CA2243852C

CA2243852C - Polyolefin elastomer blends exhibiting improved properties

Info

Publication number: CA2243852C
Application number: CA002243852A
Authority: CA
Inventors: Deepak R. Parikh; Pak-Wing S. Chum; Pradeep Jain; Rajen M. Patel; Timothy E. Clayfield; Thomas J. Mckeand, Jr.; Kyle G. Kummer; Wasif Ahmed Khan; Ronald P. Markovich
Original assignee: Dow Global Technologies LLC
Current assignee: Dow Global Technologies LLC
Priority date: 1996-01-22
Filing date: 1997-01-22
Publication date: 2006-11-07
Anticipated expiration: 2017-01-22
Also published as: CZ230898A3; NO983357L; HUP9900394A3; AU1709597A; AR012814A1; KR19990081912A; DE876427T1; CN1111563C; CA2243852A1; AU716317B2; HUP9900394A2; TR199801405T2; BR9707298A; WO1997026297A1; PT876427E; ES2123484T1; KR100445310B1; NO320562B1; US6005053A; PL327988A1

Abstract

Polymer mixtures are disclosed which comprise at least one homogeneously branched ethylene polymer (A) and at least one ethylene polymer (B) having a crystallinity which is at least 7 percent greater than the crystallinity of polymer (A) with certain provisos. A process for making a molded article using the disclosed polymer mixtures is disclose d as well as films, film layers, coatings and molded articles formed from those mixtures. These mixtures have several advantages over polymer compositions of the prior art, including improved properties at elevated temperatures such as improved softening point under load, improved hardness, improved toughness, improved 100 percent modulus of elasticity, improved compression set, improved ability to prevent oil bleed out at lower temperatures when the mixture contains oil and reduced injection molding cycle time. The mixtures retain their performance advantages even when substantial amounts of additives such as oil and filler are incorporated into the mixture. The mixtures may also be cross-linked after they are formed into the shape of an article to form vulcanized elastomeric products. The polymer mixtures have utility in a variety of applications.

Description

This invention relates to ethylene polymer compositions, processes for making such polymer compositions, and molded articles made from such compositions.
Ethylene homopolymers and interpolymers are known classes of thermoplastic polymers, each having many members. They are prepared by homopolymerizing ethylene or interpolymerizing (for example, copolymerizing) ethylene with one or more vinyl- or diene-based comonomers, for example, a-olefins of 3 to about 20 carbon atoms, vinyl esters, vinyl acids, styrene-based monomers, 1o monomers containing two or more sites of ethylenic unsaturation, etc., using known copoiymerization reactions and conditions.
Although ethylene homopolymers and interpolymers are known for their strength and processability, experiments continue to be conducted which explore the outer limits of these properties. One result of this research was the development of substantially linear ethylene polymers (SLEPs) which are less susceptible to melt fracture or formation of extrudate defects during high pressure, high speed extrusion than are conventional polyethylenes. SLEPs possess high processibility and strength without requiring additives.
Thermoplastic elastomers are known materials possessing both elastomeric 2o and thermoplastic characteristics. These materials are becoming increasingly popular in industrial applications because of their ease of fabrication and general good physical properties. Thermoplastic elastomers are of two main types, (1 ) block and graft copolymers containing soft and hard polymer chain segments, and {2) blends of certain elastomers and thermoplastics. Examples of the latter class include blends of ethylenelpropylene rubber (EDPM) with polyolefin thermoplastics, such as polypropylene or polyethylene.
Although the various types of ethylene polymers have found application in a wide range of environments, in certain of these environments improvement is both possible and desirable. For example, applications requiring good pertormance at 3o elevated temperatures (that is, temperatures above room temperature) abound.
Relevant properties under these conditions include softening point under load, toughness, 100 percent modulus of elasticity, and compression set.
Processability improvements are also desirable, for example certain ethylene polymers require a long cooling cycle time in infection molding applications. The need for thermoplastic elastomers with increased high temperature performance that are easy to process is expressed, for example, in U.S. Patent 5,371,143. Polymers or polymer blends which possess a high softening point under load, greater toughness, higher 100 percent modulus of elasticity, tower compression set, and reduced cycle time are thus desired.
According to this invention, these and other desired results are achieved with a polymer mixture comprising:
(A) at least one homogeneously branched ethylene polymer having a crystallinity in the range from 0 to 50 percent and (B) at least one ethylene polymer having a crystallinity in the range from 5 to 80 percent which is at least 7 percent greater than the crystallinity of component (A) provided that (1) (a) when component (A) has a crystallinity greater than or equal to 21.5 percent and a melt index less than or equal to 10 dglmin., component (B) is a homogeneous polymer and (b) when the crystallinity of component (B) is greater than 21.5 percent, component (B) is present in an amount less than 40 wt percent (2) the number average molecular weight of component (B) is greater than or equal to the number average molecular weight of polymer (A), (3) component (B) comprises at least one interpolymer of ethylene with at least one comonomer selected from the group consisting of vinyl esters of a saturated carboxylic acid wherein the acid moiety has up to 4 carbon atoms, unsaturated mono- or dicarboxylic acids of 3 to 5 carbon atoms, a salt of the unsaturated acid, esters of the unsaturated acid derived from an alcohol having 1 to 8 carbon atoms, and mixtures thereof, and (4) at least one of the ethylene polymer components of the polymer mixture comprises an ultra-low molecular weight ethylene polymer having a crystailinity from 0 to 80 percent, a melt viscosity at 350°F up to 8200 cp and a molecular weight distribution from 1.5 to 2.5, wherein the polymer mixture has an overall crystallinity in the range from 6 to 50 percent and when component (B) does not comprise interpolymer (B)(3) and none of the ethylene polymer components of the polymer mixture comprise the ultra-low molecular weight ethylene polymer, the polymer i i ' mixture has a molecular weight distribution not greater than 3 when the overall crystallinity is greater than or equal to 21.5 percent.
This polymer mixture may further comprise:
(C) at least one homogeneously branched ethylene polymer having a crystallinity between the crystallinities of components (A) and (B) and having a crystallinity which differs from the crystallinities of components (A) and (B) by at least 7 percent.
In one embodiment of a polymer mixture comprising component (C), the crystallinity of component (B) is at least 30~ greater than the crystallinity of component (A).
Another aspect of this invention is a process for injection molding a polyolefin having a reduced cycle time comprising:
(A) heating a polymer mixture according to the present invention as described above to a temperature suitable for injection molding;
(B) injecting the polymer mixture of step (A) into a mold to form the molded article; and (C) removing from the mold the molded article formed in step (B).
This process may optionally include:
(B1) cooling the molded article of step (B) and/or (B2) crosslinking the molded article of step (B).

