use.

As used in the present disclosure, “PCR polyethylene” means a PCR ethylene/alpha-olefin copolymer, such as a PCR high-density polyethylene; and optionally other components and additives.

It is contemplated that the PCR polyethylene includes various polyethylene compositions. PCR polyethylene may be sourced from HDPE packaging such as bottles (milk jugs, juice containers), LDPE/LLDPE packaging such as films. PCR polyethylene also includes residue from its original use, residue such as paper, adhesive, ink, nylon, ethylene vinyl alcohol (EVOH), polyethylene terephthalate (PET), and other odor-causing agents. Sources of PCR polyethylene can include, for example, bottle caps and closures, milk, water or orange juice containers, detergent bottles, office automation equipment (printers, computers, copiers, etc.), white goods (refrigerators, washing machines, etc.), consumer electronics (televisions, video cassette recorders, stereos, etc.), automotive shredder residue (the mixed materials remaining after most of the metals have been sorted from shredded automobiles and other metal-rich products “shredded” by metal recyclers), packaging waste, household waste, rotomolded parts (kayaks/coolers), building waste and industrial molding and extrusion scrap.

In embodiments, the polyethylene of the PCR polyethylene comprises low density polyethylene, linear low density polyethylene, or a combination thereof. In embodiments, the PCR polyethylene further comprises residue from its original use, such as paper, adhesive, ink, nylon, ethylene vinyl alcohol (EVOH), polyamide (PA), polyethylene terephthalate (PET), and other organic or inorganic material. Examples of PCR polymer include KWR101-150 and KWR-102 from KW Plastics, and AVANGARD™ NATURA PCR-LDPCR-100 (“AVANGARD™ 100”) and AVANGARD™ NATURA PCR-LDPCR-150 (“AVANGARD™ 150”) (PCR polymer commercially available from Avangard Innovative LP, Houston, Texas).

In some embodiments the PCR polyethylene is a PCR HDPE available as KWR101-150 from KW Plastics. When measured using a “heat-cool-heat” temperature profile as described in the Test Methods below, KWR101-150 has the DSC properties shown in the table below, wherein: “1st Cool Delta H cryst” measures the enthalpy of crystallization during the first cooling curve; “1st Cool Tel” measures the crystallization temperature during the first cooling cycle; “2nd Heat Delta H melt measures the enthalpy of fusion during the second heating curve; and “2nd Heat Tml” measures the melting temperature during the second heating curve.

In embodiments, the PCR polyethylene has a heat of fusion in the range of from 130 to 170 Joule/gram (J/g), measured according to the DSC test method described below. All individual values and subranges of from 130 to 170 J/g are disclosed and incorporated herein; for example, the heat of fusion of the PCR polyethylene can be from 130 to 170 J/g, from 130 to 160 J/g, from 130 to 150 J/g, from 130 to 140 J/g, from 140 to 170 J/g, from 140 to 160 J/g, from 140 to 150 J/g, from 150 to 170 J/g, or from 155 to 170 J/g, when measured according to the DSC test method described below. In embodiments, the PCR polyethylene has a peak melting temperature (Im) of from 115°C to 137°C, when measured according to the DSC test method describe below. All individual values and subranges of from 115°C to 137°C are disclosed and incorporated herein; for example, the peak melting temperature (Tm) of the PCR polymer can be from 121 °C to 135 °C, from 131°C to 135°C, from 132°C to 135°C or from 133.0°C to 134.0°C, when measured according to the DSC test method described below.

In some embodiments, the recycled HDPE has a density of at least 0.94 g/cc or at least 0.95 g/cc or at least 0.955 g/cc or at least 0.958 g/cc. In some embodiments, the recycled HDPE has a density of at most 0.97 g/cc or at most 0.965 g/cc.

In some embodiments the melt index (I2) of the recycled HDPE ranges from 0.01 g/10 min to 30 g/10 min. All individual values and subranges of 0.01 g/10 min to 30 g/10 min are included and disclosed herein. In some embodiments, the melt index (I2) of the recycled HDPE is at least 0.1 g/10 min or at least 0.3 g/10 min or at least 0.4 g/10 min or at least 0.5 g/10 min or at least 0.55 g/10 min. In some embodiments, the melt index (I2) of the recycled HDPE is at most 2 g/10 min or at most 1 g/10 min or at most 0.8 g/10 min or at most 0.7 g/10 min or at most 0.65 g/10 min.

In some embodiments, the melt index (I5) of the recycled HDPE is at least 1 g/10 min or at least 2 g/10 min or at least 2.5 g/10 min or at least 2.75 g/10 min. In some embodiments, the melt index (I5) of the recycled HDPE is at most 5 g/10 min or at most 4 g/10 min or at most 3.5 g/10 min or at most 3.25 g/10 min.

In some embodiments, the flow index (I21) of the recycled HDPE is at least 30 g/10 min or at least 40 g/10 min or at least 45 g/10 min or at least 50 g/10 min. In some embodiments, the flow index (I21) of the recycled HDPE is at most 100 g/10 min or at most 90 g/10 min or at most 80 g/10 min or at most 70 g/10 min or at most 60 g/10 min.

In some embodiments, the melt flow ratio (I21/I5) of the recycled HDPE is at least 10 or at least 15 or at least 17 or at least 18. In some embodiments, the melt flow ratio (I21/I5) of the recycled HDPE is at most 30 or at most 25 or at most 23 or at most 21 or at most 20.

In some embodiments, the number average molecular weight (Mn) of the recycled HDPE is at least 10,000 Da or at least 15,000 Da or at least 18,000 Da. In some embodiments, the number average molecular weight (Mn) of the recycled HDPE is at most 50,000 Da or at most 40,000 Da or at most 30,000 Da or at most 25,000 Da.

In some embodiments, the weight average molecular weight (Mw) of the recycled HDPE is at least 80,000 Da or at least 100,000 Da or at least 110,000 Da. In some embodiments, the weight average molecular weight (Mw) of the recycled HDPE is at most 200,000 Da or at most 160,000 Da or at most 130,000 Da or at most 120,000 Da.

In some embodiments, the molecular weight distribution (Mw/Mn) of the recycled HDPE is at least 3 or at least 4 or at least 5. In some embodiments, the molecular weight distribution (Mw/Mn) of the recycled HDPE is at most 10 or at most 8 or at most 7.

In some embodiments, the tensile yield strength of the recycled HDPE is at least 2500 psi or at least 3000 psi or at least 3500 psi. In some embodiments, the tensile yield strength of the recycled HDPE is at most 7000 psi or at most 5000 psi or at most 4000 psi.

In some embodiments, the flexural modulus of the recycled HDPE is at least 100 ksi or at least 130 ksi or at least 145 ksi. In some embodiments, the flexural modulus of the recycled HDPE is at most 200 ksi or at most 180 ksi or at most 170 ksi. (1 ksi = 1000 psi.)

In some embodiments, the ESCR (time to 50% failure rate under the test conditions listed below) of the recycled HDPE is at most 35 hours or at most 30 hours or at most 25 hours or at most 22 hours or at most 20 hours. In some embodiments, the ESCR (time to 50% failure rate under the test conditions listed below) of the recycled HDPE is at least 10 hours or at least 15 hours or at least 18 hours.

Suitable recycled HDPE streams are commercially available, such as from KW Plastics. Others can be prepared by know processes such as: (1) separating HDPE materials having desired properties from a recycle waste stream; (2) washing the separated HDPE materials; and (3) grinding the separated HDPE materials. An example of such a process is described in European Patent 2 697 025 Bl.

Virgin Bimodal HDPE

HDPE blends of the present invention also contain virgin bimodal high-density polyethylene polymer (or “Virgin Bimodal HDPE”). “Virgin” means that the bimodal HDPE has not been fabricated or used to make shaped articles after it was pelletized.

The density of the virgin bimodal HDPE is from 0.944 g/cc to 0.953 g/cc. In some embodiments, the density of the virgin bimodal HDPE is at least 0.946 g/cc or at least 0.947 g/cc or at least 0.948 g/cc. In some embodiments, the density of the virgin bimodal HDPE is at most 0.952 g/cc or at most 0.951 g/cc.

