Patent Description:
Polyethylene of raised temperature resistance ("PE-RT") is a class of polyethylene resins suitable for use in domestic hot and cold water piping systems such as underfloor heating and radiator connections. PE-RT resins have a molecular structure and crystalline microstructure which can provide long term hydrostatic strength at high temperature, without the need for cross-linking. PE-RT resins can be used in applications where temperatures otherwise limit the use of polyethylene ("PE") or where metallic materials will suffer from corrosion. Furthermore, the processing properties of a PE-RT resin makes it attractive for industrial applications.

For example, the PE-RT resin can be used in plastics to offer cost savings and provide other advantages such as high speed and flexible pipe production processes, and ease of installation for an application. Unlike other polyethylene ("PE"), random copolymer polypropylene ("PP-R"), polybutene ("PB") and to a lesser extent chlorinated PVC ("C-PVC"), each of which can be restricted by high temperature limitations, the versatility of PE-RT resins used at higher temperature make these polyethylene compositions useful over a wide range of applications, particularly, when temperature profiles can range from sub-ambient to beyond what is considered normal for a PE system.

<CIT> discloses a polyethylene resin and a composition containing such resin which is particularly suitable for use in pipes.

Typical characteristics of a PE-RT resin include processability such as extrudability and maximizing pipe mechanical (short-term and long-term) properties. PE-RT pipes typically have small diameters, e.g., up to <NUM>, and are fabricated at relatively fast rates of production. A fast extrusion rate; however, can introduce finishing issues such as melt fracture and result in poor surface finish. Further, increased extrusion rates can impact properties such as the smooth surface finish required by the International Standard Organization ("ISO") <NUM>-<NUM>.

Therefore, a need exists for a PE-RT pipes that provide advantages in processing of the pipe over conventional linear low density polyethylene resins, particularly, in terms of melt index and shear thinning characteristics which will lower extrusion pressures and extruder/die temperature to allow faster extrusion rates.

Provided herein are PE-RT pipes comprising a polyethylene composition of linear low density polyethylene (LLDPE) as described in attached claims <NUM>-<NUM>.

The invention also provides for a process to produce the PE-RT pipe as described herein.

The invention further provides for an assembly comprising the PE-RT pipe as described herein. The assembly may comprises two or more PE-RT pipes in fluid communication.

As used herein, the term "metallocene catalyst" refers to a catalyst having at least one transition metal compound containing one or more substituted or unsubstituted cyclopentadienyl moiety ("Cp") (typically two Cp moieties) in combination with a Group <NUM>, <NUM>, or <NUM> transition metal (M). As used herein, all reference to the Periodic Table of the Elements and groups thereof is to the NEW NOTATION published in <NPL>), unless reference is made to the Previous IUPAC form denoted with Roman numerals (also appearing in the same), or unless otherwise noted. A metallocene catalyst is considered a single site catalyst. Metallocene catalysts generally require activation with a suitable co-catalyst, or activator, in order to yield an "active metallocene catalyst", i.e., an organometallic complex with a vacant coordination site that can coordinate, insert, and polymerize olefins. Active catalyst systems generally include not only the metallocene complex, but also an activator, such as an alumoxane or a derivative thereof (preferably methyl alumoxane), an ionizing activator, a Lewis acid, or a combination thereof. Alkylalumoxanes (typically methyl alumoxane and modified methylalumoxanes) are particularly suitable as catalyst activators. The catalyst system can be supported on a carrier, typically an inorganic oxide or chloride or a resinous material such as, for example, polyethylene or silica.

The term linear medium density polyethylene ("MDPE") refers to a polyethylene copolymer having a density from about <NUM>/cm<NUM> to about <NUM>/cm<NUM>. Polymers having more than two types of monomers, such as terpolymers, are also included within the term "copolymer.

The composition distribution breadth index ("CDBI") refers to the weight percent of the copolymer molecules having a comonomer content within <NUM>% of the median total molar comonomer content. The CDBI of any copolymer is determined utilizing known techniques for isolating individual fractions of a sample of the copolymer. Temperature Rising Elution Fraction (TREF) is described in <NPL>) as well as in <CIT>.

As used herein, the shear thinning ratio refers to the complex viscosity at <NUM> at <NUM> rad/ s over the complex viscosity at <NUM> at <NUM> rad/s (or the nearest point).

Molecular weight distribution ("MWD") is equivalent to the expression Mw/Mn. The expression Mw/Mn is the ratio of the weight average molecular weight ("Mw") to the number average molecular weight ("Mn"). The weight average molecular weight is given by <MAT> the number average molecular weight is given by <MAT> the z-average molecular weight is given by <MAT> where n; in the foregoing equations is the number fraction of molecules of molecular weight Mi. Measurements of Mw, Mz, and Mn are typically determined by Gel Permeation Chromatography as disclosed in <NPL>). The measurements proceed as follows. Gel Permeation Chromatography (Agilent PL-<NUM>), equipped with three in-line detectors, a differential refractive index detector (DRI), a light scattering (LS) detector, and a viscometer, is used. Experimental details, including detector calibration, are described in: <NPL>). Three Agilent PLgel <NUM> Mixed-B LS columns are used. The nominal flow rate is <NUM>/min, and the nominal injection volume is <NUM>µL. The various transfer lines, columns, viscometer and differential refractometer (the DRI detector) are contained in an oven maintained at <NUM>. Solvent for the experiment is prepared by dissolving <NUM> grams of butylated hydroxy toluene as an antioxidant in <NUM> liters of Aldrich reagent grade <NUM>,<NUM>,<NUM>-trichlorobenzene (TCB). The TCB mixture is then filtered through a <NUM> Teflon filter. The TCB is then degassed with an online degasser before entering the GPC-3D. Polymer solutions are prepared by placing dry polymer in a glass container, adding the desired amount of TCB, then heating the mixture at <NUM> with continuous shaking for about <NUM> hours. All quantities are measured gravimetrically. The TCB densities used to express the polymer concentration in mass/volume units are <NUM>/ml at about <NUM> and <NUM>/ml at <NUM>. The injection concentration is from <NUM> to <NUM>/ml, with lower concentrations being used for higher molecular weight samples. Prior to running each sample, the DRI detector and the viscometer are purged. The flow rate in the apparatus is then increased to <NUM>/minute, and the DRI is allowed to stabilize for <NUM> hours before injecting the first sample. The LS laser is turned on at least <NUM> to <NUM> hours before running the samples. The concentration, c, at each point in the chromatogram is calculated from the baseline-subtracted DRI signal, IDRI, using the following equation: <MAT> where KDRI is a constant determined by calibrating the DRI, and (dn/dc) is the refractive index increment for the system. The refractive index, n = <NUM> for TCB at <NUM> and λ = <NUM>. Units on parameters throughout this description of the GPC-3D method are such that concentration is expressed in g/cm<NUM>, molecular weight is expressed in g/mole, and intrinsic viscosity is expressed in dL/g.