In another aspect, process step (B1) may have a cooling time that is at least 20 percent less than the cooling time of step (B1) conducted under the same conditions with a single ethylene polymer made of the same monomer components as component (A) having the same crystallinity and melt index as the polymer mixture.
According to another aspect of the present invention, there is provided the process as described herein wherein, in step (A) of the process, component (A) is produced in a first reaction vessel, component (B) is produced in a second reaction vessel operating simultaneously with the first reaction vessel and interconnected with the first reaction vessel such that component (A) is continuously mixed with component (B) as components (A) and (B) are being produced.
According to still another aspect of the present invention, there is provided a molded article obtained by forming a polymer mixture described herein into a shape and causing the shaped polymer mixture to become fixed in shape.
According to yet another aspect of the present invention, there is provided the article described herein wherein the shaped polymer mixture has at least two differential scanning calorimetry melting peaks and lacks a differential scanning calorimetry peak above 115°C.
According to a further aspect of the present invention, there is provided the article described herein wherein the shaped polymer mixture has a softening point under load of at least about 80°C, a 100 modulus of 3a ' elasticity of at least 140 psi, a compression set of less than 80~ at 70°C, an overall crystallinity less than 21.5 and a crosslink density less than 20~ gel.
According to yet a further aspect of the present invention, there is provided the article described herein wherein the shaped polymer mixture has a crosslink density of at least 50o gel.
Yet another aspect of this invention is the molded article obtained by molding the polymer mixture according to the present invention.
FIGURE 1 shows two pairs of probe penetration versus temperature plots, one pair at a constant probe force of 1 Newton (N) and the other pair at a constant probe force of 0.1 N, for a single substantially linear ethylene 1-octene copolymer commercially available from Dow Chemical Company under the trademark EG 8100 (SLEP 1) and an 80:20 blend (blend A) of a low crystallinity (9.2 percent) substantially linear ethylene 1-octene copolymer (SLEP 2) with a higher crystallinity (33.2 percent) substantially linear ethylene 1-octene copolymer (SLEP 3), blend A having the same crystallinity (14.0 percent) as the single polymer, SLEP 1. Probe penetration was determined using the same conditions for each sample, which included using a flat tip probe having a 1 mm tip diameter, heating the polymer sample under a nitrogen atmosphere at a rate of 5°C/mm (starting at room temperature), and measuring probe penetration relative to temperature.
FIGURE 2 shows probe penetration versus temperature plots obtained with the procedure described above for FIGURE 1 for five two-component blends of 3b substantially linear ethylene 1-octane copolymers according to the present invention (blends B-F), each having the same blend crystallinity (17.8 percent), in which the difference in crystallinity between the components is varied from 7.5 percent to 36 percent, and a single substantially linear ethylene 1-octane copolymer having the same crystallinity.
FIGURE 3 shows the softening point under load (SPUL) of SLEP 2, SLEP 3 and blend A as defined in FIGURE 1. The softening point means the temperature at which a TMA probe having a constant force of 1 N penetrates 1 mm into the polymer sample using the procedure for determining probe penetration versus temperature of FIGURE 1.
FIGURE 4 shows Shore A hardness vs. temperature data for single polymer SLEP 1 {defined above) and polymer blends A and G according to the present invention, each having the same crystallinity. Blend A is defined above and blend G
is a blend of SLEP 2 (defined above) and a linear low density ethylene polymer (LLDPE1).
FIGURE 5 shows Shore A hardness vs. temperature plots for a substantially linear ethylene 1-octane copolymer (SLEP 7), blend H according to the present invention, and comparative blend C-1. Blend H is a 50:50 blend of a low crystallinity substantially linear ethylene 1-octane copolymer (SLEP 9) and a higher crystallinity {38.2 percent) substantially linear ethylene 1-octane copolymer (SLEP 6) in which the number average molecular weight (M~) of SLEP 6 is greater than that of SLEP 9.
Blend C-1 is a 50:50 blend of low crystallinity (SLEP 1) and higher crystaflinity (SLEP
10) substantially linear ethylene 1-octane copolymers, each having the same crystallinity as the corresponding components of blend H, but the M~s of the lower and higher crystallinity components are reversed so that the M" of the lower crystallinity component is higher than the M" of the higher crystallinity component.
Blend C-1 is for illustration only and is not to be taken as an admission of prior art.
FIGURE B shows compression set at 70 C relative to blend ratio and blend density for two pairs of low and high crystallinity polymer components at five blend 3o ratios. One pair, SLEP 9/SLEP 6, is a combination of a low crystallinity, low Mn substantially linear ethylene 1-octane copolymer with a higher crystallinity, higher Mn ethylene 1-octane copolymer and the other pair, SLEP 1/SLEP 10, is a combination of lower and higher crystallinity substantially linear ethylene 1-octane copolymers in which, as stated above for FIGURE 5, the M~s of the lower and higher crystallinity - components are reversed from those of SLEP 9/SLEP 6, so that the M~ of the lower crystallinity component is higher than the Mn of the higher crystallinity component.
FIGURE 7 illustrates the improvement in oil loading and effect on Shore A
~ hardness for the BLEND (labelled in FIGURE 7) compared to pure Dow ENGAGETM
EG8003 (labelled PURE in FIGURE 7) having a melt index of 1.0 g/10min. and a ' density of 0.885 g/cc. The BLEND consisted of a polyole~n elastomer, EG8100 having a melt index of 1.0 g/l0min. and a density of 0.87g/cc, blended with a polyolefin plastomer, AFFINITYT"" PL1880 having a melt index of 1.0 g/l0min.
and a density of 0.902 glcc, in a 53:47 ratio to give an overall melt index of 1.0 g/l0min.
1o and a density of 0.885 g/cc.
FIGURE 8 shows apparent viscosity at 130 C for single resin and binary blend, both containing talc and oil. Formulation contained 66.67 percent polymer, 16.67 percent oil and 16.66 percent talc. The single resin polymer had a melt index of 1.0 g/10 min. and a density of 0.87 g/cc. The oil used was a United States is Pharmacopoeia (USP) white mineral oil, DuoprimeTM 200, supplied by Lyondell Petrochemical. The binary blend polymer (labelled BLEND in FIGURE 8) contained 80 percent DEG 8180, having a melt index of 0.5 g/10 min and a density of 0.863 g/cc, and 20 percent PF 1140, having a melt index of 1.6 g/10 min. and a density of 0.895 g/cc, to give an overall melt index of 0.6 g/10 min. and density of 0.87 g/cc.
2o FIGURE 9 shows stress-strain behavior of the single resin and binary blend, both containing talc and oil. The formulations are as described for FIGURE 8.
FIGURE 10 shows Shore A versus temperature for a single resin and binary blend, both containing talc and oil. The formulations are as described for FIGURE 8.
FIGURE 11 shows the dynamic modulus versus temperature of a single resin 25 and binary blend, both containing talc and oil. The formulations are as described for FIGURE 8.
FIGURE 12 shows thermomechanical analysis {TMA) of 2- and 3-component blends. The 2- component blend (labelled in FIGURE 12) consists of 50 percent EG8200, 20 percent PF1140 and 30 percent ShelIfIexT"~ 371 oil and the 3o 3-component blend {labelled in FIGURE 12) consists of 30 percent EG8150, 14 percent PF1140, 3 percent IP-90, 23 percent CaC03 and 30 percent ShellflexT""

oil.
FIGURE 13 shows stress-strain behavior at room temperature of blends made from different comonomer polymers of the lower density component, both containing - oil. One blend consisted of Dow Chemical ENGAGET"" EG8100 having a melt index of 1.0 g/10 min. and a density of 0.87 g/cc and Dow Chemical's AFFINITYT""

having a melt index of 1.0 g/10 min. and a density of 0.902 g/cc. The other blend consisted of Mitsui Petrochemical's TAFMERT"" P0480 having a melt index of 1.0 g/10 min. and a density of 0.87 g/cc and Dow Chemical's AFFINITYT~" PL1880 (described above). Each blend was combined with 50 phr oil.
FIGURE 14 shows stress-strain behavior at elevated temperature {60C) for the same blends made from different comonomer polymers of the Power density component as in FIGURE 13.
i0 FIGURE 15 shows peak stress at ambient and elevated temperature (60C} of the blends made from different comonomer polymers of the lower density component.
FIGURE 16 shows hardness versus temperature for two polymers individually, a dual reactor polymer composition without oil and the same dua! reactor polymer composition with 30 percent oil. EG8100 is the same as above and CL8003 is a polymer available from The Dow Chemical Company having a melt index of 1.0 g/10min. and a density of 0.885 g/cc.
1. Basic Definitions Unless indicated to the contrary, all parts, percentages and ratios are by weight. The expression "up to" when used to specifiy a numerical range includes any value less than or equal to the numerical value which follows this expression.
The expression "cc" stands for "cubic centimeters".
The term "polymer" means a compound prepared by polymerizing monomers, whether of the same or a different type. The generic term polymer thus embraces the term "homopolymer", usually employed to refer to polymers prepared from only one type of monomer, and the term "interpolymer", as defined hereinafter.
The term "interpolymer" means polymers prepared by the polymerization of at least two different types of monomers. The generic term "interpolymer" thus includes the term "copolymers", which is usually employed to refer to polymers prepared from two different monomers, as well as to polymers prepared from more than two different types of monomers.
The term "homogeneous" polymers are ethylene interpolymers in which any comonomer is randomly distributed within a given interpolymer molecule and substantially all of the inte~polymer molecules have the same ethylenelcomonomer ratio within that interpolymer. Homogeneous polymers generally are characterized as having a single melting peak between -30C and 150C, as determined by differential scanning calorimetry (DSC). The single melting peak may be relatively broad, such as is the case when an.ethykne polymer having a crystallinity less than 36 percent is employed. The single melting peak may be sharp, such as is the case when an ethylene polymer having a crystallinity of at feast 36 percent is employed.
to Homogeneous polymers will also typically have a molecular weight distribution, M",/M~, less than or equal to 3 (when the density of the interpolymer is less than about 0.960 glcc) preferably less than or equal to 2.5.
In addition or in the alternative, the homogeneity of the polymers is typically described by the SCBDI (Short Chain $ranch Distribution Index) or~CDBI
~5 .Composition Distribution Branch Index) and is defined as the weight percent of the polymer molecules having a comonomer content within 50 percent of the median total molar comonomer content. The SC8DI of a polymer is readily ca~ulated from data obtained from techniques known in the art, such as, for example, temperature rising elution fractionation (abbreviated herein as "TREF'~ as described, for example, in 20 Wild et al, Journal of Polymer Science, Poly. Phys. Ed., Vol. 20, p. 441 (1982), in U.S. Patent 4,798,081 (Hazlitt et al.), or in U.S. Patent 5,089,321 (Chum et al.).
The SCBDI or CDBI for the homogeneous linear and for the substantially linear ethylenela-olefin polymers used in the present invention is preferably greater than 50 percent.
25 Heterogenous polymers are ethylenela-olefin interpolymers characterized as having a linear backbone and a DSC melting curve having a distinct melting peak greater than 115°C attributable to a high density fraction.
Heterogeneous interpolymers will typically have an M,IM~ greater than 3 (when the density of the interpolymer is less than about 0.960 glcc) and will typically have a CD81 less than or 3o equal to 50, indicating that such interpolymers are a mixture of molecules having differing comonomer contents and differing amounts of short chain branching.
The crystallinity in reference to an ethylene polymer is a well known property of ethylene polymers. Various techniques have been developed to measure ethylene polymer crystallinity.