The flow index (I21) of the virgin bimodal HDPE is from 8 g/10 min. to 12 g/10 min. In some embodiments, the flow index (I21) of the virgin bimodal HDPE is at least 8.5 g/10 min or at least 9 g/10 min. In some embodiments, the flow index (I21) of the virgin bimodal HDPE is at most 11 g/10 min or at most 10 g/10 min. In some embodiments, the melt index (I2) of the virgin bimodal HDPE is at least 0.01 g/10 min or at least 0.02 g/10 min or at least 0.03 g/10 min or at least 0.04 g/10 min. In some embodiments, the melt index (I2) of the virgin bimodal HDPE is at most 0.1 g/10 min or at most 0.08 g/10 min or at most 0.06 g/10 min or at most 0.05 g/10 min.

In some embodiments, the melt index (I5) of the virgin bimodal HDPE is at least 0.1 g/10 min or at least 0.2 g/10 min or at least 0.25 g/10 min. In some embodiments, the melt index (I5) of the virgin bimodal HDPE is at most 0.8 g/10 min or at most 0.6 g/10 min or at most 0.5 g/10 min or at most 0.4 g/10 min.

In some embodiments, the melt flow ratio (I21/I2) of the virgin bimodal HDPE is at least 100 or at least 125 or at least 150 or at least 175 or at least 185 or at least 195. In some embodiments, the melt flow ratio (I21/I2) of the virgin bimodal HDPE is at most 400 or at most 300 or at most 250 or at most 225.

In some embodiments, the melt flow ratio (I21/I5) of the virgin bimodal HDPE is at least 20 or at least 25 or at least 27 or at least 28. In some embodiments, the melt flow ratio (I21/I5) of the virgin bimodal HDPE is at most 50 or at most 40 or at most 35 or at most 32.

In some embodiments, the melt strength of the virgin bimodal HDPE at 190°C is at least 10 cN or at least 12 cN or at least 15 cN. In some embodiments, the melt strength of the virgin bimodal HDPE is at most 25 cN or at most 20 cN or at most 18 cN.

In some embodiments, the number average molecular weight (Mn) of the virgin bimodal HDPE is at least 20,000 Da or at least 24,000 Da or at least 26,000 Da or at least 28,000 Da or at least 29,000 Da. In some embodiments, the number average molecular weight (Mn) of the virgin bimodal HDPE is at most 40,000 Da or at most 37,000 Da or at most 35,000 Da or at most 33,000 Da or at most 31,000 Da.

In some embodiments, the weight average molecular weight (Mw) of the virgin bimodal HDPE is at least 350,000 Da or at least 375,000 Da or at least 400,000 Da or at least 420,000 Da. In some embodiments, the weight average molecular weight (Mw) of the virgin bimodal HDPE is at most 600,000 Da or at most 550,000 Da or at most 500,000 Da or at most 475,000 Da or at most 450,000 Da.

In some embodiments, the molecular weight distribution (Mw/Mn) of the virgin bimodal HDPE is at least 10 or at least 12 or at least 13 or at least 14. In some embodiments, the molecular weight distribution (Mw/Mn) of the virgin bimodal HDPE is at most 20 or at most 18 or at most 16 or at most 15.5 or at most 15 or at most 14.8.

The virgin bimodal HDPE has a bimodal molecular weight distribution, meaning that it comprises a higher molecular weight (HMW) component, and a lower molecular weight (LMW) component. The weight average molecular weight (Mw) of the BMW component is higher than the weight average molecular weight (Mw) of the LMW component. In some embodiments, the molecular weight profile of a bimodal HDPE may form two distinct peaks, as explained and illustrated in US Patent 6,787,608B2 at column 4, lines 4-37 and Figure 1C. In some embodiments, the molecular weight profile of a bimodal HDPE may form a single peak with a shoulder, as explained and illustrated in US Patent 6,787,608B2 at column 4, lines 4-37 and Figure IB. In some embodiments, the molecular weight profile of a bimodal HDPE may form a single peak with a tail, as explained and illustrated in US Patent 6,787,608B2 at column 4, lines 4-37 and Figure 1A.

In some embodiments of the invention, the LMW Component makes up more than 50 weight percent of the virgin bimodal HDPE or more than 60 weight percent or more than 70 weight percent or more than 75 weight percent. In some embodiments of the invention, the molecular weight profile (GPC) of a virgin bimodal HDPE shows the HMW component as a shoulder on the LMW component peak.

In some embodiments of the invention, the bimodal nature of the virgin bimodal HDPE is reflected in a high molecular weight distribution (Mw/Mn) or ratio of Mz/Mw, as compared to similar unimodal HDPE.

In some embodiments, the tensile yield strength (also called “stress at yield”) of the virgin bimodal HDPE is at least 3000 psi or at least 3200 psi or at least 3400 psi or at least 3500 psi. In some embodiments, the tensile yield strength of the virgin bimodal HDPE is at most 4500 psi or at most 4000 psi or at most 3750 psi.

In some embodiments, the strain at break of the virgin bimodal HDPE is at least 500 % or at least 600 % or at least 700 % or at least 750 % or at least 775 %. In some embodiments, the strain at break of the virgin bimodal HDPE is at most 900 % or at most 800 %.

In some embodiments, the flexural modulus (2% secant modulus) of the virgin bimodal HDPE is at least 100 ksi or at least 120 ksi or at least 125 ksi. In some embodiments, the flexural modulus of the virgin bimodal HDPE is at most 160 ksi or at most 140 ksi or at most 130 ksi. (1 ksi = 1000 psi.)

In some embodiments, the melt viscosity of the virgin bimodal HDPE at a shear rate of 0.1 rad s ¹ and a temperature of 190°C (“low shear viscosity” or “r]o.i”) is at least 90,000 Pa*s or at least 100,000 Pa*s or at least 120,000 Pa«s or at least 140,000 Pa«s. In some embodiments, the melt viscosity of the virgin bimodal HDPE at a shear rate of 0.1 rad s ¹ and a temperature of 190°C (“low shear viscosity” or “T]O.I”) is at most 200,000 Pa»s or at most 180,000 Pa«s or at most 160,000 Pa«s. In some embodiments, the melt viscosity of the virgin bimodal HDPE at a shear rate of 100 rad s ¹ and a temperature of 190°C (“high shear viscosity” or “r]ioo”) is at least 2000 Pa«s or at least 2100 Pa*s or at least 2200 Pa*s or at least 2250 Pa«s. In some embodiments, the melt viscosity of the virgin bimodal HDPE at a shear rate of 100 rad s' ¹ and a temperature of 190°C (“high shear viscosity” or “r|ioo”) is at most 3000 Pa«s or at most 2750 Pa«s or at most 2500 Pa«s.

Die swell of polymers can be compared using a “timed swell test” as described in PCT Publication WO 2020/223191 at Paragraph [0074], The polymers are extruded through a specific die having a set aperture under a specific set of conditions (temperature, extrusion rate, shear, etc.), and the time required for the extrudate to reach a specified length is recorded. Polymer that swells more out of the die takes longer to reach the specified length and therefor has more die swell. In this application, the specified length is 25.4 cm.

In some embodiments, the timed die swell of the virgin bimodal HDPE under the test conditions listed below at a shear rate of 300 s ¹ is at least 22 seconds or at least 23 seconds or at least 24 seconds. In some embodiments, the timed die swell of the virgin bimodal HDPE under the test conditions listed below at a shear rate of 300 s ¹ is at most 30 seconds or at most 28 seconds or at most 26 seconds.

In some embodiments, the timed die swell of the virgin bimodal HDPE under the test conditions listed below at a shear rate of 1000 s ¹ is at least 8.0 seconds or at least 8.5 seconds or at least 9.0 seconds. In some embodiments, the timed die swell of the virgin bimodal HDPE under the test conditions listed below at a shear rate of 1000 s ¹ is at most 15 seconds or at most 12 seconds or at most 11 seconds.

In some embodiments, the Charpy impact resistance of the virgin bimodal HDPE is at least 8 kJ/m ² or at least 10 kJ/m ² or at least 12 kJ/m ² or at least 14 kJ/m ² or at least 16 kJ/m ² . There is no maximum desired Charpy Impact resistance, but performance over 20 kJ/m ² may be unnecessary.

In some embodiments, the strain hardening modulus of the virgin bimodal HDPE is at least 25 MPa or at least 30 MPa or at least 33 MPa or at least 35MPa or at least 37 MPa. There is no maximum desired strain hardening modulus for the virgin bimodal HDPE, but in some embodiments strain hardening modulus above 45 MPa or 40 MPa may be unnecessary.