The LS detector is a Wyatt Technology High Temperature DAWN HELEOS. The molecular weight, M, at each point in the chromatogram is determined by analyzing the LS output using the Zimm model for static light scattering (<NPL>): <MAT> Here, ΔR(θ) is the measured excess Rayleigh scattering intensity at scattering angle θ, c is the polymer concentration determined from the DRI analysis, A<NUM> is the second virial coefficient. P(θ) is the form factor for a monodisperse random coil, and Ko is the optical constant for the system: <MAT> where NA is Avogadro's number, and (dn/dc) is the refractive index increment for the system, which take the same value as the one obtained from DRI method. The refractive index, n = <NUM> for TCB at <NUM> and λ = <NUM>.

A high temperature Viscotek Corporation viscometer, which has four capillaries arranged in a Wheatstone bridge configuration with two pressure transducers, is used to determine specific viscosity. One transducer measures the total pressure drop across the detector, and the other, positioned between the two sides of the bridge, measures a differential pressure. The specific viscosity, ηs, for the solution flowing through the viscometer is calculated from their outputs. The intrinsic viscosity, [η], at each point in the chromatogram is calculated from the following equation: <MAT> where c is concentration and was determined from the DRI output.

The branching index (g'vis) is calculated using the output of the GPC-DRI-LS-VIS method as follows. The average intrinsic viscosity, [η]avg of the sample is calculated by: <MAT> where the summations are over the chromatographic slices, i, between the integration limits.

The branching index g'vis is defined as: <MAT> MV is the viscosity-average molecular weight based on molecular weights determined by LS analysis. Z average branching index (g'Zave) is calculated using Ci = polymer concentration in the slice i in the polymer peak times the mass of the slice squared, Mi<NUM>. All molecular weights are weight average unless otherwise noted. All molecular weights are reported in g/mol unless otherwise noted. This method is the preferred method of measurement and used in the examples and throughout the disclosures unless otherwise specified. See also, for background, <NPL>).

In an extrusion process, viscosity is a measure of resistance to shearing flow. Shearing is the motion of a fluid, layer-by-layer, like a deck of cards. When polymers flow through straight tubes or channels, they are sheared and the resistance is expressed by the viscosity. The melt index ("MI") is the number of grams extruded in <NUM> minutes under the action of a standard load is an inverse measure of viscosity. A high melt index implies low viscosity and low melt index means high viscosity. In addition, polymers are shear thinning, which means that their resistance to flow decreases as the shear rate increases. This is due to molecular alignments in the direction of flow and disentanglements.

Extensional or elongational viscosity is the resistance to stretching. In fiber spinning, in film blowing and other process where molten polymers are stretched, the elongational viscosity plays a role. For example, for certain liquids, the resistance to stretching can be three times larger than in shearing. For some polymeric liquids, the elongational viscosity can increase (tension stiffening) with the rate, although the shear viscosity decreased.

Melt strength is a measure of the extensional viscosity and is defined as the maximum tension that can be applied to the melt without breaking. Extensional viscosity is the polymer's ability to resist thinning at high draw rates and high draw ratios. In melt processing of polyolefins, the melt strength is defined by two key characteristics that can be quantified in process related terms and in rheological terms. In extrusion blow molding and melt phase thermoforming, a branched polyolefin of the appropriate molecule weight can support the weight of the fully melted sheet or extruded parison prior to the forming stage. This behavior is sometimes referred to sag resistance.

When LLDPE are extended in the melt phase, because of the lack of long chain branching, the chains align and tend to slide over one another. There is a momentary point where they begin to exhibit an increase in viscosity that is immediately flowed by the onset of shear thinning. The melt will thin out from specific points where the critical draw rate or draw ratio has been exceed. So, while a lower elongational viscosity permits the LLDPE to be easily down gaged since there is no strong tension stiffening, the low elongational viscosity and melt strength is often bad for formation of larger diameter PE-RT pipes.

Therefore, as provided herein, the present PE-RT resins/polyethylene compositions can improve melt strength and shear thinning which can lower extrusion pressure and melt temperature to allow for faster extrusion rates. Through use of the polyethylene compositions described herein, the PE-RT pipes can be produced at relatively fast extrusion rates without many of the finishing issues typically associated with the conventional processing of PE-RT pipe.

As described herein, the polyethylene composition comprises from about <NUM> mole% to <NUM> mole% of units derived from ethylene. The lower limit on the range of ethylene content can be from <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, or <NUM> mole% based on the mole% of polymer units derived from ethylene. The polyethylene composition can have an upper limit on the range of ethylene content of <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, <NUM> mole%, or <NUM> mole%, based on polymer units derived from ethylene.