- When the ethylene polymer is derived exclusively from hydrocarbon monomers (for example, non-functionalized ethylene a-olefin interpolymers}, the crystallinity can be determined from the density of the polymer using the following equation:
percent C = (p - pa) / p (p~- pa) x 100 in which percent C is the percent crystallinity of the ethylene polymer, pa is the density of an ethylene polymer which has 0 percent crystallinity (that is, 100 percent amorphous) at room temperature (0.852 g/cc.}, p~ represents the density of an ethylene polymer at 100 percent crystallinity at room temperature (1.000 g/cc.) and p 1o represents the density of the polymer for which the percent crystallinity is being determined. Density may be determined according to ASTM D792 in which the samples are annealed at ambient temperature for 24 hours before the measurement is taken.
Another method for determining the percent crystallinity of an ethylene polymer relies upon differential scanning calorimetry (DSC). The percent crystalfinity may be calculated with the equation:
percent C=(A/292 J/g) x 100, in which percent C represents the percent crystallinity and A represents the heat of fusion of the ethylene in Joules per gram (J/g).
Another method by which crystallinity can be determined is through the use of wide-angle X-ray diffraction (WAXD). The percent crystallinity may be calculated with the following equation:
percent C=(A~ /(Ae + A ~)) x 100, in which percent C again represents percent crystallinity, A~ represents the total area under the crystalline peaks of the WARD pattern and Aa + A~ represents the total area under the WAXD pattern, Aa representing the amorphous peaks.
When the ethylene polymer is a nonfunctionalized ethylene polymer, the method for determining percent crystallinity based on polymer density is preferred, and for any ethylene polymer the method based on DSC is preferred over the method 3o based on WARD.
The term "softening point under load" (SPUL) means the temperature at which probe penetration of 1 mm into the polymer is achieved using a device capable of applying a constant force of 1 N to a flat tip probe having a diameter of 1 mm while raising the temperature of the polymer from 25 C at a rate of 5 C/minute under a nitrogen atmosphere. One such device is a ThermoMechanical Analyzer (TMA) such as Model TMA-7 made by the P~erkin-Elmer Instrument Company. The procedure for conducting this test is described in more detail in the Examples section below.
The softening point can be approximated by measuring the temperature at which the Shore A hardness of the polymer, or polymer blend, is about 45.
2. Components (A), (B). and (C) Component (A) is at least one homogeneous ethylene polymer, preferably at least one substantially linear ethylene polymer (SLEP), having a crystallinity of 0 1o percent up to 50 percent. The crystaliinity of (A) is preferably at feast 2 percent and preferably up to 30 percent, more preferably up to 20 percent, and even more preferably up to 15 percent. Component (A) is preferably of a type obtainable by using a metallocene catalyst.
Component (B) is at least one homogeneous or heterogeneous ethylene polymer having a crystallinity of at feast 5 percent, preferably at feast 10 percent, more preferably at least 21.5 percent and preferably up to 80 percent, more preferably up to 60 percent, even more preferably up to 50 percent. However, when component (A) has a crystallinity greater than or equal to 21.5 percent and a melt index (MI) s 10 dg/min., component (B) is preferably a homogeneous polymer.
SLEPs, linear low density polyethylenes (LLDPEs), low density polyethylenes (LDPEs), high density polyethylenes (HDPEs) , ethylene terpolymers and ethylene copolymers with carboxylic acids, esters and salts, such as ethylene vinyl acetate (EVA), ethylene acrylic acid (EAA), etc., are among the ethylene polymers that may be used as component (B). SLEPs are preferred.
Optional component (C) is at least one homogeneous ethylene polymer, preferably at least one SLEP, having a crystailinity of at least 7 percent, preferably at least 14 percent, up to 73 percent.
Components (A), (B), and (C) are preferably sufficiently compatible with each other that they are miscible in each other when in the molten form. The polymer 3o mixture of this invention is preferably a single phase mixture when in the molten form.
Homogeneous Ethylene Polymers The homogeneous polyethylenes that can be used as components (A), (B), and (C) of this invention fall into two broad categories, the linear homogeneous polyethylenes and the substantially linear homogeneous polyethylenes. Both are known.
Homogeneous linear ethylene polymers have long been commercially available. As exemplified in U.S. Patent No. 3,645,992 to Elston, homogeneous linear ethylene polymers can be prepared in conventronal polymerization processes using Ziegler-type catalysts such as, for example, zirconium and vanadium catalyst systems. U.S. Patent No. 4,937,299 to Ewen et al. and U.S. Patent No.
5,218,071 to Tsutsui et ai. disGose the use of metallocene catalysts, such as catalyst systems based on hafnium, for the preparation of homogeneous linear ethylene polymers.
to Homogeneous linear ethylene polymers are typically characte~~zed as having a molecular weight distribution, My~IMn, of about 2. Commercially available examples of homogeneous linear ethylene polymers include those sold by Mitsui Petrochemical Industries as TafmerT"" resins and by Exxon Chemical Company as Exadt"' resins.
The substantially linear ethylene polymenr (SLEPa) are homogeneous polymers having long chain branching. They are disclosed in U.S. Patent Nos. 5,272,236 and 5,278,272. SLEPs which are available from The Dow Chemical Company as polymers made by the InsiteT"' Process and Catalyst Technology such as Affinity T""
polyolefin plastomers (POPS) and as EngageT"' polyolefin elastomers (P01's).
ZO Specific examples include polymer products designated EG 8100, EG 8150, PF
1140, CL 8003, PL 1880, SM 1300 and SM 8400, each of which is commercially available from The Dow Chemical Corporation. SLEPs can be prepared via the solution, slurry, or gas phase, preferably solution phase, polymerization of ethylene and one or more optional a-olefin comonomers in the presence of a constrained geometry catalyst, such as is disGosed in European Patent Application 416,815-A .
The constrained geometry catalysts are described in more detail later.
The term "substantially linear" means that, in addition to the short chain branches attributable to homogeneous comonomer incorporation, the ethylene polymer is further characterized as having long chain branches in that the polymer backbone is substituted with an average of 0.01 to 3 long chain branches11000 carbons. Preferred substantially linear polymers for use in the invention are substituted with from 0.0'1 long chain branchl1000 carbons to 1 long chain branch11000 carbons, and more preferably from 0.05 long chain branch/1000 carbons to 1 long chain branch11000 carbons.
"Long chain branching" (LC8) means a chain length of at least 6 carbons, above which the length cannot be distinguished using "C nuGear magnetic resonance spectroscopy. Each long chain branch has the same comonomer distribution as the polymer backbone and can be as long as the polymer backbone to which it is attached.
The presence of long chain branching can be determined in ethylene polymers by using "C nuclear magnetic resonance (NMR) spectroscflpy and is quantified using the method described by Randall (Rev. Macxomol. Chem. Phys., C.29, V. 283, p. 285-297).
As a practical matter, current "C nuclear magnetic resonance spectroscopy cannot determine the length of a long chain branch in excess of six carbon atoms.
However, there are other known techniques useful for determining the presence of long chain branches in ethylene polymers, including ethylenell-octene interpolymers.
Two such methods are gel permeation chromatography coupled with a low angle laser light scattering detector (GPC-LALLS) and gel permeation chromatography coupled with a differential viscometer detector {GPC-DV). The use of these 2o techniques for long chain branch detection and the underlying theo~~es have been well documented in the literature. See, for example, Zimm, G.H. and Stockmayer, W.H., J.Chem. Phys., 17,1301 (1949) and Rudin, A., Modern Methods of Pol~rmer Characterisation, John Wiley 8 Sons, New York (1991) pp. 103-112.
A. Willem deGroot and P. Steve Chum, both of The Dow Chemical Company, at the October 4, 1994 conference of the Federation of Analytical Chemistry and Spectroscopy Society (FACSS) in St. Louis, Missouri, presented data demonstrating that GPC-DV is a useful technique for quantifying the presence of long chain branches in SLEPs. In particular, deGroot and Chum found that the level of long 3o chain branches in homogeneous SLEP samples measured using the Zirnm-Stockmayer equation correlated well with the level of long chain branches measured using "C NMR.
Further, deGroot and Chum found that the presence of octene does not change the hydrodynamic volume of the polyethylene samples in solution and, as _ such, one can account for the molecular weight increase attributable to octene short chain branches by knowing the mole percent octene in the sample. By deconvaluting the contribution to molecular weight increase attributable to 1-octene short chain branches, deGroot and Chum showed that GPC-DV may be used to quantify the level of long chain branches in substantially linear ethylene/octene copolymers.
deGroot and Chum also showed that a plot of Log (i2, Melt Index} as a ' function of Log{GPC Weight Average Molecular Weight} as determined by GPC-DV
illustrates that the long chain branching aspects (but not the extent of long branching) of SLEPs are comparable to that of high pressure, highly branched low density 1o polyethylene (LDPE) and are clearly distinct from ethylene polymers produced using Ziegler-type catalysts such as titanium complexes and ordinary catalysts for making homogeneous polymers such as hafnium and vanadium complexes.
For ethylene/a-olefin interpoiymers, the long chain branch is longer than the short chain branch that results from the incorporation of the a.-olefins) into the polymer backbone. The empirical effect of the presence of long chain branching in the substantial linear ethylene/a-olefin interpolymers used in the invention is manifested as enhanced theological properties which are quantified and expressed herein in terms of gas extrusion rheometry (GER) results and/or melt flow, I,~IIa, increases.
2o In contrast to the term "substantially linear", the term "linear" means that the polymer lacks measurable or demonstrable long chain branches, that is, the polymer is substituted with an average of less than 0.01 long chain branch/1000 carbons.
SLEPs are further characterized as having:
{a) a melt flow ratio, I,~/Iz > 5.63, {b) a molecular weight distribution, MW/M~ as determined by gel permeation chromatography and defined by the equation:
(MW/M~} < {I,o/Iz) - 4.63, (c) a critical shear stress at the onset of gross melt fracture, as determined by gas extrusion rheometry, of greater than 4 x 106 dynes/cmz or a gas extrusion theology such that the critical shear rate at onset of surface melt fracture for the SLEP is at least 50 percent greater than the critical shear rate at the onset of surface melt fracture for a linear ethylene polymer, wherein the SLEP and the linear ethylene polymer comprise the same comonomer or comonomers, the linear ethylene polymer has an h, M""IM" and density within ten percent of the SLEP and inrherein the respective critical shear rates of the SLEP and the linear ethylene polymer are measured at the same melt temperature using a gas extrusion rheometer, and (d) a single differential scanning taiorimetry, DSC, mening peak between -30 and 150 C.
Determination of the critical shear rate and critical shear stress in regards to melt fracture as well as other fieology properties such as Theological processing index (PI), is performed using a gas extrusion rheometer (GER). The gas extrusion i0 rheometer is described by M. Shida, R.N. Shroff and L.V. Cancio in Polymer Engineering Science, Vol. 17, No. 11, p. 770 (1977), and in "Rheometers for Molten Plastics" by John Dealy,published by Van Nostrand ReinholdCo. (1982) on pp. 97-99. GER experiments are performed at a temperature of 190 C, at nitrogen pressures between 250 to 5500 psig using a 0.0754 mm diameter, 20:1 LID die with an entrance angle of 180°. For the SLfPs described herein, the PI is the apparent viscosity (in kpoise) of a material measured by GER at an apparent shear stress of 2.15 x 1~ dynelcm~.
The SLEPs for use in the invention includes ethylene interpolymers and have a PI in the range of 0.01 kpoise to 50 kpoise, preferably 15 kpoise or less. The SLEPs used 2o herein have a PI less than or equal to 70 percent of the PI of a linear ethylene polymer (either a 2iegler polymerized polymer or a linear uniformly branched polymer as described by Elston in US Patent 3,645,992) having an 12, M"!M" and density, each within ten percent of the SLEPs.
The Theological behavior of SLEPs can also be characterized by the Dow Rheology Index (DRI), which expresses a polymer's "normalized relaxation time as the result of long chain branching " (See, S. Lai and G.W. KnigM ANT~C '93 Proceedings, INSITE""' Technology Polyolefins (SLEP) - New Rules in the StructurelRheology Relationship of Ethylene a-Oefin Copolymers, New Orleans, La., May 1993). DRI values range from 0 for polymers which do not 3p have any measurable long chain branching (for example, Tafmer""
products available from Mitsui Petrochemical Industries and ExadTM products available from Exxon Chemical Company) to about 15 and are independent of melt index. In general, for low to medium pressure ethylene polymers (particularly at lower densities) DRI provides improved ~orrelations to melt elasticity and high shear flowability relative to correlations of the same attempted with melt flow ratios. For the SLEPs useful iri this invention, DRI is preferably at (east 0.1, and espeaally at least 0.5, and most especially at least 0.8. DRI can be calculated from the equation:
ORI = (3652879 » to'.°°"°/ ~a 1)/10 where to is the characteristic relaxation time of the material and n o is the zero shear viscos'dy of the material. Both To and ~ o are the "best fd" values to the Cross equation, that is, rl Iq o = 1/(1 + (Y ~ to )''") in which n is the power law index of the material, and ~ and Y are the measured viscosity and shear rate, respectively. Baseline determination of viscosity and shear rate data are obtained using a Rheometric Mechanical Spectrometer (RMS-800) under dynamic sweep mode from 0.1 to t00 radianslsecond at lfi0 C and s Gas i5 Extrusion Rheometer (GER) at extrusion pressures from 1,000 psi to 5,000 psi (6.89 to 34.5 MPa), which corresponds to shear stress from 0.088 to 0.43 MPa, using a 0.0754 mm diameter, 20:1 LID die at 190 C. Specific material determinations can be performed from 140 to 190 C as required to au:ommodate matt index variations.
An apparent shear stress versus apparent shear rate plot is used to identify 2o the melt fracture phenomena and quantify the critical shear rate and critical shear stress of ethylene polymers. According to Ramamurthy in the Jo~na! of Rheology, 30(2), 337-357, 1986, above a certain critical flow rate, the observed extrudate irregularities may be broadly classified into two main types: surface melt fracture and gross melt fracture.
25 Surface melt fracture occurs under apparently steady flow conditions and ranges in detail from loss of specular film gloss to the more severe form of "sharkskin." Herein, as determined using the above-described GER, the onset of surtace melt fracture (OSMF) is characterized at the beginning of losing extrudate gloss at which the surface roughness of the extrudate can only be detected by 3o magnification. The critical shear rate at the onset of surface melt fracture for the SLEPs is at least 50 percent greater than the critical shear rate at the onset of surtace melt fracture of a linear ethylene polymer having essentially the same h and M"~II".