In some embodiments, the ESCR (time to 50% failure rate under the test conditions listed below) of the virgin bimodal HDPE is at least 500 hours or at least 600 hours or at least 700 hours or at least 800 hours or at least 900 hours or at least 1000 hours. There is no maximum desirable ESCR performance, but ESCR over 1500 hours may be unnecessary. In some embodiments, the Notched Constant Ligament Stress (NCLS) of the virgin bimodal HDPE is at least 100 hours or at least 200 hours or at least 300 hours or at least 400 hours or at least 500 hours or at least 600 hours or at least 700 hours or at least 800 hours or at least 900 hours or at least 1000 hours. There is no maximum desirable NCLS performance, but NCLS over 1500 hours may be unnecessary.

A particularly useful virgin bimodal high-density polyethylene polymer (virgin bimodal HDPE) comprises a higher molecular weight ethylene/l-hexene copolymer component and a lower molecular weight ethylene/l-hexene copolymer component wherein (a) the density of the virgin bimodal HDPE polymer is from 0.944 g/cc to 0.953 g/cc; (b) the flow index (I21) of the virgin bimodal HDPE polymer is from 8 g/10 min.to 12 g/10 min.; and (c) the melt flow ratio (I21/I5) of the virgin bimodal HDPE polymer is from 25 to 35.

Another embodiment of the present invention is the virgin bimodal high-density polyethylene polymer comprising a higher molecular weight ethylene/l-hexene copolymer component (“HMW component” or “HMW PE”) and a lower molecular weight ethylene/l-hexene copolymer component (“LMW component” or “LMW PE”) wherein: the density of the virgin bimodal HDPE polymer is from 0.944 g/cc to 0.953 g/cc; the flow index (I21) of the virgin bimodal HDPE polymer is from 8 g/10 min.to 12 g/10 min.; and the melt flow ratio (I21/I5) of the virgin bimodal HDPE polymer is from 25 to 35. In some embodiments the melt flow ratio (I21/I2) of the virgin bimodal HDPE polymer is at least 125. In some embodiments the virgin bimodal high- density polyethylene polymer itself, and as used in the blend, has a component split (also known as component weight fraction) wherein the HMW component is from 29.0 wt% to 36.0 wt% and the LMW component is from 71.0 wt% to 64.0 wt%, respectively, alternatively the HMW component is from 30.1 wt% to 34.9 wt% and the LMW component is from 69.9 to 65.1 wt%, respectively, calculated based on the combined weights of the HMW and LMW components. In some embodiments the virgin bimodal high-density polyethylene polymer itself, and as used in the blend, has an ESCR of 750 hours or longer. In some embodiments the virgin bimodal high- density polyethylene polymer itself, and as used in the blend, has any one of limitations (i) to (x): (i) a density of 0.948 to 0.951 g/cc; (ii) a melt index (I5) of 0.29 to 0.42 g/10 minutes; (iii) a flow index (I21) °f 8.8 to 11.9 g/10 minutes; (iv) a melt flow ratio (I21/ 15) of 28 to 32; (v) Abs M _n of 28,000 to 30,999 g/mol; (vi) Abs M _w of 250,000 to 340,000 g/mol; (vii) Abs M _z of 3,400,000 to 3,990,000 g/mol; (viii) Abs M _w /M _n of 8.0 to 12.2; (ix) M _z /M _w 11.0 to 14.0; or (x) any two or more of limitations (i) to (ix). The “Abs” molecular weights are measured by the absolute GPC test method described later. The virgin bimodal high-density polyethylene polymer is made in a single gas phase polymerization reactor by polymerizing ethylene and 1-hexene with a bimodal catalyst system. In some embodiments the bimodal catalyst system comprises, or is made from, a zirconium- containing metallocene catalyst, a zirconium-containing post-metallocene catalyst, a silica support material, and an activator; wherein the zirconium-containing metallocene catalyst is bis(n- butylcyclopentadienyl)zirconium of formula (I): wherein each R1 is -

CH2CH2CH2CH3 and each X is Cl or each X is methyl; wherein the zirconium-containing post- metallocene catalyst is bis(2-(pentamethylphenylamido)ethyl)amine zirconium dibenzyl, which is a compound of formula (II) wherein M is Zr and each R is benzyl (“Bn”).

The polymerization may be run under conditions comprising a reactor bed temperature of about 100° C. ± 2° C., a molar ratio of 1-hexene to ethylene (Cg/C2 mol/mol) of 0.0024 ± 0.0005; a molar ratio of hydrogen to ethylene (H2/C2 mol/mol) of 0.0008 ± 0.0001; and an isopentane concentration of 12.5 ± 0.5 mole percent.

In some embodiments of virgin bimodal HDPE polymer, the molecular weight distribution (Mw/Mn) is at most 16. Other potential embodiments within those limits are as previously described.

This species of virgin bimodal HDPE is useful in formulations of the present invention. It is also useful by itself for blow-molding, such as medium sized parts. It has good impact strength and flexural modulus and has excellent ESCR and NCLS performance.

Virgin bimodal high-density polyethylenes and processes for their manufacture are described in numerous references such as the following patent applications: US 2007/0043177 Al; US 2009/0036610 Al; US 2020/0071509 Al, WO 2009/148487 Al, WO 2019/241045 Al, WO 2020/046663 Al, and WO 2020/068413 Al; and the following patents: US 5.539,076; US 5,882,750; US 6,403,181 Bl; US 7,090,927; US 8,110,644 B2; and US 8,378,029 B2 and Publication B5845, Bimodal Molecular Weight Polyethylene for Blow Molding, issued by Total Petrochemicals USA, Inc. Some production techniques use dual sequential reactors, and some production techniques use a single reactor with a bimodal catalyst system. Suitable bimodal catalyst systems are commercially available from Univation Technologies, LLC.

An example of a suitable bimodal catalyst system is the bimodal catalyst system provided under the PRODIGY™ BMC 300 trademark or can be produced as described in the patents above and in US Application 2020/0024376 Al . The PRODIGY™ BMC 300 catalyst system comprises, or is made from, a zirconium-containing metallocene catalyst, a zirconium-containing postmetallocene catalyst, a support material, and an activator. The zirconium-containing metallocene catalyst is bis(n-butylcyclopentadienyl)zirconium X2 of formula wherein each R1 is -CH2CH2CH2CH3 and each X is a leaving group. In some embodiments of formula (I) each X is Cl or each X is methyl. The zirconium-containing post-metallocene catalyst is bis(2- (pentamethylphenylamido)ethyl)amine zirconium dibenzyl, which is sometimes referred to in the art as “HN5 dibenzyl” and is a compound of formula (II) (II), wherein M is

Zr and each R is benzyl (“Bn”). Both catalysts are well known in the art. For example, the zirconium-containing post-metallocene catalyst may be made by procedures described in the art or obtained from Univation Technologies, LLC, Houston, Texas, USA, a wholly-owned entity of The Dow Chemical Company, Midland, Michigan, USA. Representative Group 15-containing metal compounds, including bis(2-(pentamethylphenylamido)ethyl)amine zirconium dibenzyl, and preparation thereof can be as discussed and describedin U.S. Pat. Nos. 5,318,935; 5,889,128; 6,333,389; 6,271,325; 6,689,847; and 9,981,371; and WO Publications WO 99/01460; WO 98/46651; WO 2009/064404; WO 2009/064452; and WO 2009/064482.

The PRODIGY™ BMC-300 embodiment of the bimodal catalyst system was used to make inventive virgin bimodal HDPE polymer number 1, called “Virgin Bimodal HDPE 1” in the EXAMPLES.

Another suitable embodiment of the bimodal catalyst system is made from the same constituents as used to make the BMC-300 type catalyst system except wherein the bis(n- butylcyclopentadienyl)zirconium X2 of formula (I) is replaced by (cyclopentadienyl)(l,5- dimethylindenyl)zirconium X2, which is a zirconium-containing metallocene of formula (III): , wherein M is Zr and each X is a leaving group. In some embodiments of formula (III) each X is Cl or each X is methyl. This other suitable bimodal catalyst system thus comprises, or is made from, the zirconium-containing metallocene of formula (III), the HN5 dibenzyl, the support, and an activator. For convenience herein, this other embodiment of the bimodal catalyst system is called “BMC Analog”.

The BMC Analog embodiment of the bimodal catalyst system was used to make inventive virgin bimodal HDPE polymer number 2, called “Virgin Bimodal HDPE 2” in the EXAMPLES.

The support material used in these bimodal catalyst systems may be an inorganic oxide material. The terms “support” and “support material” are the same as used herein and refer to a porous inorganic substance or organic substance. In some embodiments, desirable support materials may be inorganic oxides that include Group 2, 3, 4, 5, 13 or 14 oxides, alternatively Group 13 or 14 atoms. Examples of inorganic oxide-type support materials are silica, alumina, titania, zirconia, thoria, and mixtures of any two or more of such inorganic oxides. Examples of such mixtures are silica-chromium, silica-alumina, and silica-titania.