Comonomer content is based on the total content of all monomers in the polymer. The polyethylene copolymer has minimal long chain branching (i.e., less than <NUM> long-chain branch/<NUM> carbon atoms, preferably particularly <NUM> to <NUM> long-chain branch/<NUM> carbon atoms). Such values are characteristic of a linear structure that is consistent with a branching index (as defined below) of g'vis ≥ <NUM>, <NUM>, ≥ <NUM>, ≥ <NUM>, or <NUM>. While such values are indicative of little to no long chain branching, some long chain branches can be present (i.e., less than <NUM> long-chain branch/<NUM> carbon atoms, preferably less than <NUM> long-chain branch/<NUM> carbon atoms, particularly <NUM> to <NUM> long-chain branch/<NUM> carbon atoms).

In another class of embodiments, the polyethylene compositions provided herein are ethylene-based copolymers having about <NUM> to about <NUM> wt%, <NUM> to <NUM> wt%, <NUM> to <NUM> wt%, <NUM> to <NUM> wt%, <NUM> to <NUM> wt%, <NUM> to <NUM> wt%, or <NUM> to <NUM> wt%, of polymer units derived from ethylene and about <NUM> to about <NUM> wt%, <NUM> to <NUM> wt%, <NUM> to <NUM> wt%, <NUM> to <NUM> wt%, <NUM> to <NUM> wt%, <NUM> to <NUM> wt%, or <NUM> to <NUM> wt% of polymer units derived from one or more C<NUM> to C<NUM> α-olefin comonomers, preferably C<NUM> to C<NUM> α-olefins, and more preferably C<NUM> to C<NUM> α-olefins. The α-olefin comonomer can be linear, branched, cyclic and/or substituted, and two or more comonomers can be used, if desired. Examples of suitable comonomers include of propylene, butene, <NUM>-pentene; <NUM>-pentene with one or more methyl, ethyl, or propyl substituents; <NUM>-hexene; <NUM>-hexene with one or more methyl, ethyl, or propyl substituents; <NUM>-heptene; <NUM>-heptene with one or more methyl, ethyl, or propyl substituents; <NUM>-octene; <NUM>-octene with one or more methyl, ethyl, or propyl substituents; <NUM>-nonene; <NUM>-nonene with one or more methyl, ethyl, or propyl substituents; ethyl, methyl, or dimethyl-substituted <NUM>-decene; <NUM>-dodecene. Particularly suitable comonomers include <NUM>-butene, <NUM>-hexene, and <NUM>-octene, <NUM>-hexene, and mixtures thereof.

In some compositions, the polyethylene composition comprises from about <NUM> wt% to about <NUM> wt%, of C<NUM>-C<NUM> α-olefin derived units, and from about <NUM> wt% to about <NUM> wt% ethylene derived units, based upon the total weight of the copolymer.

In other compositions, the polyethylene composition comprises from about <NUM> wt% to about <NUM> wt%, of C<NUM>-C<NUM> α-olefin derived units, and from about <NUM> wt% to about <NUM> wt% ethylene derived units, based upon the total weight of the polymer for example.

The polyethylene compositions have a melt index (MI), I<NUM> or simply I<NUM> for shorthand according to ASTM D1238, condition E (<NUM>/<NUM>) reported in grams per <NUM> minutes (g/<NUM>), of ≥ about <NUM>/<NUM>, e.g., ≥ about <NUM>/<NUM>, ≥ about <NUM>/<NUM>, ≥ about <NUM>/<NUM>, ≥ about <NUM>/<NUM>, ≥ about <NUM>/<NUM>, ≥ about <NUM>, or ≥ about <NUM>/<NUM>. Additionally, the second polyethylene polymers can have a melt index (I<NUM>) ≤ about <NUM>/<NUM>, ≤ about <NUM>/<NUM>, ≤ about <NUM>/<NUM>, ≤ about <NUM>/<NUM>, ≤ about <NUM>/<NUM>, ≤ about <NUM>/<NUM>, ≤ about <NUM>/<NUM>, ≤ about <NUM>/<NUM>, ≤ about <NUM>/<NUM>, ≤ about <NUM>/<NUM>, ≤ about <NUM>/<NUM>, ≤ about <NUM>/<NUM>, or ≤ about <NUM>/<NUM>. Ranges expressly disclosed include, but are not limited to, ranges formed by combinations any of the above-enumerated values, e.g., from about <NUM> to about <NUM>, about <NUM> to about <NUM>, about <NUM> to about <NUM>/<NUM>, etc..

The polyethylene compositions also have High Load Melt Index (HLMI), I<NUM> or I<NUM> for shorthand, measured in accordance with ASTM D-<NUM>, condition F (<NUM>/<NUM>). For a given polymer having an MI and MIR as defined herein, the HLMI is fixed and can be calculated in accordance with the following paragraph.

The polyethylene compositions can have a Melt Index Ratio (MIR) which is a dimensionless number and is the ratio of the high load melt index to the melt index, or I<NUM>/I<NUM> as described above. The MIR of the second polyethylene polymers can be from <NUM> to <NUM>, alternatively, from <NUM> to <NUM>, alternatively, from about <NUM> to about <NUM>, and alternatively, from about <NUM> to about <NUM>.

The polyethylene compositions can have a density > <NUM>/cm<NUM>, ≥ <NUM>/cm<NUM>, ≥ <NUM>/cm<NUM>, ≥ <NUM>/cm<NUM>, ≥ <NUM>/cm<NUM>. Alternatively, polyethylene compositions can have a density ≤ <NUM>/cm<NUM> ≤ <NUM>/cm<NUM>, e.g., ≤ <NUM>/cm<NUM>, ≤ <NUM>/cm<NUM>, ≤ <NUM>/cm<NUM>. Ranges expressly disclosed include, but are not limited to, ranges formed by combinations any of the above-enumerated values, e.g., from <NUM> to <NUM>/cm<NUM>, <NUM> to <NUM>/cm<NUM>. Density is determined using chips cut from plaques compression molded in accordance with ASTM D-<NUM> Procedure C, aged in accordance with ASTM D-<NUM> Procedure A, and measured as specified by ASTM D-<NUM>.