_ Gross melt fracture occurs at unsteady extrusion flow conditions and ranges in detail from regular (alternatirig rough and smooth, helical, etc.) to random distortions. For commercial acceptability to maximize the performance properties of films, coatings and moldings, surtace defects should be minimal, if not absent. The critical shear stress at the onset of gross melt fracture for the SLEPs, especially those having a density >0.910 g/cc, used in the invention is greater than 4 x dynes/cm2. The critical shear rate at the onset of surface melt fracture (OSMF) and the onset of gross melt fracture (OGMF) will be used herein based on the changes of surface roughness and configurations of the extrudates extruded by a GER.
Preferably, the SLEP will be characterized by its critical shear rate when used as the first ethylene polymer of the invention and by its critical shear stress when used as the second ethylene polymer of the invention.
The SLEPs used in the invention are also characterized by a single DSC
melting peak. The single melting peak is determined using a differential scanning is calorimeter standardized with indium and deionized water. The method involves 3-7 mg sample sizes, a "first heat" to about 180 C which is held for 4 minutes, a cool down at 10 C/min. to -30 C which is held for 3 minutes, and heat up at 10 Clmin. to 140 C for the "second heat". The single melting peak is taken from the "second heat"
heat flow vs. temperature curve. Total heat of fusion of the polymer is calculated 2o from the area under the curve.
For polymers having a density of 0.875 g/cc to 0.910 g/cc, the single melting peak may show, depending on equipment sensitivity, a "shoulder or a "hump" on the low melting side that constitutes less than 12 percent, typically, less than 9 percent, and more typically less than 6 percent of the total heat of fusion of the polymer. Such 25 an artifact is observable for other homogeneously branched polymers such as ExactT~" resins and is discerned on the basis of the slope of the single melting peak varying monotonically through the melting region of the artifact. Such an artifact occurs within 34 C, typically within 27 C, and more typically within 20 C of the melting point of the single melting peak. The heat of fusion attributable to an artifact can 30 separately determined by specific integration of its associated area under the heat flow vs. temperature curve.
The SLEPs are analyzed by gel permeation chromatography (GPC) on a Waters 150 C high temperature chromatographic unit equipped with differential refractometer and three columns of mixed porosity. The columns are supplied by Polymer Laboratories and are commonly packed with pore sizes of 103, 104, 105 and 106. The solvent is 1,2,4-trichlorobenzene, from which 0.3 percent by weight solutions of the samples are prepared for injection. The flow rate is1.0 mllmin, unit operating temperature is 140 C, and the injection size is 100 microliters.
The molecular weight determination with respect to the polymer backbone is deduced by using narrow molecular weight distribution polystyrene standards (from Polymer Laboratories) in conjunction with their elution volumes. The equivalent polyethylene molecular weights are determined by using appropriate Mark-Houwink coefficients for polyethylene and polystyrene (as described by Williams and Ward in io Journal of Polymer Science, Polymer Letters, Vol. 6, p. 621, 1968) to derive the equation Mpolyethylene = a ' (Mpolystyrene)b~
In this equation, a = 0.4316 and b = 1Ø Weight average molecular weight, MW, is calculated in the usual manner according to the formula MW = ~{w. x M.,) where w, and M; are the weight fraction and molecular weight, respectively, of the ith fraction eluting from the GPC column.
SLEPs are known to have excellent processability, despite having a relatively narrow molecular weight distribution (that is, the MW/Mn ratio is typically less than 3.5).
Moreover, unlike homogeneously and heterogeneously branched linear ethylene 2o polymers, the melt flow ratio (I,o/l2) of SLEPs can be varied independently of the molecular weight distribution, M""/M".
Accordingly, the first ethylene polymer, Component {A), of the inventive polymer mixtures is preferably a SLEP.
Heterocteneous Ethylene Polymers The heterogeneous polyethylenes that can be used in the practice of this invention fall into two broad categories, those prepared with a free radical initiator at high temperature and high pressure, and those prepared with a coordination catalyst at high temperature and relatively low pressure. The former are generally known as low density polyethylenes (LDPE) and are characterized by branched chains of polymerized monomer units pendant from the polymer backbone. LDPE polymers generally have a density between about 0.910 and 0.935 g/cc. Ethylene polymers and copolymers prepared by the use of a coordination catalyst, such as a Ziegler or Phillips catalyst, are generally known as linear polymers because of the substantial absence of branch chains of polymerized monomer units pendant from the backbone.
High density polyethylene (HDPE), generally having a dens'~ty of about 0.941 to about 0.965 glcc, is typically a homopolymer of ethylene, and it contains relatively few branch chains relative to the various linear copolymers of ethylene and an a-olefin.
HDPE is well known, commercially available in various grades, and may be used in this invention.
Linear copolymers of ethylene and at least one a-olefin of 3 to 12 carbon atoms, preferably of 4 to 8 carbon atoms, are also well known and commercially available. As is well known in the art, the density of s linear ethylenela-olefin copolymer is a function of both the length of the a-olefin and the amount of such monomer in the copolymer relative to the amount of ethylene, the greater the length of the a-olefin and the greater the amount of a-olefin present, the lower the density of the copolymer. Linear low density polyethylene (Lt_DPE) is typically a.copolymer of ethylene and an a-olefin of 3 to 12 carbon atoms, preferably 4 to 8 carbon atoms (for example, 1-butane, 1-octane, etc.), that has sufficient a-olefin content to reduce the density of the copolymer to that of LDPE. When the copolymer contains even more a-olefin, the density will drop below about 0.91 glcc and these copolymers are known as ultra low density polyethylene (ULDPE) or very low density polyethylene (VLDPE).
The densities of these linear polymers generally range from about 0.87 to 0.91 gfcc.
2o Both the materials made by the free radical catalysts and by the coordination catalysts are well known in the art, as are their methods of preparation.
Heterogeneous linear ethylene polymers are available from The Dow Chemical Company as Dowlex'"' LLDPE and as Attane'r'~" ULDPE resins. Heterogeneous linear ethylene polymers can be prepared via the solution, slurry or gas phase zs polymerization of ethylene and one or more optional a-olefin comonomers in the presence of a Ziegler Natta catalyst, by processes such as are disclosed in U.S. Patent No. 4,076,698 to Anderson et al. Preferably, heterogeneous ethylene polymers are typically characterized as having molecular weight distributions, Mr~M," in the range of from 3.5 to 4,1.
Relevant 3o discussions of both of these classes of materials, and their methods of preparation are found in U.S. Patent No_ 4,950,541 and the patents to which it refers.

Ethylene Interpolymers The ethylene polymers useful as components (A), (B), and (C) can independently be interpolymers of ethylene and at least one a-olefin. Suitable a-olefins are represented by the following formula:
CHZ = CHR
in which R is a hydrocarbyl radical. The comonomers which form a part of ' component (A) may be the same as or different from the comonomers which form parts of polymers (B) and (C) of the inventive mixture and the comonomer which forms a part of component (B) may be the same or different from the comonomers to which form parts of polymers (A) and (C).
R generally has from one to twenty carbon atoms. Suitable a-olefins for use as comonomers in a solution, gas phase or slurry polymerization process or combinations thereof include 1-propylene, 1-butane, 1-isobutylene, 1-pentane, hexene, 4-methyl-1-pentane, 1-heptene and 1-octane, as well as other monomer types such as tetrafluoroethyiene, vinyl benzocyclobutane, 1,4-hexadiene, 1,7-octadiene, and cycloalkenes, for example cyclopentene, cyclohexene, cyclooctene, norbornene (NB), and ethylidene norbornene (ENB)). Preferably, the a-olefin will be 1-butane, 1-pentane, 4-methyl-1-pentane, 1-hexane, 1-heptene, 1-octane, NB or ENB, or mixtures thereof. More preferably, the a-olefin wilt be 1-hexane, 1-heptene, 1-octane, or mixtures thereof. Most preferably, the a-olefin will be 1-octane.
Ethylene/a-olefin/diene terpolymers may also be used as elastomeric polymers in this invention. Suitable a-olefins include the a-olefins described above as suitable for making ethylene a-olefin copolymers. The dienes suitable as monomers for the preparation of such terpolymers are typically non-conjugated dienes having from 6 to 15 carbon atoms. Representative examples of suitable non-conjugated dienes that may be used to prepare the terpolymer include:
a) Straight chain acyclic dienes such as 1,4-hexadiene, 1,5-heptadiene, and 1,6-octadiene;
b) branched chain acyclic dienes such as 5-methyl-1, 4-hexadiene, 3,7-dimethyl-1-6-octadiene, and 3,7-dimethyl-1,7-octadiene;
c) single ring alicyclic dienes such as 4-vinylcyclohexene, 1-allyl-4-isopropylidene cycfohexane, 3-allylcyclopentene, 4-allylcyclohexene, and 1-isopropenyl-4-butenylcyclohexane;