The inorganic oxide support material is porous and has variable surface area, pore volume, and average particle size. In some embodiments, the surface area is from 50 to 1000 square meter per gram (m^/g) and the average particle size is from 20 to 300 micrometers (pm). Alternatively, the pore volume is from 0.5 to 6.0 cubic centimeters per gram (cc/g) and the surface area is from 200 to 600 m^/g. Alternatively, the pore volume is from 1.1 to 1.8 cc/g and the surface area is from 245 to 375 m^/g. Alternatively, the pore volume is from 2.4 to 3.7 cc/g and the surface area is from 410 to 620 m^/g. Alternatively, the pore volume is from 0.9 to 1.4 cc/g and the surface area is from 390 to 590 m^/g. Each of the above properties are measured using conventional techniques known in the art.

The support material may comprise silica, alternatively amorphous silica (not quartz), alternatively a high surface area amorphous silica (e.g., from 500 to 1000 m^/g). Such silicas are commercially available from several sources including the Davison Chemical Division of W.R. Grace and Company (e.g., Davison 952 and Davison 955 products), and PQ Corporation (e.g., ES70 product). The silica may be in the form of spherical particles, which are obtained by a spraydrying process. Alternatively, MS3050 product is a silica from PQ Corporation that is not spray- dried. As procured, these silicas are not calcined (i.e., not dehydrated). Silica that is calcined prior to purchase may also be used as the support material.

Prior to being contacted with a catalyst, such as the HN5 dibenzyl and the zirconium- containing metallocene, the support material may be pre-treated by heating the support material in air to give a calcined support material. The pre-treating comprises heating the support material at a peak temperature from 350° to 850° C., alternatively from 400° to 800° C., alternatively from 400° to 700° C., alternatively from 500° to 650° C. and for a time period from 2 to 24 hours, alternatively from 4 to 16 hours, alternatively from 8 to 12 hours, alternatively from 1 to 4 hours, thereby making a calcined support material. The support material may be a calcined support material.

The method of making the virgin bimodal HDPE using the bimodal catalyst system may further employ a trim catalyst, typically in the form of a trim catalyst solution comprising the aforementioned zirconium-containing metallocene of formula (I) or (DI) and an additional quantity of activator. For convenience the trim catalyst is fed in solution in a hydrocarbon solvent (e.g., mineral oil, heptane, or isopentane). The trim catalyst may be used to vary, within limits, the amount of the zirconium-containing metallocene used in the method relative to the amount of the zirconium-containing post-metallocene (e.g., HN5 dibenzyl) of the bimodal catalyst system, so as to adjust the properties of the inventive HDPE blend.

Each catalyst of the bimodal catalyst system is activated by contacting it with an activator. Any activator may be the same or different as another and independently may be a Lewis acid, a non-coordinating ionic activator, or an ionizing activator, or a Lewis base, an alkylaluminum, or an alkylahiminoxane (alkylalumoxane). The alkylaluminum may be a trialkylaluminum, alkylaluminum halide, or alkylaluminum alkoxide (diethylaluminum ethoxide). The trialkylaluminum may be trimethylaluminum, triethylaluminum (“TEA1”), tripropylaluminum, or tris(2-methylpropyl)aluminum. The alkylaluminum halide may be diethylaluminum chloride. The alkylaluminum alkoxide may be diethylaluminum ethoxide. The alkylaluminoxane may be a methylahiminoxane (MAO), ethylaluminoxane, 2-methylpropyl-aluminoxane, or a modified methylaluminoxane (MMAO). Each alkyl of the alkylaluminum or alkylaluminoxane independently may be a (Cj-C7)alkyl, alternatively a (C j-C^alkyl, alternatively a (C]-C4)alkyl. The molar ratio of activator’ s metal (Al) to a particular catalyst compound’ s metal (catalytic metal, e.g., Zr) may be 1000:1 to 0.5:1, alternatively 300:1 to 1:1, alternatively 150:1 to 1:1. Suitable activators are commercially available.

Once the activator and the catalysts of the bimodal catalyst system contact each other, the catalysts of the bimodal catalyst system are activated and activator species may be made in situ. The activator species may have a different structure or composition than the catalyst and activator from which it is derived and may be a by-product of the activation of the catalyst or may be a derivative of the by-product. The corresponding activator species may be a derivative of the Lewis acid, non-coordinating ionic activator, ionizing activator, Lewis base, alkylaluminum, or alkylaluminoxane, respectively. An example of the derivative of the by-product is a methylaluminoxane species that is formed by devolatilizing during spray-drying of a bimodal catalyst system made with methylaluminoxane.

Each contacting step between activator and catalyst independently may be done either in a separate vessel outside of a gas phase polymerization (GPP) reactor, such as outside of a floatingbed gas phase polymerization (FB-GPP) reactor, or in a feed line to the GPP reactor. The bimodal catalyst system, once its catalysts are activated, may be fed into the GPP reactor as a dry powder, alternatively as a slurry in a non-polar, aprotic (hydrocarbon) solvent. The activator(s) may be fed into the GPP reactor in “wet mode” in the form of a solution thereof in an inert liquid such as mineral oil or toluene, in slurry mode as a suspension, or in dry mode as a powder. Each contacting step may be done at the same or different times.

The gas phase polymerization reactor may be a fhiidized-bed gas phase polymerization (FB-GPP) reactor and the effective polymerization conditions may comprise the following reaction conditions: the FB-GPP reactor having a fluidized bed at a bed temperature from 80 to 110 degrees Celsius (° C.); the FB-GPP reactor receiving feeds of respective independently controlled amounts of ethylene, 1 -alkene characterized by a 1-alkene-to-ethylene (C _x /C2, wherein subscript x indicates the number of carbon atoms in the 1-alkene; for example, when the 1-alkene is 1 -hexene, the C _x /C2 ratio is the 1-hexene-to-ethylene ratio, which may be written as a Cg/C2 ratio) molar ratio, the bimodal catalyst system, optionally a trim catalyst solution, optionally hydrogen gas (H2) characterized by a hydrogen-to-ethylene (H2/C2) rnolar ratio or by a weight parts per million H2 to mole percent C2 ratio (H2 ppm/C2 mol%), and optionally an induced condensing agent (ICA) comprising a (C5-Cjo)alkane(s), e.g., isopentane; wherein the (Cg/C2) molar ratio is from 0.0010 to 0.1; and wherein when the ICA is fed, the concentration of ICA in the reactor is from 1 to 20 mole percent (mol%), based on total moles of ethylene, 1 -alkene, and ICA in the reactor. The average residence time of the copolymer in the reactor may be from 1.0 to 4.0 hours. A continuity additive may be used in the FB-GPP reactor during polymerization. In some embodiments the reaction conditions are those described in the EXAMPLES for making Virgin Bimodal HDPE 1, plus-or-minus (±) 10%.

HDPE blends

The HDPE blend is a post-reactor blend of the recycled HDPE and the virgin bimodal HDPE.

In HDPE blends of the present invention, the recycled HDPE and the virgin bimodal HDPE are melt-blended together in a relative amount of from 25 to 90 weight percent recycled HDPE and from 10 to 75 weight percent virgin bimodal HDPE. The blending can be accomplished by any known means, such as coextruding the two polymers in known extruders or melt blending in known mixers, such as from Hakke, Brabender or Banbury.

In some embodiments, the HDPE blend contains at least 35 weight percent recycled HDPE or at least 40 weight percent or at least 45 weight percent or at least 55 weight percent or at least 65 weight percent or at least 70 weight percent or at least 75 weight percent or at least 80 weight percent or at least 85 weight percent or at least 90 weight percent. In some embodiments, the HDPE blend contains at most 90 weight percent recycled HDPE or at most 85 weight percent or at most 80 weight percent or at most 75 weight percent or at most 65 weight percent or at most 55 weight percent. For example, the HDPE blend may contain 45 to 80 weight percent recycled HDPE, or 45 to 65 weight percent, or 65 to 80 weight percent, or 70 to 90 weight percent.