The polyethylene compositions have a molecular weight distribution (MWD, defined as Mw/Mn) of <NUM> to <NUM>, preferably <NUM> to <NUM>.

The branching index, g'vis is inversely proportional to the amount of branching. Thus, lower values for g' indicate relatively higher amounts of branching. The amounts of short and long-chain branching each contribute to the branching index according to the formula: g'=g'LCB×g'SCB.

The polyethylene compositions have a g'vis of <NUM> to <NUM>, particularly, <NUM> to <NUM>, <NUM> to <NUM>, <NUM> to <NUM>, <NUM> to <NUM>, or <NUM> to <NUM>.

The polyethylene composition can be made by any suitable polymerization method including solution polymerization, slurry polymerization, supercritical, and/or gas phase polymerization using supported or unsupported catalyst systems, such as a system incorporating one or more metallocene catalysts.

Metallocene catalysts generally require activation with a suitable co-catalyst, or activator, in order to yield an "active metallocene catalyst", i.e., an organometallic complex with a vacant coordination site that can coordinate, insert, and polymerize olefins. Active catalyst systems generally include not only the metallocene complex, but also an activator, such as an alumoxane or a derivative thereof (preferably methyl alumoxane), an ionizing activator, a Lewis acid, or a combination thereof. Alkylalumoxanes (typically methyl alumoxane and modified methylalumoxanes) are particularly suitable as catalyst activators. The catalyst system can be supported on a carrier, typically an inorganic oxide or chloride or a resinous material such as, for example, polyethylene or silica.

Examples of useful metallocene catalysts/systems for producing polyethylene compositions desired herein include bridged and unbridged biscyclopentadienyl zirconium compounds (particular where the Cp rings are indenyl or fluorenyl groups). Non-limiting examples of metallocene catalysts and catalyst systems include those disclosed in <CIT> and <CIT>, and in <CIT>; <CIT>; <CIT>; <CIT>; <CIT>; <CIT>, and <CIT>. Additional examples include the catalysts and catalyst systems described in <CIT> and <CIT>, and <CIT>.

Zirconium transition metal metallocene-type catalyst systems are particularly suitable. Non-limiting examples of metallocene catalysts and catalyst systems useful to make the present polyethylene compositions described herein include those described in, <CIT>; <CIT>; <CIT>; and <CIT>, and in the references cited therein. Particularly useful catalyst systems include supported dimethylsilyl bis(tetrahydroindenyl) zirconium dichloride.

Supported polymerization catalyst can be deposited on, bonded to, contacted with, or incorporated within, disposed on, adsorbed or absorbed in, or on, a support or carrier. In another embodiment, the metallocene is introduced onto a support by slurrying a presupported activator in oil, a hydrocarbon such as pentane, solvent, or non-solvent, then adding the metallocene as a solid while stirring. The metallocene can be finely divided solids. Although the metallocene is typically of very low solubility in the diluting medium, it is found to distribute onto the support and be active for polymerization. Very low solubilizing media such as mineral oil (e.g., Kaydo™ or Drakol™) or pentane can be used. The diluent can be filtered off and the remaining solid shows polymerization capability much as would be expected if the catalyst had been prepared by traditional methods such as contacting the catalyst with methylalumoxane in toluene, contacting with the support, followed by removal of the solvent. If the diluent is volatile, such as pentane, it can be removed under vacuum or by nitrogen purge to afford an active catalyst. The mixing time can be greater than <NUM> hours, but shorter times are suitable.

In a gas phase polymerization process, a continuous cycle is employed where in one part of the cycle of a reactor, a cycling gas stream, otherwise known as a recycle stream or fluidizing medium, is heated in the reactor by the heat of polymerization. This heat is removed in another part of the cycle by a cooling system external to the reactor. (See e.g., <CIT>; <CIT>; <CIT>; <CIT>; <CIT>; <CIT>; <CIT>; <CIT>; <CIT>; <CIT>; and <CIT>. ) To obtain the copolymers, individual flow rates of ethylene, comonomer, and hydrogen should be controlled and adjusted to obtain the desired polymer properties.

Suitable commercial polyethylene compositions are available from ExxonMobil Chemical Company, Houston, TX, as ENABLE® metallocene polyethylene resins ("ENABLE® mPE" or "ENABLE®") polyethylene compositions (resins) as described below. ENABLE® mPE polyethylene compositions offer an excellent balance between processability and mechanical properties, including tensile strength and elongation to break that leads to highpressure PE-RT pipe with advanced drawdown and enhanced pipe rupture (failure) time and toughness. For example, ENABLE <NUM> HH is a medium density metallocene ethylene-hexene copolymer including a processing aid additive, a thermal stabilizer additive, and having a density of about <NUM>/cm<NUM> and melt index <NUM>/ kg of about <NUM>/<NUM>. Applications for ENABLE products include but are not limited to food packaging, form fill, and seal packaging, heavy duty bags, lamination film, stand up pouches, multilayer packaging film, and shrink film.

Likewise, ENABLE MC is yet another medium density metallocene ethylene-hexene copolymer including a processing aid additive, a thermal stabilizer, and having density of about <NUM>/cm<NUM> and melt index <NUM>/<NUM> of about <NUM>/<NUM>. It is useful in food packaging, form fill and seal packaging, heavy duty bags, lamination film, stand-up pouches, multilayer packaging film, and shrink film.