WO 97!26297 PCT/US97/01180 d) mufti-ring alicyciic fused and bridged ring dienes such as dicyclopentadierie; alkenyl, alkylidene, cycloalkenyl and cycloalkylidene norbornenes such as 5-methylene-2-norbornene, 5-- methylene-6-methyl-2-norbornene, 5-methylene-6, 6-dimethyl-2-norbornene, 5-propenyl-2-norbornene, 5-(3-cyclopentenyf)-2-norbornene, 5-ethylidene-2-norbornene, 5-cyclohexyfidene-2-norbornene, etc.
The preferred dienes are selected from the group consisting of 1,4-hexadiene, dicyclopentadiene, 5-ethylidene-2-norbornene, 5-methylene-2-norbornene, 7-methyl-1, 6-octadiene, piperylene, 4-vinylcyclohexene, etc.
The preferred terpolymers for the practice of the invention are terpolymers of ethylene, propylene and a non-conjugated diene (EPDM). Such terpolyrners are commercially available. Ethylene/a-olefin/diene terpolymers are useful when it is desired to make elastomeric polymer blends vulcanizabfe with the well known sulfur i5 compound vulcanization process.
Ultra-Low Molecular Weight Ethylene Polymers Ethylene polymers having an ultra-low molecular weight can also be used as component (A), (B), and/or (C) of this invention. In one embodiment, it is contemplated that one or more of components (A), (B), or (C) may comprise an ultra-low molecular weight ethylene polymer characterized as having a M~ less than 11,000 and an M""/M~ of from 1.5 to 2.5. These ultra-low molecular weight ethylene polymers may have a greater degree of crystallinity than corresponding higher molecular weight materials. In certain instances, the ultra-low molecular weight ethylene polymer preferred for component {A), (B), and/or (C) is an ultra-low molecular weight semicrystalline ethylene/a-olefin interpolymer having a density less than 0.900 g/cc and characterized as having lamella greater than 40 nanometers in length when viewed using electron transmission microscopy.
3o These ultra-low molecular weight ethylene polymers are either homopolymers or interpolymers of ethylene with at least one ethylenicaliy unsaturated monomer, conjugated or nonconjugated diene, polyene, etc.
When these ultra-low molecular weight ethylene polymer are interpoiymers, preferred comonomers include the C3-CZO a-olefins, especially propene, isobutylene, 1-butene, 1-hexene, 4-methyl-1-pentene, and 1-octene. Other preferred monomers include sfyrene, halo- or alkyl substituted styrenes, tetrafluoroethylene, vinylbenzocyclobutane, 1,4-hexadiene, and naphthenics (for example, cyclopentene, cyclohexene and cyclooctene).
In some cases, ultra-low molecular weight ethylene polymers suitable for use in the polymer mixtures of this invention have a M" less than 10,000, and using the process for making the ultra-low molecular weight ethylene polymers described below, useful ethylene polymers having a M" less than 5,000 may be obtained.
However, typically the M" of these polymers will be greater than 2,500.
M~ is related to the viscosity at 350°F (177°C) of the ultra-low molecular weight ethylene polymers. The ultra-low molecular weight ethylene polymers are characterized by a melt viscosity at 350°F (177°C) of less than about 8200, in some cases less than 6000, with melt viscosities less than about Ti00 being Easily attained with the process for making these polymers described below.
IS These ultra-iow molecular weight ethylene polymers are homogeneous and have a narrow molecular weight distribution (M"/M"). For these polymers, the M",!M" is in the range from about 1.5 to about 2.5, in some cases in the range from 1.8 to 2.2. The ultra-low molecular weight polymers have a polymer backbone which is optionally substituted with up to 3 long chain branches per 1000 carbons.
Further, the M" of the ultra-low molecular weight ethylene polymers is related to the melt index (I=). For the ultra-low molecular weight ethylene polymers of the invention, melt index is not measured, but is calculated from viscosity correlations. The ultra-low molecular weight ethylene polymers are characterized by a calculated melt index (I=) at 190 C greater than 1000 dglmin., in some cases greater than 1300 dglmin., with these polymers having calculated melt indices of at least 10,000 dgl min. being easily attained.
The ultra-low molecular weight ethylene polymers will typically have a density of from 0.850 to 0.970 glcc. The density employed is a function of the End use contemplated. For instance, when the polymer is intended as a wax substitute densities greater than 0.910, preferably greater than fl.920, glcc are appropriate. In contrast, when the polymer is intended as the strength-imparting~omponent densities less than 0.900, preferably less than 0.895, glcc are appropriate.
When the ultra-low molecular weight polyriner is an interpofymer of ethylene with an aromatic comonomer, such as styrene, the density will be less than 1.10 glcc.
The ultra-low molecular weight ethylene polymers of the invention are characterized as being non-pourable. That is, the ultra-low molecular weight ethylene polymers of the invention are characterized as having a pour point greater than -30 C as determined by ASTM D-97. Preferably, the pour point of the ultra-low molecular weight ethylene polymers will be greater than room temperature (25 C), and more preferably greater than 50 C.
1o The ultra-low molecular weight ethylene polymers have a crystallinity from percent to 80 percent and thus may be selected according to the preferred density ranges of components (A), (B) and (C).
Homogeneous ultra-low molecular weight ethylene/a-olefin interpolymers may be advantageous in certain applications of this invention, as they lead to a low polymer and formulation viscosity but are characterized by a peak crystallization temperature which is greater than that of corresponding higher molecular weight materials of the same density.
The ultra-low molecular weight ethylene polymers may be obtained by reacting ethylene and at least one ethylenically unsaturated comonomer at a reaction 2o temperature of at least 80 C in the presence of a constrained geometry catalyst. The reactor temperature is typically in the range from 100 C to 250 C, preferably from 100 C to 150 C, with temperatures at the higher end of the range favoring the formation of lower molecular weight polymers.
In conjunction with the reactor temperature, the hydrogen:ethylene molar ratio influences the molecular weight of the polymer, with greater hydrogen levels leading to lower molecular weight polymers. When the desired plymer has an IZ of 1 dg/min., the hydrogen:ethylene molar ratio will typically be in the range from 0.45:1 to 0.7:1.
The upper limit of the hydrogen:ethylene molar ratio is about 2.2-2.5.1.
Generally the polymerization process is carried out with a differential pressure of ethylene of from about 10 to about 1000 psi (70 to 7000 kPa), most preferably from about 40 to about 400 psi (30 to 300 kPa}. The polymerization is generally conducted at a temperature of from 100 to 250 C, preferably from 100 to 150 C, and most preferably from greater than 110 to 140 C.
In general, the ultra-low molecular weight ethylenela-olefins useful in the polymer mixtures of this invention may be polymerized at conditions for Ziegter-Natta or Kaminsky-Sinn type polymerization reactions, that is, reactor pressures ranging from atmospheric to 3500 atmospheres (355 MPa).
Suspension, solution, slung, gas phase, solid state powder polymerization or other process condition may be employed if desired using catalysts such as the constrained geometry catalysts described in U.S. Patent Nos. 5,272,236 and 5,278,272 and further described below. A support, especially silica, alumina, or a polymer (especially poly(tetrafluoroethylene) or a polyolefin) may be employed, and desirably is employed when the catalysts are used in a gas phase polymerization process. The support is preferably employed in an amount to provide a weight ratio of catalyst (based on metal)aupport from 1:100,000 to 1:10, more preferably from ~5 1:50,000 to 1:20, and most preferably ftom 1:10,000 to 1:30. In most polymerization reactions the molar ratio of catalyst:polymerizable compounds employed is from 1fl-'~:1 to 1fl'':1, more preferably from 10'°:1 to 10's:l.
Solution polymerization conditions utilize a solvent for the respective components of the reaction. Preferred solvents include mineral oils and the various 2o hydrocarbons which are liquid at reaction temperatures. Illustrative examples of useful solvents include alkanes such as pentane, iso-pentane, hexane, heptane, octane and nonane, as well as mixtures of alkanes including kerosene and Isopar ET"", available from Exxon Chemicals Inc.; cycloalkanes such as cyclopentane and cyclohexane; and aromatics such as benzene, toluene, xylenes, ethylber~,tene and 25 diethylbenzene.
The solvent is present in an amount sufficient to prevent phase separation in the reactor. As the solvent functions to absorb heat, less solvent leads to a less adiabatic reactor. The solvent:ethylene weight ratio is typically in the range from 2.5:1 to 12:1, beyond which point the catalyst efficiency suffers. The most typical 30 solvent:ethylene weight ratio is in the range from 5:1 to 10:1.