In some embodiments, the HDPE blend contains at most 65 weight percent virgin bimodal HDPE or at most 55 weight percent or at most 45 weight percent or at most 35 weight percent or at most 30 or at most 25 weight percent or at most 20 weight percent weight percent. In some embodiments, the HDPE blend contains at least 15 weight percent virgin bimodal HDPE or at least 20 weight percent or at least 25 weight percent or at least 35 weight percent or at least 45 weight percent. For example, the HDPE blend may contain 20 to 55 weight percent virgin bimodal HDPE, or 35 to 55 weight percent, or 20 to 35 weight percent , or 10 to 30 weight percent.

In some embodiments, the HDPE blend may contain additives. Additives for polyolefin polymers are described in numerous publications, such as the pamphlet: Tolinski, “Additives for Polyolefins. Getting the Most out of Polypropylene, Polyethylene and TPO (Second Edition)” published by the Plastics Design Library in 2015. Examples of common additives include antistatic agents, color enhancers, dyes, lubricants, fillers, pigments, primary antioxidants, secondary antioxidants, processing aids, UV stabilizers, nucleators, slip agents such as erucamide, antiblock agents such as talc, and combinations thereof. In some embodiments, additives make up no more than 5 weight percent of the HDPE blend or no more than 4 weight percent or no more than 3 weight percent or no more than 2 weight percent or no more than 1 weight percent. In some embodiments, additives make up essentially 0 weight percent of the HDPE blend.

In some embodiments, the density of the HDPE blend is at least 0.95 g/cc or at least 0.952 g/cc or at least 0.954 g/cc. In some embodiments, the density of the HDPE blend is at most 0.965 g/cc or at most 0.960 g/cc or at most 0.958 g/cc.

In some embodiments, the melt index (h) of the HDPE blend is at least 0.06 g/10 min or at least 0.08 g/10 min or at least 0.1 g/10 min. In some embodiments, the melt index (I2) of the HDPE blend is at most 2 g/10 min or at most 1 g/10 min or at most 0.5 g/10 min or at most 0.4 g/10 min or at most 0.3 g/10 min or at most 0.25 g/10 min.

In some embodiments, the flow index (I21) of the HDPE blend is at least 10 g/10 min or at least 12 g/10 min or at least 15 g/10 min or at least 17 g/10 min or at least 19 g/10 min. In some embodiments, the flow index (I21) of the HDPE blend is at most 50 g/10 min or at most 45 g/10 min or at most 40 g/10 min or at most 35 g/10 min or at most 32 g/10 min.

In some embodiments, the melt flow ratio (I21/I2) of the HDPE blend is at least 100 or at least 110 or at least 120 or at least 140. In some embodiments, the melt flow ratio (I21/I2) of the HDPE blend is at most 250 or at most 200 or at most 190 or at most 185.

In some embodiments, the tensile yield strength (stress at yield) of the HDPE blend is at least 3200 psi or at least 3400 psi or at least 3600 psi or at least 3700 psi. In some embodiments, the tensile yield strength of the HDPE blend is at most 5000 psi or at most 4500 psi or at most 4200 psi.

In some embodiments, the strain at break of the HDPE blend is at least 500% or at least 600% or at least 700% or at least 800%. In some embodiments, the strain at break of the HDPE blend is at most 1000% or at most 900% or at most 850%. In some embodiments, the flexural modulus (2% secant modulus) of the HDPE blend is at least 125 ksi or at least 130 ksi or at least 135 ksi or at least 140 ksi. In some embodiments, the flexural modulus of the HDPE blend is at most 175 ksi or at most 160 ksi or at most 155 ksi. (1 ksi = 1000 psi.)

In some embodiments, the Charpy impact resistance of the HDPE blend is at least 3.5 J/m ² or at least 4 J/m ² or at least 5 J/m ² or at least 6 J/m ² . In some embodiments, the Charpy impact resistance of the HDPE blend is at most 12 J/m ² or at least 4 J/m ² or at most 10 J/m ² or at most 9 J/m ² .

In some embodiments, the strain hardening modulus of the HDPE blend is at least 8 MPa or at least 10 MPa or at least 12 MPa or at least 13 MPa. There is no maximum desired strain hardening modulus of the HDPE blend, but in some embodiments a strain hardening modulus above 35 MPa or 125 MPa may be unnecessary.

In some embodiments, the ESCR (time to 50% failure rate under the test conditions listed below) of an HDPE blend that contains at least 20 weight percent recycled HDPE is at least 500 hours or at least 600 hours or at least 700 hours or at least 800 hours or at least 900 hours or at least 950 hours. In some embodiments, the ESCR (time to 50% failure rate under the test conditions listed below) of an HDPE blend that contains at least 45 weight percent recycled HDPE is at least 200 hours or at least 250 hours or at least 275 hours or at least 300 hours or at least 325 hours or at least 350 hours. In some embodiments, the ESCR (time to 50% failure rate under the test conditions listed below) of an HDPE blend that contains at least 70 weight percent recycled HDPE is at least 200 hours or at least 250 hours or at least 275 hours or at least 300 hours or at least 325 hours. In some embodiments, the ESCR (time to 50% failure rate under the test conditions listed below) of an HDPE blend that contains at least 85 weight percent recycled HDPE is at least 200 hours or at least 250 hours or at least 275 hours or at least 300 hours or at least 325 hours. There is no maximum desired ESCR, but performance over 1500 hours or 2000 hours may be unnecessary. For HDPE blends that contain high levels of recycled HDPE, lower ESCR may be acceptable such as 750 hours or 500 hours or 400 hours.

In some embodiments, the NCLS (time to 50% failure rate under the test conditions listed below) of an HDPE blend that contains at least 20 weight percent recycled HDPE is at least 100 hours or at least 200 hours or at least 300 hours or at least 400 hours or at least 500 hours or at least 600 hours or at least 700 hours or at least 750 hours. In some embodiments, the NCLS (time to 50% failure rate under the test conditions listed below) of an HDPE blend that contains at least 45 weight percent recycled HDPE is at least 15 hours or at least 25 hours or at least 35 hours or at least 45 hours or at least 55 hours or at least 65 hours or at least 75 hours. In some embodiments, the NCLS (time to 50% failure rate under the test conditions listed below) of the HDPE blend that contains at least 70 weight percent recycled HDPE is at least 11 hours or at least 13 hours or at least 15 hours or at least 16 hours. In some embodiments, the Notched Constant Ligament Stress (time to 50% failure rate under the test conditions listed below) of an HDPE blend that contains at least 85 weight percent recycled HDPE is at least 7 hours or at least 8 hours or at least 9 hours or at least 10 hours. There is no maximum desired NCLS, but for HDPE blends that contain at least 45 weight percent recycled HDPE, performance over 150 hours may be unnecessary, and for HDPE blends that contain at least 70 weight percent recycled HDPE, performance over 50 hours or 25 hours may be unnecessary.

In some embodiments, the melt strength of the HDPE blend that contains at least 45 weight percent of the recycled HDPE is at least 8 cN or at least 10 cN or at least 11 cN. In some embodiments, the melt strength of the HDPE blend that contains at least 45 weight percent of the recycled HDPE is at most 16 cN or at most 15 cN.

In some embodiments, the melt strength of the HDPE blend that contains at least 70 weight percent of the recycled HDPE is at least 8 cN or at least 9 cN or at least 10 cN. In some embodiments, the melt strength of the HDPE blend that contains at least 70 weight percent of the recycled HDPE is at most 15 cN or at most 12 cN.

In some embodiments, the melt strength of the HDPE blend that contains at least 85 weight percent of the recycled HDPE is at least 6 cN or at least 7 cN or at least 8 cN. In some embodiments, the melt strength of the HDPE blend that contains at least 70 weight percent of the recycled HDPE is at most 12 cN or at most 10 cN.

Blow Molding and Fabricated Articles

HDPE blends of the present invention can be used in common blow molding processes, such as extrusion blow-molding, injection blow molding or injection stretch blow molding. All three processes use the following steps: (1) placing a quantity of molten HDPE blend in a mold cavity, (2) blowing air or a neutral gas such as nitrogen into the molten HDPE blend, causing it to expand and assume the approximate shape of the mold cavity, and (3) cooling the HDPE blend.

In an extrusion blow molding process, the HDPE blend is melted and extruded as a hollow tube, called a parison. The parison is enclosed in a cooled metal mold for a shaped article such as a bottle, container, or part. Air or a neutral gas such as nitrogen is then blown into the parison, inflating it into the shape of the mold. After the HDPE blend has cooled sufficiently, the mold is opened, and the part is ejected.

In an injection blow molding process, the HDPE blend is melted and injected into a metal mold for a shaped article such as a bottle, container, or part. Air or a neutral gas such as nitrogen is then blown into the mold, inflating the HDPE blend into the shape of the mold. After the HDPE blend has cooled sufficiently, the mold is opened, and the part is ejected.