The polyethylene compositions and end-use application of PE-RT pipe as described herein comprise a linear low density polyethylene ("LLDPE") copolymer having at least <NUM> percent ethylene and at least one α-olefin co-monomer. The co-monomer can have from <NUM> to about <NUM> carbon atoms. The polyethylene composition can have a composition distribution breadth index ("CDBI") of at least <NUM>% and a melt index ("MI") as measured at <NUM> and <NUM> from about <NUM> to about <NUM>/<NUM>. The polyethylene composition has a molecular weight distribution ("MWD)" from about <NUM> to about <NUM>.

As described herein, the polyethylene composition includes LLDPE which is a copolymer of ethylene and at least one other alpha-olefin ("α-olefin"). Co-monomers useful for making LLDPE copolymers include alpha-olefins, such as C<NUM>-C<NUM> alpha-olefins, preferably C<NUM>-C<NUM> alpha-olefins, and more preferably C<NUM>-C<NUM> alpha-olefins. The alpha-olefin co-monomer can be linear or branched, and two or more comonomers can be used, if desired. The comonomers include propylene, butene, <NUM>-pentene; <NUM>-pentene with one or more methyl, ethyl, or propyl substituents; <NUM>-hexene; <NUM>-hexene with one or more methyl, ethyl, or propyl substituents; <NUM>-heptene; <NUM>-heptene with one or more methyl, ethyl, or propyl substituents; <NUM>-octene; <NUM>-octene with one or more methyl, ethyl, or propyl substituents; <NUM>-nonene; <NUM>-nonene with one or more methyl, ethyl, or propyl substituents; ethyl, methyl, or dimethyl-substituted <NUM>-decene; <NUM>-dodecene.

Specifically, but without limitation, the combinations of ethylene with co-monomer can include: ethylene propylene, ethylene butene, ethylene <NUM>-pentene; ethylene <NUM>-methyl-<NUM>-pentene; ethylene <NUM>-hexene; ethylene <NUM>-octene; ethylene decene; ethylene dodecene; ethylene <NUM>-hexene <NUM>-pentene; ethylene <NUM>-hexene <NUM>-methyl-<NUM>-pentene; ethylene <NUM>-hexene <NUM>-octene; ethylene <NUM>-hexene decene; ethylene <NUM>-hexene dodecene; ethylene <NUM>-octene <NUM>-pentene; ethylene <NUM>-octene <NUM>-methyl-<NUM>-pentene; ethylene <NUM>-octene <NUM>-hexene; ethylene <NUM>-octene decene; ethylene <NUM>-octene dodecene; combinations thereof and like permutations.

Generally, LLDPE copolymers can be obtained via a continuous gas phase polymerization using supported catalyst comprising an activated molecularly discrete catalyst in the substantial absence of an aluminum alkyl based scavenger (e.g., triethylaluminum (TEAL), trimethylaluminum (TMAL), triisobutyl aluminum (TIBAL), tri-n-hexylaluminum (TNHAL), and the like).

Representative LLDPEs produced using these catalysts generally each have a melt index of from <NUM> to <NUM>/<NUM>, a CDBI of at least <NUM>%, a density from <NUM> to <NUM>/ml, a haze value of less than <NUM>%, a melt index ratio (MIR), I<NUM>/I<NUM>, from <NUM> to <NUM>. While prior art processes and polymers can be similar, none describe LLDPE copolymers having good shear thinning and therefore relatively favorable extrusion and other melt processing properties with a high stiffness and high impact strength for use as a PE-RT pipe. For example, in comparison to LDPE (low density polyethylene) made in a high pressure polymerization process and having a comparable density and MI, the LLDPE copolymer used in the present PE-RT pipe have a favorable processability/mechanical properties balance for PE-RT pipe applications. Likewise, in comparison with LLDPE copolymer made by a gas phase process using conventional Ziegler-Natta supported catalysts, the present polyethylene copolymers have improved shear thinning characteristics.

LLDPE copolymers can have a composition distribution breadth index of at least <NUM>%, a melt index I<NUM> from about <NUM> to about <NUM>/<NUM>, a melt index ratio, I<NUM>/I<NUM>, of from about <NUM> to about <NUM>, a molecular weight distribution by GPC from about <NUM> to about <NUM>, and a density from about <NUM> to about <NUM>. The LLDPE copolymers can be combined with at least one additional polymer that is a high density polyethylene, a linear low density polyethylene, a low density polyethylene, a medium density polyethylene, a differentiated polyethylene, or combinations thereof. The LLDPE copolymers can also be combined with at least one additional polymer that is a very low density polyethylene, an ethylene- or propylene-based polymer, a polymer derived from one or more dienes, and/or combinations thereof.

As to the reactor process conditions used to produce polyethylene, the overall conditions are described in <CIT> can be used. A combination of process conditions can be beneficial in making the LLDPE copolymers described herein. For example, it is advantageous to use a catalyst system in which the metallocene has a pair of bridged cyclopentadienyl groups, preferably with the bridge consisting of a single carbon, germanium or silicon atom to provide an open site on the catalytically active cation. The activator can be methyl alumoxane as described in <CIT>; <CIT>; and <CIT>, or a non-coordinated anion as described in <CIT>. Additionally, there should be substantially no scavengers which can interfere with the reaction between the vinyl end unsaturation of polymers formed and the open active site on the cation. By the statement "substantially no scavengers" and "substantially devoid or free of Lewis acid scavengers", it is meant that there should be less than <NUM> ppm by weight of such scavengers present in the feed gas, or preferably, no intentionally added scavenger, such as, for example, an aluminum alkyl scavenger, other than that which can be present on the support.

Conditions for the production of the LLDPE copolymers can include steady state polymerization conditions which are not likely to be provided by batch reactions in which the amount of catalyst poisons can vary and where the concentration of the comonomer can vary in the production of the batch.