Substantial linear and homogenous ultra-low molecular weight ethylenela-olefin interpolymers useful in the invention may further be made in a slung polymerization process, using the catalysts as described above as supported in an inert support, such as silica. As a practical limitation, slurry polymerizations take place in liquid diiue~ts in which the polymer produd is substantially insoluble.
Preferably, the diluent for slurry polymerization is one or more hydrocarbons with less than 5 carbon atoms. If desired, saturated hydrocarbons such as ethane, propane or butane may be used in whole or_ part as the diluent. Likewise the a-olefin monomer or a mixture of different a-olefin monomers may be used in whole or part as the t0 diluent. Most preferably the diluent comprises in at least major part the a-olefin monomer or monomers to be polymerized.
The polymerization may be carried out as a batchwise or a continuous polymerization process, with continuous polymerization processes being required for the preparation of SLEPs. In a continuous process, ethylene, copolymer and is optionaNy solvent are continuously suppNed to the reaction zone and polymer product is continuously removed therefrom.
The ultra-low molecular weight ethylene polymer may be prepared by the solution, slurry, or gas phase polymerization of ethylene and any desired comonomer(s), using a constrained geometry metal complex as the catalyst. The 2o constrained geometry catalyst is described in more detail later.
EthvteneJUnsaturated Carboxylic Acid. Salt and Esher lnteroolvmers Ethylene/unsatuarated carboxylic acid salt and ester interpolymers may be used as component (A), (8) or (C) in this invention, particularly as component (B).
25 These are interpolymers of ethylene with at Least one comonomer selected from the group consisting of vinyl esters of a saturated carboxylic acid wherein the acid moiety has up to 4 carbon atoms, unsaturated mono- or dicarboxylic acids of 3 to 5 carbon atoms, a salt of the unsaturated acid, esters of the unsaturated aad derived from an alcohol having 1 to B carbon atoms, and mixtures thereof. Terpolymers of ethylene 3o and these comonomers are also suitable. lonomers, which are completely or partially neutralized copolymers of ethylene and the acids described above, are discussed in more detail in U.S. Patent 3,264,272. In addition, terpolymers of ethylene/vinyl acetate/carbon monoxide or ethylene/methyl acrylatelcarbon monoxide containing up to about 15 percent by weight of carbon monoxide can also be employed.
The ethylene to unsaturated carboxylic comonomer weight ratio is preferably from 95:5 to 40:60, more preferably from 90:10 to 45:50, and even more preferably from 85:15 to 60:40.
The melt index of these interpolymers msy range from about 0.1 to about 150, preferably from about 0.3 to about 50, and more preferably from about 0.7 to about dg/min. Physical properties, principally elongation, are known to decline to lower levels when the ethylene copolymer melt index is above about 30 dglmin.
Suitable ethylene/unsaturated carboxylic acid, salt and ester interpolymers include ethylenelvinyl acetate (1_1/A) including, but not limited to, the stabifQed EVA
described in U.S. Patent 5,096,955; ethylene/acrylic acid (EEA) and its ionomers; ethylene/methacrylic acid and its t5 ionomers; ethylenelmethyl acrylate; ethylenelethyl acrylate;
elhylene~sobutyl acrylate; ethylenelnormal butyl acrylate; ethylenelisobutyl acrylatelrnethacrylic acid and its ionomers; ethylenelnormal butyl acrylatelmethacrylic aad and its ionomers;
ethylenefisobutyl acrylatelacrylic acid and its ionomers; ethylenelnormal butyl acrylatelacrylic acid and its ionomers; ethylenelmethyl methacrylate;
ethylene/vinyl 2o acetatelmethacrylic acid and its ionomers; ethylenelvinyl acetatelacrylic acid and its ionomers; ethylenelvinyl acetatelcarbon monoxide; ethylenelmethacrylatelcarbon monoxide; ethyienefnortnal butyl acrylatelcarbon monoxide; ethylenelisobutyl acrylatelcarbon monoxide; ethylenehrinyl acetatelmonoethyl maleate and ethylenelmethyl acrylatelmonoethyl maleate. Particularly suitable copolymers are 25 EVA; EEA; ethylenelmethyl acrylate; ethylenefisobutyl acrylate; and ethylenelmethyl methacrylate copolyers and mixtures thereof. Certain properties, such as tensile elongation, are taught to be improved by certain combinations of these ethylene interpolymers described in U.S. Patent 4,379,190. The procedures for making these ethylene interpolymers are well known in the art and many are commercially available.
Constrained Geometry Catalysts Constrained geometry metal complexes which are suitable for making substantially linear ethylene polymers and ultra-low molecular weight polymers, and methods for their preparation, are disclosed in EP-A-416,815;
EP-A-514,828; as well as US-A-5,470,993, 5,374,696, 5,231,106, 5,055,438, 5,057,475, 5,096,867, 5,064,802, and 5,132,380.
In EP-A-514,828 certain borane derivatives of the foregoing constrained geometry catalysts are disdosed and a method for their preparation taught and claimed. In US A 5,453,410 combinations of cationic constrained geometry catalysts with an atumoxane were disclosed as suitable olefin polymerization catalysts.
Exemplary constrained geometry metal complexes in which titanium is present in the +4 oxidation state include but are not limited to the following: (n t5 butylamido)dimethyl(r!5-tetramethylcyclopentadienyl)silanetitanium (IV) dimethyt; (n-butylam:do)dimethyl(rl5-tetramethylcyclopentadienyl)silanetitanium (IV) dibenzyl; (t-butylamido)dimethyl(tl5-tetramethylcydopentadienyl)silanetitanium (IV) dimethyl; (t-butylamido)dimethyl(~5-teiramethy~yclopentadienyl)silanetitanium (IV) dibenzyl;
(cydododecylamido)dimethyl(~y5-tetramethylcydo-pentadienyt)silanetitanium (IV) 2o dibenzyl; (2,4,6-trimethylanilido)dimethyl(rt5-tetramethykyclopentadienyl)silane-titanium (IV) dibenzyl; (1-adamantylamido)dimethyl(rt5-tetramethyicyclopentadienyl)-sifanetitanium (IV) dibenzyl; (t-butylamido)dimethyl(rl5-tetramethylcyclopentadienyl)-silanetitanium (IV) dimethyl; (t-butyiamido)dimethyl(~5-tetramethylcyclopentadienyl)-silanetitanium (1~ dibentyl; (1-adamantylamido)dimethyl(~5~tetramethykyclopenta-25 dienyl)silanetitanium (IV) dimethyl; (n-butylamido)diisopropoxy(~5-tetramethykyclo-pentadienyl)silanetitanium (IV) dimethyl; (n-butylamido)diisopropoxy(~5-tetramethyl-cyclopentadienyl)silanetitanium (IV) dibenzyl; (cyclododecylamido)-diisopropoxy(rl5-tetramethylcyclopentadienyl)-silanetitanium (IV) dimethyl;
(cyclododecylamitfo)-diisopropoxy(~5-tetramethylcyclopentadienyl)-silanetitanium (IV) dibenxyl;
(2,4,6-30 trimethylanilido)diisopropoxy(~5-tetramethylcyclopentadienyl)silanet~anium (IV) dimethyl; (2,4,6-trimethylanilido)dnsopropoxy(~5-tetramethyfcyclopentadienyl)~
silanetitanium (IV) dibenzyl; (cyclododecylamido)dimathoxy(~5-tetramethyl-cyclopentadienyl)silanetitanium (IV) dimethyl;
(cyclododecylamido)dirnethoxy~rl5-_ tetramethylcyclopentadienyl)silanetitanium (IV) dibenzyl; {1-adamantylamido)diiso-propoxy(rl~-tetramethylcyclopentadienyl)silanetitanium (IV) dimethyl; (1-adamantylamido)diisopropoxy(r~5-tetramethylcycfopentadienyl)silanetitanium (IV) dibenzyl; (n-butylamido)dimethoxy(r15-tetramethylcyclo-pentadienyl)silanetitanium (IV) dimethyl; (n-butylamido)dimethoxy(r15-tetramethylcyclopentadienyl)silanetitanium (IV) dibenzyl; (2,4,6-trimethylanilido)dimethoxy(rl5-tetramethylcyclo-pentadienyl)silanetitanium (IV) dimethyl; (2,4,6-trimethylanilido)dimethoxy(rl~-tetramethylcyclopentadienyl)silane-titanium (IV) dibenzyl; (1-adamantylamido}-dimethoxy(rl5-tetramethylcyclo-pentadienyl)silanetitanium {IV} dimethyl; (1-to adamantylamido)dimethoxy(ri5-tetramethylcyclopentadienyl)silanetitanium (IV) dibenzyi; (n-butylamido)-ethoxymethyl(r15-tetramethylcyclopentadienyl)silanetitanium (IV) dimethyl; (n-butylamido)ethoxymethyl(rlb-tetramethylcyclopentadienyl)silane-titanium (IV) dibenzyl; (cyclododecylamido)ethoxymethyl(r15-tetramethylcyclopenta-dienyi)-silanetitanium (IV) dimethyl; (cyclododecylamido)ethoxymethyl(rl5-tetramethyl-cyclopentadienyl)siianetitanium (IV) dibenzyl; (2,4,6-trimethylanilido)-ethoxymethyl-(rl5-tetramethylcyclopentadienyl}silanetitanium (IV) dimethyl;
(2,4,6-trimethylanilido)ethoxymethyl{r15-tetramethyicycfopentadienyl)silanetitanium (1V}
dibenzyl; (cyclododecylamido)dimethyl{r~~-tetramethylcyclopentadienyl)silane-titanium (IV) dimethyl; (1-adamantylamido)ethoxymethyl(r15-tetramethylcyclopenta-2o dienyl)silanetitanium (IV) dimethyl; and (1-adamantylamido)ethoxymethyl(~5-tetramethylcyclo-pentadienyl)silanetitanium (IV) dibenzyl_ Exemplary constrained geometry metal complexes in which titanium is present in the ~-3 oxidation state include but are not limited to the following: (n-butylamido}dimethyl(rl'-tetramethylcyclopentadienyl)silanetitanium (III) 2-{N,N-dimethylamino)benzyl; (t-butylamido)dimethyf(rl5-tetramethylcyclopentadienyl}-silanetitanium (111} 2-(N,N-dimethylamino)benzyl;
(cyclododecylamido)dimethyl(r15-tetramethylcyclopentadienyl)siianetitanium (ill) 2-(N,N-dimethylamino)benzyl;
(2,4,6-trimethylanilido)dimethyl(r~5-tetramethylcyclopentadienyl)silanetitanium (III) 2-(N,N-dimethylamino)benzyf; (1-adamantylamido)dimethyl(rl5-tetramethylcyclopentadienyl)-3o silanetitanium (111) 2-(N,N-dimethylamino)benzyl; (t-butylamido)dimethyl(rl~-tetramethylcyclopentadienyl)silanetitanium (III) 2-(N,N-dimethylamino)benzyf;
(n-butylamido)diisopropoxy(r15-tetramethylcyclopentadienyl)silanetitanium (III) 2-{N,N-dimethylamino)benzyf; (cyclododecylamido)diisopropoxy(rlb-tetramethylcyclopenta-_ dienyl)silanetitanium (lll} 2-(N,N-dimethylamino)benzyl; (2,4,6-trimethylanilido)-diisopropoxy{rl5-2-methylin-deriyl)silanetitanium {III) 2-(N,N-dimethylamino)benzyl;
(1-adamantyfamido)diisopropoxy(rl5-tetramethylcyclopentadienyl)silanetitanium (iii) 2-(N,N-dimethylamino)benzyl; (n-butylamfdo)dimethoxy(rl5-tetramethylcyclopenta-dienyl)silanetitanium (III) 2-(N,N-dimethylamino)benzyl; (cyclododecylamfdo)-dimethoxy(rl5-tetramethylcyclopentadienyl)silanetitanium (Ill) 2-(N,N-dimethylamino}benzyl; (1-adamantylamido)dimethoxy(rl~-tetramethylcyclopenta-dienyl)silanetitanium (III} 2-(N,N-dimethylamino)benzyl; (2,4,6-trimethylanilido)-dimethoxy(rl5-tetramethylcyclopentadienyl)silanetitanium (Ill) 2-(N,N-dfmethylamino)-1o benzyl; (n-butylamido}ethoxymethyl(rl'-tetramethylcyclopentadienyl}silanetitanium (III} 2-(N,N-dimethylamino)benzyl; (cyclododecylamido}ethoxymethyl(rlb-tetramethylcyclopentadienyf}silanetitanium (III) 2-(N,N-dimethylamino)benzyl;
(2,4,6-trimethyfanilido}ethoxymethyl(r15-tetramethylcyclopentadienyl)silanetitanium (Ill) 2-(N,N-dimethylamino)benzyl; and (1-adamantylamido)ethoxymethyl(115-tetramethyl-cyclopentadienyl)silanetitanium {III) 2-(N,N-dimethylamino)benzyl.
Exemplary constrained geometry metal complexes in which titanium is present in the +2 oxidation state include but are not limited to the following: (n-butylamido)dimethyl-(rl5-tetramethylcyclopentadienyl)sifanetitanium (II) 1,4-diphenyl-1,3-butadiene; (n-butylamido)dimethy!{rl5-tetramethylcyclopentadienyl)silanetitanium {II} 1,3-pentadiene; (t-butylamido)dimethyl(rl~-tetramethyfcyclopentadienyl}sffane-titanium (II) 1,4-diphenyl-1,3-butadiene; (t-butylamido)dimethyl(~5-tetramethyl-cyclopentadienyl)siianetitanium (II) 1,3-pentadiene;
(cyclododecylamido)dimethyl(rl~-tetramethylcyclopentadienyl)silanetitanfum (II) 1,4-diphenyl-1,3-butadiene;
(cyclododecylamido)dimethyl(rl~-tetramethylcyclopentadienyl)silanetitanium (fl) 1,3-pentadiene; (2,4,&-trimethylanilido)dimethyl(rl~-tetramethyicyclopentadienyl)-silanetitanium (II) 1,4-diphenyl-1,3-butadiene; (2,4,6-trimethylanilido)dimethyl{rl5-tetramethylcyclopentadienyl)silanetitanium (fl) 1,3-pentadiene; (2,4,6-trimethyl-anifido)dimethyl(rl5-tetramethylcyclopentadienyl)silanetitanium (IV) dimethyl;
(1-adamantylamido)dimethyl(rl5-tetramethylcyclopentadienyl)silane-titanium (ll) 1,4-diphenyl-1,3-butadiene; (1-adamantylamido)dimethyl(rl5-tetramethylcycfopenta-dfenyl)silanetitanium (II) 1,3-pentadiene; (t-butylamido)-dimethyl(rlb-tetramethylcyclo-pentadienyl)silanetitanium (11) 1,4-Biphenyl-1,3-butadiene; (t-butylamido)dimethyl(~~-tetramethylcyclopentadienyl}silanetitanium (Il) 1,3-pentadiene; ; (n-butylamido)diisopropoxy{rl5-tetramethylcycfopentadienyl}-silanetitanium (II}
1,4-diphenyl-1,3-butadiene; (n-butylamido)diisopropoxy(rlb-tetramethylcyclopentadienyl)-silanetitanium (II) 1,3-pentadiene; (cyclododecylamido)-diisopropoxy(rl5-tetramethylcyclopentadienyl}silanetitanium (II) 1,4-Biphenyl-1,3-butadiene;
(cyclo-Bodecylamido)diisopropoxy(rl5-tetramethylcyclopentadienyl)-silanetitanium (II) 1,3-pentadiene; (2,4,6-trimethylanilido)diisopropoxy(rl5-2-methyl-indenyl)silanetitanium ((l) 1,4-Biphenyl-1,3-butadiene; (2,4,6-trimethylanifido)-diisopropoxy(~5-tetramethyl-cyclopentadienyl)silanetitanium (II) 1,3-pentadiene; (1-adamantylamido)diiso-propoxy(rl~-tetramethyicyclopentadienyl)silanetitanium (ll) 1,4-Biphenyl-1,3-1o butadiene; (1-adamantylamido)diisopropoxy(rl~-tetramethyl-cyclopentadienyl)silane-titanium (II) 1,3-pentadiene; (n-butylamido)dimethoxy{r15-tetramethylcyclopenta-dienyl)silanetitanium (II) 1,4-Biphenyl-1,3-butadiene; (n-butylamido)dimethoxy(r15-tetramethyfcyclopentadienyl)silanetitanium (II) 1,3-pentadiene;
(cyclododecyiamido)-dimethoxy(r15-tetramethylcyclopentadienyl)-silanetitanium (II) 1,4-Biphenyl-1,3-butadiene; {cyclododecylamido)dimethoxy(rl~-tetramethylcyciopentadienyl)silane titanium (II) 1,3-pentadiene; (2,4,6-trimethylanilido)dimethoxy(r15-tetramethyl cyclopentadienyl)silanetitanium (II) 1,4-Biphenyl-1,3-butadiene; (2,4,6-trimethyl-anilido)dimethoxy(~~-tetramethylcyclopentadienyl)sifanetitanium (II) 1,3-pentadiene;
(1-adamantyl-amido}dimethoxy(r15-tetramethylcyclopentadienyl}siianetitanium {II}
2o 1,4-Biphenyl-1,3-butadiene; (1-adamantylamido)dimethoxy(r15-tetramethylcyclopenta-dienyl)silanetitanium (II) 1,3-pentadiene; (n-butylamido)ethoxymethyl{rl5-tetramethylcyclopentadienyl)silanetitanium {I I) 1,4-Biphenyl-1,3-butadiene;
(n-butylamido}ethoxymethyl(rl~-tetramethylcyclopentadienyl)silanetitanium (II) 1,3-pentadiene; (cycfododecylamido)ethoxymethyf(rl5-tetramethylcyclopentadienyl)-silanetitanium (II) 1,4-Biphenyl-1,3-butadiene;
(cyclododecylamido)ethoxymethyl(rl5-tetramethylcyclopentadienyl)silanetitanium (II) 1,3-pentadiene; {2,4,6-trimethyl-anilido)ethoxymethyl(~5-tetramethylcyclopentadienyl)siianetitanium (It) 1,4-diphenyl-1,3-butadiene; (2,4,6-trimethylanilido)ethoxymethyl(rl5-tetramethylcyciopentadienyl)-silanetitanium {ll) 1,3-pentadiene; (1-adamantylamido)ethoxymethyl(rt5-tetramethyl-3o cyclopentadienyl)silanetitanium (II) 1,4-Biphenyl-1,3-butadiene; and (1-adamantyl-amido)ethoxymethyl(rl5-tetramethylcyclopentadienyl)silanetitanium (II) 1,3-penta-diene.