In an injection stretch blow molding process, a preform of the HDPE blend is made by injection molding. In some embodiments, the final neck features for the final molded item (such as threading on a bottle neck) are made on the preform. Next, the molten preform is placed in a mold. Air or a neutral gas such as nitrogen is then blown into the preform, inflating it into the shape of the mold. After the HDPE blend has cooled sufficiently, the mold is opened, and the part is ejected. The preform may be blown immediately after it is formed, or it may be cooled and then reheated and blown later.

In some embodiments, the temperature of the molten HDPE blend is at least 150°C or at least 155°C or at least 160°C. In some embodiments, the temperature of the molten HDPE blend is at most 210°C or at most 190°C or at most 180°C.

The product of the blow-molding is a shaped article. In some embodiments, the shaped article is a liquid container, such as ajar or bottle. In some embodiments, the liquid container has a capacity of at most 10 L or at most 5 L or at most 2 L or at lost 1 L or at most 0.75 L or at most 0.5 L or at most 0.4 L or at most 0.3L. In some embodiments, the liquid container has a capacity of at least 0.1 L or at least 0.3 L or at least 0.5 L or at least 0.75 L or at least 1 L. In some embodiments, the liquid container is smaller, having a capacity from 1 to 100 mL. In some embodiments, the HDPE blends with a flow index of at least 30 g/10 min. may be more useful in small parts, such as small bottles, whereas the HDPE blends with a flow index of below 30 g/10 min. may be more useful in large parts, such as large bottles.

In some embodiments, the shaped article is a pipe such as a corrugated pipe.

The blow molding processes are well-known and described in numerous publications such as: “Blow Molding Design Guide”, published by Gemini Group at https://geminigroup.net/wp- content/uploads/2018/06/Blow-Molding-Design-Guide-by-Regency -Plastics.pdf, “Blow- Molding ”, published by Industrial Quick Search at https://www.iqsdirectory.com/articles/blow- molding.html, “A Guide to Polyolefin Blow Molding”, Publication 6683/0715 published by LyondellBasell Industries, and N. C. Lee, Understanding Blow Molding (Hanser Publications, 2007).

In some embodiments the high-density polyethylene blend comprises: (a) from 25 to 90 weight percent recycled high-density polyethylene; and (b) from 10 to 75 weight percent virgin bimodal HDPE polymer having a density from 0.944 g/cc to 0.953 g/cc and a flow index (I21) from 8 g/10 min.to 12 g/10 min. In some embodiments the recycled high-density polyethylene is post-consumer recycled polymer.

In some embodiments the melt flow ratio (I21/I2) of the virgin bimodal high-density polyethylene polymer is at least 125.

In some embodiments the flow index (I21) of the high-density polyethylene blend is from 10 g/10 min to 50 g/10 min.

In some embodiments the molecular weight distribution (Mw/Mn) of the virgin bimodal high-density polyethylene polymer is at most 16.

In some embodiments the melt flow ratio (I21/I2) of the high-density polyethylene blend is at least 140.

In some embodiments the high-density polyethylene blend contains at least 45 weight percent PCR high-density polyethylene, and has an NCLS of at least 50 hours as measured according to ASTM F2136.

In some embodiments the high-density polyethylene blend contains at least 70 weight percent PCR high-density polyethylene, and which has an NCLS of at least 15 hours as measured according to ASTM F2136 or has a melt strength of at least 9 cN or both.

In some embodiments the high-density polyethylene blend contains at least 85 weight percent PCR high-density polyethylene, and which has an NCLS of at least 8 hours as measured according to ASTM F2136 or a melt strength of at least 8 cN or both.

In some embodiments the high-density polyethylene blend has an ESCR that is at least 200 hours as measured according to ASTM D 1693-13, Condition A, with at 10% surfactant in water.

In some embodiments the high-density polyethylene blend has a Notched Constant Ligament Stress (NCLS) that is at least 15 hours.

In some embodiments the virgin bimodal high-density polyethylene polymer constituent of the high-density polyethylene blend comprises a higher molecular weight ethylene/1 -hexene copolymer component and a lower molecular weight ethylene/1 -hexene copolymer component wherein: the density of the virgin bimodal HDPE polymer is from 0.944 g/cc to 0.953 g/cc; the flow index (I21) of the bimodal HDPE polymer is from 8 g/10 min.to 12 g/10 min.; and the melt flow ratio (I21/I2) of the bimodal HDPE polymer is at least 125.

In some embodiments is a shaped article comprising the high-density polyethylene blend.

In some embodiments is a blow molding process comprising the steps of: (1) placing a quantity of molten high-density polyethylene (HDPE) blend in a mold cavity, (2) blowing a gas into the molten HDPE blend, causing it to expand and assume the approximate shape of the mold cavity, and (3) cooling the HDPE blend, wherein the HDPE blend is the high-density polyethylene blend.

In some embodiments is a blow molded article prepared by the blow molding process.

EXAMPLES

Test Methods:

The following test methods are used to measure properties described in this application: The following test methods are used to measure properties described in this application: Density: Density is measured according to ASTM D792-13, Standard Test Methods for Density and Specific Gravity (Relative Density) of Plastics by Displacement, Method B (for testing solid plastics in liquids other than water, e.g., in liquid 2-propanol). Report results in units of grams per cubic centimeter (g/cc).

Differential Scanning Calorimetry (DSC): Differential scanning calorimetry (DSC) is a common technique that can be used to examine the melting and crystallization of semi-crystalline polymers. General principles of DSC measurements and applications of DSC to studying semicrystalline polymers are described in standard texts e.g., E. A. Turi, ed., Thermal Characterization of Polymeric Materials, Academic Press, 1981).

In preparation for Differential Scanning Calorimetry (DSC) testing, pellet-form samples are first loaded into a 1 in. diameter chase of 0.13 mm thickness and compression molded into a film under 25,000 lbs. of pressure at 190°C for approximately 10 seconds. The resulting film is then cooled to room temperature, after which the film is subjected to a punch press in order to extract a disk that will fit the aluminum pan supplied by TA Instruments. The disk is then weighed individually (note: sample weight is approximately 4-8mg) and placed into the aluminum pan and sealed before being inserted into the DSC test chamber.

In accordance with ASTM standard D3418, the DSC test is conducted using a heat-cool- heat cycle. First, the sample is equilibrated at 180°C and held isothermally for 5 min to remove thermal and process history. The sample is then quenched to -40°C at a rate of 10°C/min and held isothermally once again for 5 min during the cool cycle. Lastly, the sample is heated at a rate of 10°C/min to 150°C for the second heating cycle. For data analysis, the melting temperatures and enthalpy of fusion is extracted from the second heating curve, whereas the enthalpy of crystallization is taken from the cooling curve. The enthalpy of fusion and crystallization were obtained by integrating the DSC thermogram from -20°C to the end of melting and crystallization, respectively. The tests are performed using the TA Instruments Q2000 and Discovery DSCs, and data analyses were conducted via TA Instruments Universal Analysis and TRIOS software packages. Melt Index, Flow Index and Melt Flow Ratio: Flow index (I21) is measured according to ASTM D1238-13, Condition 190°C/21.6 kg, and is reported in g/lOmin. Melt index I5 and I2 are measured following the same procedure using 5.0kg and 2.16 kg load conditions, respectively. Melt Flow Ratio (I21/I5) is calculated based on the results.

Melt Strength: Melt Strength testing is conducted on either Rheotester 2000 or Rheograph 25 capillary rheometers paired with a Rheotens model 71 .97, all of which are manufacture by Gottfert. The die used for testing has a diameter of 2 mm, length of 30 mm, and an entry angle of 180 degrees. Each test is performed isothermally at 190° C. Prior to initiating the test, the sample pellets are loaded into the capillary barrel and allowed to equilibrate at the testing temperature for 10 min. During the test, a piston inside the barrel applies a steady force on the molten sample to achieve an apparent wall shear rate of 38.16 s’ ¹ , and the melt is extruded through the die with an exit velocity of approximately 9.7 mm/second. Located 100 mm below the die exit, the extrudate in the form of a strand is guided through wheel pairs of the Rheotens, which accelerate at a constant rate of 2.4 mm/s ² and measures the extrudate’s response to the applied extensional force. Note that the Rheotens wheel pairs are typically serrated and are spaced 0.4 mm apart. The results of this test are documented into plots of force with respect to Rheotens wheel speed using the RtensEvaluations 2007 excel macros. In these plots, the force levels off, i.e., plateaus, before the extrudate strand breaks. For analysis, the melt strength is reported as the plateau force in centinewtons (cN) before the extrudate strand broke. The corresponding speed of the of the Rheotens wheel at the point of strand breakage is documented as the drawability limit.