The overall continuous gas phase processes for the polymerization of the LLDPE compositions herein can therefore comprise: (<NUM>) continuously circulating a feed gas stream containing monomer and inerts to thereby fluidize and agitate a bed of polymer particles; (<NUM>) adding metallocene catalyst to the bed; and (<NUM>) removing polymer particles, in which: a) the catalyst comprises at least one bridged bis cyclopentadienyl transition metal and an alumoxane activator on a common or separate porous support; b) the feed gas is substantially devoid of a Lewis acidic scavenger and wherein any Lewis acidic scavenger is preferably present in an amount less than <NUM> ppm by weight of the feed gas; c) the temperature in the bed is no more than <NUM> less than the polymer melting temperature as determined by DSC, at a ethylene partial pressure in excess of <NUM> pounds per square inch absolute (<NUM> kPaa); and d) the removed polymer particles have an ash content of transition metal of less than <NUM> ppm by weight, an MI less than <NUM>, an MIR at least <NUM>, and substantially no detectable chain end unsaturation as determined by HNMR.

By the statement that the polymer has substantially no detectable end chain unsaturation, it is meant that the polymer has vinyl unsaturation of less than <NUM> vinyl groups per <NUM> carbon atoms in the polymer, preferably less than <NUM> vinyl groups per <NUM> carbon atoms, and more preferably <NUM> vinyl groups per <NUM> carbon atoms or less.

The processes described above can provide LLDPE copolymer via the use of a single catalyst, and the processes do not depend on the interaction of bridged and unbridged species. Preferably, the catalyst is substantially devoid of a metallocene having a pair of pi-bonded ligands (e.g., cyclopentadienyl compounds) which are not connected through a covalent bridge. In other words, no such metallocene is intentionally added to the catalyst or, preferably, no such metallocene can be identified in such catalyst. Additionally, the processes use substantially a single metallocene species comprising a pair of pi-bonded ligands, at least one of which has a structure with at least two cyclic fused rings (e.g., indenyl rings). Best results can be obtained by using a substantially single metallocene species comprising a monoatom silicon bridge connecting two polynuclear pi-bonded ligands to the transition metal atom.

The catalyst is preferably supported on silica with the catalyst homogeneously distributed in the silica pores. Preferably, fairly small amounts of methyl alumoxane should be used, such as amounts giving an Al to transition metal ratio of from <NUM> to <NUM>, and especially of from <NUM> to <NUM>.

In order to obtain a desired melt index ratio (i.e., <NUM> to <NUM>), both the molar ratio of ethylene and comonomer and the concentration of the comonomer can be varied. Control of the temperature can help control the MI. Overall monomer partial pressures can be used which correspond to conventional practice for gas phase polymerization of LLDPE.

The above-described processes can be tailored to achieve desired polyethylene compositions. For example, comonomer to ethylene concentration or flow rate ratios are commonly used to control density. Similarly, hydrogen to ethylene concentrations or flow rate ratios are commonly used to control molecular weight. In both cases, higher levels of a modifier results in lower values of the respective resin parameter. Gas concentrations can be measured by, for example, an on-line gas chromatograph or similar apparatus to ensure relatively constant composition of recycle gas streams. Optimization of these modifier ratios and the given reactor conditions can achieve a targeted melt index, density, and/or other resin properties.

As provided herein, the present polyethylene compositions are useful as pipe made of polyethylene of raised temperature ("PE-RT") or for PE-RT pipe. Fabricated pipe using these PE-RT qualified resins (referred to herein as "polyethylene compositions") must meet a range of performance specifications depending on the end use of the pipe and geographically specific regulations. The PE-RT specifications are provided in ISO <NUM>-<NUM> which specify the pipe characteristics necessary for hot and cold water handling within building construction applications. The primary mechanical specification of ISO <NUM>-<NUM> is the pipe's resistance to bursting under hydrodynamic (hoop) stress at various temperatures and times. In addition to long term burst resistance, a key resin characteristic is extrudability (extruder processability) since these pipes are typically small diameter (up to <NUM>) fabricated at relatively fast extrusion rates which can introduce finishing issues such as melt fracture resulting in a poor surface finish and possibly impacting properties. As described below in detail, another requirement of ISO <NUM>-<NUM> is an unblemished, smooth surface finish.

It is to be understood that while the invention has been described in conjunction with the specific embodiments thereof, the foregoing description is intended to illustrate and not limit the scope of the invention. Other aspects, advantages and modifications will be apparent to those skilled in the art to which the invention pertains.

Therefore, the following examples are put forth so as to provide those skilled in the art with a complete disclosure and description and are not intended to limit the scope of that which the inventors regard as their invention.

International Organization for Standardization (ISO) <NUM>-<NUM> specifies the characteristics of pipe made of polyethylene of raised temperature resistance ("PE-RT"), Type I intended to be used for hot and cold water installations within buildings for the conveyance of water, whether or not the water is intended for human consumption (domestic systems), and for heating systems, under the design pressures and temperatures appropriate to the class of application according to ISO <NUM>-<NUM>.

Pipe material as used herein refers to the material from which the pipe is made and means the polyethylene compositions described herein as polyethylene of raised temperature resistance ("PE-RT"). Pipe material is evaluated in accordance with ISO <NUM> or equivalent, with internal pressure tests carried out in accordance with ISO <NUM>-<NUM> and ISO <NUM>-<NUM>, to determine the σLPL values. The σLPL value is at least as high as the corresponding values of the reference curves given in <FIG> (taken from ISO <NUM>:<NUM>) over the complete range of times. Alternatively, one equivalent way of evaluation is to calculate the σLPL value for each temperature individually.