The complexes can be prepared by use of well known synthetic techniques.
The reactions are conducted in a suitable noniMerfering solvent at a temperature from -100 to 300 C, preferably from -78 to 100 C, most preferably from 0 to 50 C. A
redudng agent may be used to cause the metal M, to be reduced from a higher to a lower oxidation state. Examples of su'ttable redudng agents are alkali metals, alkaline earth metals, aluminum and zinc, alloys of alkali metals or alkaline earth metals such as sodiumlmercury amalgam and sodium/potassium alloy, sodium naphthalenide, potassium graphite, lithium alkyls, lithium or potassium alkadienyls, and Grignard reagents.
Suitable reaction media for the formation of the complexes include aliphatic and aromatic hydrocarbons, ethers, and cydic ethers, particularly branched-chain hydrocarbons such as isobutane, butane, pentane, hexane, heptane, octane, and mixtures thereof; cyclic and alicydic hydrocarbons such as cyclohexane, cydo-heptane, methylcydohexane, methylcydoheptane, and mixtures thereof; aromatic and hydrocarbyl-substituted aromatic compounds such as benzene, toluene, and xylene, C1~ dialkyl ethers, C1~ dialkyl ether derivatives of (poly)alkytene glycots, and tetrahydrofuran. Mixtures of the foregoing are also suitable.
Suitable activating cocatalysts~and activating techniques have been previously taught with respect to different metal complexes in the following references:
EP-A-277,003, US-A-5,153,157, US-A-5,064,802, EP-A-468,651, EP-A-520,732 and EP-A-520,732.
Suitable activating cocatalysts for use herein include perfluorinated tri(aryl)boron compounds, and most especially tris(pentafluoro-phenyl)borane;
nonpolymeric, compatible, noncoordinating, ion forming compounds (including the use of such compounds under oxidizing conditions), especially the use of ammonium-phosphonium-, oxonium-, carbonium-, silylium- or sulfonium- salts of compatible, noncoordinating anions, and ferrocenium salts of compatible, noncoordinating anions.
Suitable activating techniques include the use of bulk electrolysis. A
combination of the foregoing activating cocatalysts and techniques may be employed as well.
Illustrative, but not limiting, examples of boron compounds which may be used as an activating cocatalyst in the preparation of the improved catalysts of this invention are tri-substituted ammonium salts such as trimetilylammonium tetrakis(pentafluorophenyl) borate, triethylammonium tetrakis(pentafluorophenyf) borate, tripropylamrnonium tetrakis(pentafluorophenyl) borate,tri(n-butyl)ammonium tetrakis(pentaffuorophenyl) borate, tri(sec-butyl)ammonium tetrakis(pentafluoro-phenyl) borate, N,N-dimethylanilinium tetrakis(pentafluorophenyl) borate, N,N-dimethylanilinium n-butyltris(pentafluorophenyl) borate, N,N-dimethylanilinium benzyltris(pentafluorophenyl) borate, N,N-dimethylanilinium tetrakis(4-(t-butyldimethylsilyl}-2, 3, 5, 6-tetrafiuorophenyl) borate, N,N-dimethylanilinium tetrakis(4-(triisopropylsilyl)-2, 3, 5, 6-tetrafluorophenyl) borate, N,N-dimethylanilinium to pentafluorophenoxytris(pentafluorophenyf} borate, N,Ndiethylanilinium tetrakis(penta-fluorophenyl) borate, N,N-dimethyl-2,4,6-trimethylanilinium tetrakis-(pentafluorophenyl) borate, trimethylammonium tetrakis(2,3,4,6-tetrafluorophenyl)-borate, triethylammonium tetrakis(2,3,4,6-tetrafluorophenyl) borate, tripropyl-ammonium tetrakis(2,3,4,6-tetrafluorophenyl) borate, tri(n-butyl)ammonium tetrakis(2,3,4,6-tetrafiuorophenyl) borate, dimethyl(t-butyl)ammonium tetrakis(2,3,4,6-tetrafluorophenyl) borate, N,N-dimethylanilinium tetrakis(2,3,4,6-tetrafluorophenyl) borate, N,N-diethyianilinium tetrakis(2,3,4,6-tetrafluorophenyl) borate, and N,N-dimethyl-2,4,6-trimethylanilinium tetrakis(2,3,4,6-tetrafluorophenyl) borate;
disubstituted ammonium salts such as di-(i-propyl)ammonium tetrakis(pentafluoro-2o phenyl) borate, and dicyclohexylammonium tetrakis(pentafluorophenyl) borate;
trisubstituted phosphonium salts such as triphenylphosphonium tetrakis(pentafluoro-phenyl) borate, trio-tolyl)phosphonium tetrakis(pentafluorophenyl) borate, and tri(2,6-dimethylphenyf)phosphonium tetrakis(pentafluorophenyl) borate;
disubstituted oxonium salts such as diphenyloxonium tetrakis(pentafluorophenyl) borate, di(o-tolyl)oxonium tetrakis(pentafluorophenyl) borate, and di(2,6-dimethyl-phenyl)oxonium tetrakis(pentafluorophenyl) borate; disubstituted sulfonium salts such as diphenylsulfonium tetrakis(pentafluorophenyl} borate, di(o-tolyl)sulfonium tetrakis(pentafluorophenyl) borate, and bis(2,6-dimethylphenyl)sulfonium tetrakis-(pentafluorophenyl) borate.
3o A most preferred activating cocatalyst is trispentafluorophenylborane.
Alumoxanes, especially methylalumoxane or triisobutylaluminum modified methylalumoxane are also suitable activators and may be used for activating these metal complexes.