Environmental Stress Crack Resistance (ESCR): ESCR measurements are conducted according to ASTM D1693-15, Standard Test Method for Environmental Stress-Cracking of Ethylene Plastics, Method B. ESCR (10% IGEPAL CO-630, F50) is the number of hours to failure of 50 percent of specimens of a bent, notched, compression-molded test specimen that is immersed in a solution of 10 weight percent IGEPAL CO-630 in water at a temperature of 50° C. IGEPAL CO-630 is an ethoxylated branched-nonylphenol of structural formula 4-(branched-C9H19)- phenyl-[OCH2CH2] _n -OH, wherein subscript n is a number such that the branched ethoxylated nonylphenol has a number-average molecular weight of about 619 grams/mole.

Notched Constant Ligament Stress (NCLS): NCLS is measured using ASTM F2136.

Charpy Impact Resistance: Charpy impact strength is tested at -40° C. according to ISO 179, Plastics - Determination of Charpy Impact Properties. Specimens that have the dimensions 80 mm x 10 mm x 4 mm are cut and machined from a 4 mm compression molded plaque that has been cooled at 5°C/minute. The specimens are notched on their long sides in the thickness direction to a depth of 2 mm using a notching device with a 22.5 degree half-angle and a 0.25 radius curvature at its tip. Specimens are cooled in a cold box for 1 hour then removed and tested in less than 5 seconds. The impact tester meets the specification described in ISO 179. Results are reported in units of kilojoules per square meter (kJ/m2).

2% Secant Flexural Modulus: Is measured according to ASTM D790-10, Procedure B, Standard Test Methods for Flexural Properties of Unreinforced and Reinforced Plastics and Electrical Insulating Materials. Results are reported in megapascals (MPa). 1,000.0 pounds per square inch (psi)=6.8948 MPa.

Tensile Strength: Tensile Strength is measured using ASTM D638-14. The average of five specimens tested at a speed of 2 in/min is reported.

Strain Hardening Modulus: The ISO 18488 standard is followed to determine strain hardening modulus (“SHM”). Polymer pellets are compression molded into sheets of 0.3 mm thickness following molding conditions described in Table 1 of the ISO 18488 standard. After molding, the sheets are conditioned at 120 °C for one hour followed by controlled cooling at a rate of 2 °C/min to room temperature. Five tensile bars (dog bone shaped) are punched out of the compression molded sheets. The tensile test is conducted in a temperature chamber at 80 °C. Each specimen is conditioned for at least 30 minutes in the temperature chamber prior to starting the test. The test specimen is clamped top and bottom and a pre-load of 0.4 MPa with a speed of 5 mm/min is applied. During the test, the load and the elongation sustained by the specimen are measured. The test specimen is extended at a constant speed of 20 mm/min and data point are collected from a draw ratio ( ) of 8.0 until X=12.0 or breakage. As specified in ISO 18488, the plot of true stress vs. draw ratio is used to calculate the slope between a draw ratio of 8.0 and 12.0. If failure occurred before a draw ratio of 12.0, then the draw ratio corresponding to the failure strain is considered as upper limit for the slope calculation. If failure occurred before a draw ratio of 8.0, then the test is considered invalid.

Die Swell: Polymer swell is characterized in terms of “timed swell” by a capillary rheometer. In this approach, the time required for an extruded polymer strand to travel a distance of 10 in. (25.4 cm) is determined. The more the polymer swells, the slower the free end of the strand travels, and the longer it takes to cover the distance. A 12 mm barrel Gbttfert Rheotester 2000 equipped with a 30/1 (mm/nun) L/D capillary die is used for the measurement. The measurement is carried out at 190°C at two fixed shear rates: 300 s ¹ and 1000 s' ¹ . The time measure of swell is reported as the t300 and tlOOO values, respectively.

High Shear and Low Shear Viscosity: Dynamic oscillatory shear measurements are conducted over a range of 0.1 rad s- 1 to 100 rad s- 1 at a temperature of 190°C and 10% strain with stainless steel parallel plates of 25 mm diameter on the strain controlled rheometer ARES/ARES- G2 by TA Instruments. The rheometer is preheated for at least 30 minutes at 190°C. Place the disk prepared by the Compression Molded Plaque Preparation Method between two “25 mm” parallel plates in the oven. Slowly reduce the gap between the “25 mm” parallel plates to 2.0 mm. Allow the sample to remain for exactly 5 minutes at these conditions. Open the oven, and carefully trim excess sample from around the edge of the plates. Close the oven. Allow an additional 5- minute delay to allow for temperature equilibrium. Then determine the complex shear viscosity via a small amplitude, oscillatory shear, according to an increasing frequency sweep from 0.1 to 100 rad/s to obtain the complex viscosities at 0.1 rad/s and 100 rad/s. Define the shear viscosity ratio (SVR) as the ratio of the complex shear viscosity in pascal-seconds (Pa.s) at 0.1 rad/s to the complex shear viscosity in pascal-seconds (Pa.s) at 100 rad/s.

Molecular Weights (Determined by Gel Permeation Chromatography (GPC)):

The chromatographic system consisted of a PolymerChar GPC-IR (Valencia, Spain) high temperature GPC chromatograph equipped with an internal IR5 infra-red detector (IR5) and 4- capillary viscometer (DV) coupled to a Precision Detectors (Now Agilent Technologies) 2-angle laser light scattering (LS) detector Model 2040. For all absolute Light scattering measurements, the 15 degree angle is used for measurement. The autosampler oven compartment was set at 160° Celsius and the column and detector compartment were set at 150° Celsius. The columns used were 4 Agilent “Mixed A” 30cm 20-micron linear mixed-bed columns. The chromatographic solvent used was 1,2,4 trichlorobenzene and contained 200 ppm of butylated hydroxytoluene (BHT). The solvent source was nitrogen sparged. The injection volume used was 200 microliters and the flow rate was 1.0 milliliters/minute.

Calibration of the GPC column set was performed with 21 narrow molecular weight distribution polystyrene standards with molecular weights ranging from 580 to 8,400,000 and were arranged in 6 “cocktail” mixtures with at least a decade of separation between individual molecular weights. The standards were purchased from Agilent Technologies. The polystyrene standards were prepared at 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 pre-dissolved at 80 °C with gentle agitation for 30 minutes then cooled and the room temperature solution is transferred cooled into the autosampler dissolution oven at 160°C for 30 minutes. The polystyrene standard peak molecular weights were converted to polyethylene molecular weights using Equation 1 (as described in Williams and Ward, J. Polym. Sci., Polym. Let., 6, 621 (1968)).: where M is the molecular weight, A has a value of 0.4389 and B is equal to 1.0.

A fifth order polynomial was used to fit the respective polyethylene-equivalent calibration points.

The total plate count of the GPC column set was performed with decane which was introduced into blank sample via a micropump controlled with the PolymerChar GPC-IR system. The plate count for the chromatographic system should be greater than 18,000 for the 4 Agilent “Mixed A” 30cm 20-micron linear mixed-bed columns.

Samples were prepared in a semi-automatic manner with the PolymerChar “Instrument Control” Software, wherein the samples were weight-targeted at 2 mg/ml, and the solvent (contained 200ppm BHT) was added to a pre nitrogen-sparged septa-capped vial, via the PolymerChar high temperature autosampler. The samples were dissolved for 2 hours at 160° Celsius under “low speed” shaking.

The calculations of Mn<GPC), MW(GPQ, and MZ(GPQ were based on GPC results using the internal IR5 detector (measurement channel) of the PolymerChar GPC-IR chromatograph according to Equations 2-4, using PolymerChar GPCOne™ software, the baseline-subtracted IR chromatogram at each equally spaced data collection point (i), and the polyethylene equivalent molecular weight obtained from the narrow standard calibration curve for the point (i) from Equation 1.

In order to monitor the deviations over time, a flowrate marker (decane) was introduced into each sample via a micropump controlled with the PolymerChar GPC-IR system. This flowrate marker (FM) was used to linearly correct the pump flowrate (Flowrate(nominal)) for each sample by RV alignment of the respective decane peak within the sample (RV(FM Sample)) to that of the decane peak within the narrow standards calibration (RV(FM Calibrated)). Any changes in the time of the decane marker peak are then assumed to be related to a linear shift in flowrate (Flowrate(effective)) for the entire run. After calibrating the system based on a flow marker peak, the effective flowrate (with respect to the narrow standards calibration) is calculated as Equation 5. Processing of the flow marker peak was done via the PolymerChar GPCOne™ Software. Acceptable flowrate correction is such that the effective flowrate should be within +/-

O.5% of the nominal flowrate.