The reference curves for PE-RT Type I in <FIG> in the temperature range of <NUM> to <NUM> are derived from Equations (<NUM>) and (<NUM>). First branch (i.e., the left-hand portion of the lines shown in <FIG>): <MAT> Second branch (i.e., the right-hand portion of the lines shown in <FIG>): <MAT>.

The <NUM> values are determined separately using water inside and air outside the test specimen and are not derived from Equations (<NUM>) and (<NUM>).

In order to demonstrate conformance to the reference lines, pipe samples should be tested in accordance with ISO <NUM>-<NUM> and ISO <NUM>-<NUM> at the following temperatures: <NUM>; <NUM> to <NUM>; and <NUM>, and at various hoop stresses such that, at each of the temperatures, at least three failure times fall in each of the following time intervals: <NUM> to <NUM>; <NUM> to <NUM>,<NUM>; <NUM>,<NUM> to <NUM>,<NUM> and over. In tests lasting more than <NUM>,<NUM> without failure, any test time after <NUM>,<NUM> can be considered as the failure time.

Dimensions are measured in accordance with ISO <NUM>. The maximum calculated pipe value, Scalc, max, for the applicable class of service condition and design pressure, pD, are in accordance with Table <NUM> for PE-RT Type I. The values of outside diameter and wall thickness apply to the PE-RT pipe and, for design calculation purposes, are exclusive of any barrier layer thickness.

For corresponding pipe dimension class, the mean outside diameter, dem of pipe is in accordance with Tables <NUM>, <NUM>, <NUM>, and <NUM> below.

For any particular class of service condition, design pressure and nominal size, the minimum wall thickness, emin, is such that the corresponding S series or Scalc value is less than or equal to the values of Scalc, max given in Table <NUM>. For the corresponding pipe dimension class, the wall thicknesses, emin and en, is in accordance with Tables <NUM>, <NUM>, <NUM> or <NUM> as applicable, in respect of pipe series S or Scalc values. However, pipes joined together by fusion have a minimum wall thickness of <NUM>. The tolerance on the wall thickness, e, is in accordance with Table <NUM>.

Per the requirements of ISO <NUM>, the pipe is tested using the test methods and test parameters specified in Table <NUM>.

The pipe is tested using the test method and test parameters, and conforming to the requirements of ISO <NUM> as specified in Table <NUM>.

Principles for the calculation of the maximum calculated pipe value, Scalc, max values are provided below. Hence the determination of minimum wall thickness, emin of pipes, relative to the classes of service conditions (application class) in accordance with ISO <NUM>-<NUM> Table <NUM> and the applicable design pressure, pD.

The design stress, σD, for a particular class of service conditions (application class) is calculated using Equations (<NUM>) and (<NUM>), using Miner's rule in accordance with ISO <NUM>, and taking into account the applicable class requirements given above, and the service coefficients given in Table <NUM> below.

The resulting design stress, σD, as provided in ISO <NUM>, is given in Table <NUM> below.

The derivation of the maximum value of Scalc, Scalc, max, is the smaller of the values obtained from Equations (A. <NUM>) and (A. <NUM>): <MAT> where.

The valves of Scalc, max relative to each class of service are given in Table <NUM>.

The S series and Scalc values are chosen for each application class and design pressure from Tables <NUM>, <NUM>, <NUM> or <NUM>, as applicable, in such a way that S or Scalc is not greater than Scalc, max given in Table <NUM> for PE-RT Type I.

Reactor granules from Comparative <NUM> (<NUM>. 5MI, <NUM>/cc), Reference <NUM> (<NUM>. 5MI, <NUM>/cc), and Reference <NUM> (<NUM>. 2MI, <NUM>/cc) were mixed in a Coperion ZSK-<NUM> twin screw extruder at <NUM> lbs/hr output rate with a standard antioxidant and metal deactivation additive package.

The density of the polyethylene composition referred to herein as Comparative <NUM> was. <NUM>/cm<NUM> having a melt index of. <NUM>/<NUM>. The composition includes a processing aid additive and a thermal stabilizer additive and is used in applications such as blown film, collation shrink, food packaging, form fill and seal packaging, multilayer packaging film, heavy duty bags, shrink film, lamination film, and stand up pouches.

The density of the polyethylene composition referred to as Reference <NUM> was. <NUM>/cm3 having a melt index of <NUM> (<NUM>/<NUM>). This composition includes a processing aid additive and a thermal stabilizer additive, and is used in applications such as collation shrink, lamination film, compression packaging, and multilayer packaging film.

Flexural modulus, tensile modulus, environmental stress crack resistance ("ESCR"), notched constant ligament series ("NCLS"), and oxidative induction temperature ("OIT") were measured for each sample and compared to an industry standard for PE-RT type I referred to herein as Comparative <NUM>. The physical and thermal properties of the polyethylene compositions are summarized in Table 11A and Table 11B below. In addition, <FIG> shows the results from tensile strength studies at various strain rates at an elevated (<NUM>) temperature acquired at Datapoint Labs.

At a higher strain rate, the strength of the polyethylene composition (sometimes referred to as a "resin") was dominated by its density and MI. When the strain rate is low, due to its poor conomomer distribution, the strength of the Comparative <NUM> deteriorates quickly. In summary, the physical characteristics of the Reference <NUM> and Reference <NUM> polyethylene compositions meet or exceed those of the Comparative <NUM> incumbant composition for most physical property tests. Furthermore, each of the four polyethylene composition grades were shown to meet the <NUM> minute minimium requirement for oxidative induction temperature at <NUM>.

Small amplitude oscillatory shear ("SAOS") rheology and capillary rheology was acquired for the Comparative <NUM>, Reference <NUM>, and Reference <NUM> polyethylene compositions as well as the industry control Comparative <NUM> as shown in <FIG>.

All measurements in small angle oscillatory shear have been conducted using TA Instruments advanced rheometric expansion system (ARES). Parallel plate fixtures of <NUM> were used for small-angle oscillatory shear measurements at <NUM> and a frequency range <NUM>-<NUM> rad/s (add here actual frequency-range). All measurements were made within the linear regime as confirmed from strain sweep experiments. After loading and every temperature change the samples have been equilibrated at constant temperature during approximately <NUM> minutes until normal forces were completely relaxed. In the course of the measurements, the sample has been kept under nitrogen protection to avoid thermal degradation.

From the complex viscosity response to angular frequency (shear rate) demonstrated in the figures, the polyethylene compositions advantageously demonstrate more shear thinning which for the <NUM>. 5MI Comparative <NUM> and Reference <NUM> polyethylene compositions lead to lower viscosity in typical extrusion conditions (~<NUM> - <NUM>-<NUM>) when compared to the Comparative <NUM>. The melt viscosity of the <NUM>. 2MI Reference <NUM> indicated comparable viscosity to the Comparative <NUM> resin for the shear rates tested.

Pipe samples for strength testing were fabricated in their standard multi-layer pipe structure with <NUM> outer diameter, <NUM> wall section, and an adhesive + EVOH barrier layer. Further, samples were fabricated with Comparative <NUM>, Reference <NUM>, and Reference <NUM> polyethylene compositions and compared to the incumbent benchmark composition, Comparative <NUM>. Barrier composition was EVOH and process aid was used during fabrication.

Extrusion performance of Comparative <NUM> and Reference <NUM> polyethylene compositions were superior to the Comparative <NUM> polyethylene composition incumbent. Both Comparative <NUM> and Reference <NUM> polyethylene compositions processed through the line under standard extrusion rates of <NUM>/min and were able to run at <NUM>/min at still meet size and aesthetic requirements of quality control. Extrusion performance of Reference <NUM> polyethylene composition under standard control conditions was comparable to Comparative <NUM> which was less than optimal and deemed unsuitable. Both polyethylene compositions required polymer processing aid (PTFE based additive) to be added to eliminate drag marking. Internal coil memory assessment of all fabricated pipes was similar and deemed acceptable. Fabricated pipes of the Reference <NUM>, Reference <NUM>, and Comparative <NUM> polyethylene compositions were noticeably whiter than Comparative <NUM>, which exhibited dull yellow tinge.

PE-RT Pipe samples were submitted for long term hydrostatic pressure testing, and the results are summarized below in Table <NUM>. Reference <NUM> and Reference <NUM> included a synthetic hydrocarbon viscosity modifier that improves coil memory, but that could reduce the time of failure and cause the pipe to hold less pressure.

Pipe samples for strength testing were fabricated by using a pipe extruder with nominal <NUM> outer diameter and <NUM> wall section.

Another PE-RT resin was produced for pipe extrusion and tests. It had a density of <NUM>/cc and a MI of <NUM> /<NUM>. PE-RT pipe samples were extruded by using an industrial pipe extruder. The nominal dimensions of the pipe samples were <NUM> outer diameter and <NUM> wall thickness. Various line speeds were tested from <NUM> to <NUM> meters per minutes against a commercial metallocene resin benchmark. Pipes were found to have good dimension and surface appearance.

Pipe samples were submitted for long term hydrostatic testing using DETERMINATION OF THE LONG-TERM HYDROSTATIC STRENGTH ISO <NUM>:2012ISO <NUM> at <NUM> temperatures: <NUM>, <NUM>, <NUM> and <NUM>. The pressure testing at <NUM>, <NUM> and <NUM> was performed using deionized water on the inside and on the outside of the pipe specimens. <NUM> air is used on the outside. The accuracy temperature and pressure is better than ±<NUM> and +<NUM>/-<NUM>% respectively. The measurement of the wall thickness are accurate within ±<NUM> and the diameter1 within ±<NUM>.

Table <NUM> summarizes the results of the observations obtained from the tests of the <NUM> different temperatures. Table <NUM> summarizes distribution of stress rupture data.

Table <NUM> summarizes the extrapolated strength values at te. By its LPL value of <NUM> MPa at <NUM> and <NUM> years the natural PE-RT pipe grade, this material has a minimum required strength (MRS) classification of <NUM> MPa and is thereby designated PE-RT <NUM> according to ISO <NUM>:<NUM>.

The resulting design hoop stresses of the Miner's rule calculations for a design time of <NUM> years are presented below. Table <NUM> lists the resulting design Hoop Stress and conformity check with the application classes.

Claim 1:
A PE-RT pipe made from a linear low density polyethylene (LLDPE) composition comprising at least <NUM> mole percent ethylene derived units and one or more alpha-olefin co-monomer derived units, wherein the polyethylene composition has a molecular weight distribution (Mw/Mn) of from <NUM> to <NUM>, a long chain branching index g'vis of from <NUM> to <NUM>, a density of from <NUM> to <NUM>/cm<NUM>, and a shear thinning ratio of <NUM> to <NUM>, wherein the one or more alpha-olefin co-monomer derived units is derived from propylene, butene, l-pentene; <NUM>-pentene with one or more methyl, ethyl, or propyl substituents; <NUM> -hexene; <NUM> -hexene with one or more methyl, ethyl, or propyl substituents; l-heptene; l-heptene with one or more methyl, ethyl, or propyl substituents; <NUM>-octene with one or more methyl, ethyl, or propyl substituents; <NUM>-nonene; l-nonene with one or more methyl, ethyl, or propyl substituents; ethyl, methyl, or dimethyl-substituted l-decene; l-dodecene; or a combination thereof and wherein the polyethylene composition has a tensile strength at <NUM>% strain that satisfies the following relationship: <MAT> wherein y is the tensile strength (MPa) at <NUM>% strain at <NUM> and x is the strain rate (s-<NUM>).