Flowrate(effective) = Flowrate(nominal) * (RV(FM Calibrated) / RV(FM Sample)) (EQ5) Triple Detector GPC (TDGPC)

For the determination of the viscometer and light scattering detector offsets from the IR5 detector, the Systematic Approach for the determination of multi-detector offsets is done in a manner consistent with that published by Balke, Mourey, et. al. (Mourey and Balke, Chromatography Polym. Chpt 12, (1992)) (Balke, Thitiratsakul, Lew, Cheung, Mourey, Chromatography Polym. Chpt 13, (1992)), optimizing triple detector log (MW and IV) results from a linear homopolymer polyethylene standard (3.5 > Mw/Mn > 2.2) with a molecular weight in the range of 115,000 to 125,000 g/mol to the narrow standard column calibration results from the narrow standards calibration curve using PolymerChar GPCOne™ Software.

The absolute molecular weight data was obtained in a manner consistent with that published by Zimm (Zimm, B.H., J. Chem. Phys., 16, 1099 (1948)) and Kratochvil (Kratochvil,

P., Classical Light Scattering from Polymer Solutions, Elsevier, Oxford, NY (1987)) using PolymerChar GPCOne™ software. The overall injected concentration, used in the determination of the molecular weight, was obtained from the mass detector area and the mass detector constant, derived from a suitable linear polyethylene homopolymer, or one of the polyethylene standards of known weight-average molecular weight. The calculated molecular weights (using GPCOne™) were obtained using a light scattering constant, derived from one or more of the polyethylene standards mentioned below, and a refractive index concentration coefficient, dn/dc, of -0.104. Generally, the mass detector response (IR5) and the light scattering constant (determined using GPCOne™) should be determined from a linear standard with a molecular weight in excess of about 50,000 g/mole. The viscometer calibration (determined using GPCOne™) can be accomplished using the methods described by the manufacturer, or, alternatively, by using the published values of suitable linear standards, such as Standard Reference Materials (SRM) 1475a (available from National Institute of Standards and Technology (NIST)). A viscometer constant (obtained using GPCOne™) is calculated which relates specific viscosity area (DV) and injected mass for the calibration standard to its intrinsic viscosity. The chromatographic concentrations are assumed low enough to eliminate addressing 2nd viral coefficient effects (concentration effects on molecular weight).

The absolute weight average molecular weight (MW(Abs)) is obtained (using GPCOne™) from the Area of the Light Scattering (LS) integrated chromatogram (factored by the light scattering constant) divided by the mass recovered from the mass constant and the mass detector (IR5) area. The molecular weight and intrinsic viscosity responses are linearly extrapolated at chromatographic ends where signal to noise becomes low (using GPCOne™). Other respective moments, Mn<Abs) and Mz(Abs) are be calculated according to equations 8-10 as follows :

The following working examples illustrate some specific embodiments of the invention but do not limit the broad scope of the invention.

Production of Virgin Bimodal HDPE 1

Virgin Bimodal HDPE 1 is an inventive embodiment of the virgin bimodal HDPE polymer made using ethylene (“C2”) monomer and 1 -hexene (“Cg”) comonomer and PRODIGY™ BMC- 300 bimodal catalyst system from Univation Technologies, LLC. Virgin Bimodal HDPE 1 comprises a higher molecular weight component that is an ethylene/1 -hexene copolymer and a lower molecular weight constituent that is an ethylene/1 -hexene copolymer. Virgin Bimodal HDPE 1 is made in a gas-phase, fluidized-bed reactor with an isopentane (“iC5”) feed, under conditions shown in Table 1.

Production of Virgin Bimodal HDPE 2

Virgin Bimodal HDPE 2 is an inventive embodiment of the virgin bimodal HDPE polymer made using ethylene (“C2”) monomer and 1-hexene (“Cg”) comonomer and the BMC Analog bimodal catalyst system. Virgin Bimodal HDPE 2 comprises a higher molecular weight component that is an ethylene/1 -hexene copolymer and a lower molecular weight constituent that is an ethylene/1 -hexene copolymer. Virgin Bimodal HDPE 2 is made in a gas-phase, fluidized- bed reactor with an isopentane (“iCg”) feed, under conditions shown in Table 1. Table 1:

For comparative purposes, a virgin unimodal HDPE polymer that is commonly blended with recycled polyethylene Marlex HXM 501 OOP polyethylene from Chevron Phillips) is obtained. The properties of all both polymers are reported in Table 2.

Table 2: In Table 2, the “GPC” molecular weight data were measured by the conventional GPC, the “Abs” molecular weight data were measured by the absolute GPC test method, N/a means not applicable, and N/m means not measured.

In Table 2, the embodiments of the inventive virgin bimodal high-density polyethylene polymer Virgin Bimodal HDPE 1 and Virgin Bimodal HDPE 2, and the comparative Marlex HDPE, each contain 0.06 wt.% of Irganox 1010 antioxidant and 0.10 wt.% of Irgafos 168 antioxidant.

Post-consumer recycled (PCR) HDPE homopolymer is obtained: KWR 101-150 natural homopolymer high-density polyethylene polymer from KW Plastic. The PCR polymer is melt- blended with Virgin Bimodal HDPE 1 in quantities of 25 weight percent PCR polymer, 50 weight percent PCR polymer, 75 weight percent PCR polymer and 90 weight percent PCR polymer to form HDPE blends. Separately the PCR polymer is melt-blended with Virgin Bimodal HDPE 2 in quantities of 25 weight percent PCR polymer, 50 weight percent PCR polymer, 75 weight percent PCR polymer and 90 weight percent PCR polymer to form HDPE blends.

The melt-blending is carried out on a Coperion ZSK 25 mm twin-screw extruder (11 barrel, 44 L/D, electric heating and water cooling). The motor is rated at 40 horsepower. The gearbox ratio is 1:89, and the maximum screw speed is 1,200 RPM. Maximum torque for this line is 106 Nm. Barrel length is 1125 mm per with 11 barrels comprising the entire process section. Screw diameter is 25.5 mm. Extruder barrel I.D. is 25 mm. Nitrogen padding (9.5 SCFH) is maintained at the feed throat during the entire compounding process. The screw design is the ZSK-25 mild screw. The screw RPM is 300.

Polymers are fed to the extruder using a single auger screw K-tron T-20 polymer feeder. The feed rate is 30 lbs./hr.

The compounded materials are extruded through a 3mm, 2 hole die into a 6 foot long chilled water bath. The strands are passed thru a Huestis Air Block to remove excess water. The cooled and dried strands are pelletized with the Conair strand pelletizer.

The properties of each HDPE blend are measured. In addition, the properties of each virgin polymer are measured.

The measured properties are listed in Table 2. Examples listed as “IE” are inventive examples, and examples listed as “CE” are comparative examples. The inventive HDPE blends have higher NCLS performance and substantially equivalent physical properties as compared with comparative HDPE blends that contain the same level of virgin polymer.

The melt strengths at 190°C for the samples are shown in Figures 1 through 5. In Table 3a, the reported melt strength for each sample is the average melt strength observed in the range of velocities for which the sample shows a rough melt strength plateau. It can be observed that for HDPE blends that contain at least 70 weight percent PCR HDPE, the melt strength of the inventive HDPE blends is substantially equivalent to the comparative HDPE blends.

In Table 3b, the inventive blends are prophetic examples. Therefore no properties can be reported for these prophetic inventive blends, which is indicated by “N/a”, which means not applicable.

In Tables 3a and 3b cN is centinewtons, ksi is kilopounds per square inch, psi is pounds per square inch, kJ/m^ is kilojoules per square meter, MPa is megapascals, and hr is hours.

Table 3a. Properties of inventive examples with Virgin Bimodal HDPE 1 and comparative examples. Table 3a Continued. Properties of inventive examples with Virgin Bimodal HDPE 1 and comparative examples.

Table 3b: Properties of prophetic inventive examples with Virgin Bimodal HDPE 2. See Table

3a for comparative examples.

*prophetic example. Table 3b Continued: Properties of prophetic inventive examples with Virgin Bimodal HDPE 2.

See Table 3a for comparative examples.

*prophetic example.