The molar ratio of metal complex: activating cocatalyst employed preferably ranges from 1:1000 to 2:1, more preferably ftom 1:5 to 1.5:1, most preferably from 1:2 to 1:1. In the preferred case in which a metal complex is activated by trispenta-fluorophenylborane and triisobutylaiuminum modified methylalumoxane, the titanium:boron:aluminum molar ratio is typically from 1:10:50 to 1:.05:0.1, most typically from about 1:3:5.
At all times, the individual ingredients as well as the recovered catalyst components must be protected from oxygen and moisture. Therefore, the catalyst components and catalysts must be prepared and recovered in an oxygen and t0 moisture free atmosphere. Preferably, therefore, the reactions are performed in the presence of an dry, inert gas such as, for example, n'ttrogen.
The catalysts may be utilized in combination with at least one additional homogeneous or heterogeneous polymerizat'ron catalyst in separate reactors connected in series or in parallel to prepare the polymer blends according to the is present invention. An example of such a process is disclosed in WO 94/00500 and U.S. Patent No. 5,844,045.
These catalyst compositions may be prepared as a homogeneous catalyst by 20 addition of the requisite components to a solvent in which polymerization wdl be carried out by solution polymerization procedures. The catalyst system may also be prepared and employed as a heterogeneous catalyst by adsorbing the requisite components on a catalyst support material such as silica gel, alumina or other suitable inorganic support material. When prepared in heterogeneous or supported 25 form, it is preferred to use silica as the support material. The heterogeneous form of the catalyst system is employed in a slurry polymerization. As a practical limitation, slurry polymerization takes place in liquid difuents in which the polymer product is substantially insoluble. Preferably, the diluent for slurry polymerization is one or more hydrocarbons with less than 5 carbon atoms. If desired, saturated hydrocarbons 30 such as ethane, propane or butane may be used in whole or part as the diluent.
Likewise the a-olefin monomer or a mixture of different a-olefin monomers may be used in whole or part as the diluent. Most preferably the diluent comprises in at least major part the a-olefin monomer or monomers to be polymerized.

WO 97/26297 PCTlUS97/01180 Preferred Ranges The polymer mixtures of the present invention will preferably have a crystallinity of at least 6 percent, more preferably at least 15 percent, preferabiy up to 50 percent, more preferably up to 30 percent, more preferably up to 21.5 percent, and even more preferably up to 18 percent.
For the inventive polymer mixture, the difference between the crystallinities of component (A) and component (B) is generally at least 7 percent, preferably at least 14 percent, more preferably at least 18 percent. The difference between the 1o crystallinity of any one of components (A), (B}, and (C) and the crystallinity of the component (A), (B), or (C) closest in crystallinity is preferably not greater than 60 percent, more preferably not greater than 50 percent, even more preferably not greater than 40 percent, even more preferably not greater than 30 percent.
in a preferred embodiment of this invention, the number average molecular 15 weight of component (B}, M~2, is greater than or equal to the number average molecular weight of component (A), M~,. In a particularly preferred embodiment, Mn2 exceeds M"~ by 10 percent preferably by 20 percent, more preferably 50 percent.
These blends generally have improved properties relative to polymer mixtures that do not fulfill this further requirement, such as higher softening point under load and lower 20 compression set.
The weight ratio of component (A) to component {B) in the polymer mixture is preferably at least 30:70, more preferably greater than 60:40 and even more preferably at feast 65:35, up to about 95:5, more preferably up to about 90:10. The combined weight of component (A) and component {B) in the polymer mixture is 25 preferably at least 60 wt percent, more preferably at least 75 wt percent, even more preferably at least 90 wt percent and even more preferably at feast 95 wt percent, either based on the combined weight of the polymers in the polymer mixture or in some instances based on the total weight of the polymer mixture (the "total weight"
including other components such as nonpolymer adjuvants and difuents as opposed 30 to the "combined weight" which here includes just the polymer components).
Component (C) may optionally be present in an amount greater than zero, preferably at Feast 5 wt percent, more preferably at least 10 wt percent, up to about 40 wt percent, preferably up to about 25 wt percent, either based on the total weight of the mixture of polymers (A), {B) and (C) or based on the total weight of the polymer mixture (the "total weight" including other components such as nonpolymer adjuvants and diluents as opposed to the "combined weight" which here includes just the polymer components).
Component (A) and component (B) preferably each independently have a MI
in the range from 0.01, preferably from 0.05, up to 5000 dg/ min. Component tC) preferably has a MI of at least about 0.05 up to 5000, more preferably up to 200, dglmin. The MI of component (A) is preferably greater than or equal to the Ml of component (B), more preferably greater than that of component (B).
The MI of the polymer mixture of the invention is preferably at least 0.05, more preferably 0.5, preferably up to 100 dglmin.
Preferably, component (A) has a MWD (M""IM") of at least 1.6, more preferably at least 1.8, up to about 3.2, more preferably up to about 2.7, and even more preferably up to abort 2.2 and components (B) and (aC) have MWDs greater than or equal to 1.6, more preferably at least 1.8, up to about 40, more preferably up to about 32. The MWD of the overall mixture is not greater than 3 when the overall crystallinity is greater than or equal to 21.5 percent.
The blends according to this invention usually, but not always, have at least two DSC melting peaks.
3. Methods of Makino and Usino Another aspect of the present invention is a process for fabricating the polymer mixture of the invention into the form of a film, film layer, coating or molded article. The process can include a lamination and coextrusion technique or combinations thereof, or using the polymer mixture alone, and includes a blown film, cast film, extrusion coating, injection molding, blow molding, compression molding, rotomolding, or injection blow molding operation or combinations thereof.
The polymer mixture of the invention can be formed by any convenient method. Preparing the present compositions by physical admixture includes dry blending, melt blending and solution blending, that is dissolving one or both of the components in a suitable solvent, such as for example a hydrocarbon, and combining the components followed by removing the solvent or solvents. Dry blending involves blending the individual components in solid particulate and subsequently melt mixing in a mixer or by mixing the components together directly in a mixer (for.example, a Banbury mixer, a Haake mixer, a Brabender internal mixer, or a single or twin screw extruder inGuding a compounding extruder and a side-arm extruder employed directly downstream of a interpolymerization process.
The mixtures of the invention can further be formed in-situ via the interpolymerization of ethylene and the desired a-olefin using a constrained geometry catalyst in at least one reactor and a constrained geometrycatalyst or a Ziegler-type catalyst in at least one other reactor. The reactors can be operated sequentially or in parallel. An exemplary in-situ interpolymerization process is disclosed in WO 94/17112.
Preferably, the resent compositions are prepared using two reactors ~0 operated in series or in parallel, or by in-reactor blending using two or more catalysts in a single reactor or combinations of multiple catalysts and muHiple reactors. The general principle of making polymer blends by in-reactor blending using two or more catalysts in a single reactor or combinations of multiple catalysts and multiple reactors is described in WO 93/13143, EP-A~19827, and USP 3,914,362.
The present polyolefin compositions can be prepared by selecting appropriate catalyst and process conditions with a view to the final composition characteristics.
The polymer mixture of the invention can further be formed by isolating component (A) from a heterogeneous ethylene polymer by fractionating the heterogeneous ethylene polymer into specific polymer fractions with each fraction having a narrow branching distribution, selecting the fractions appropriate to meet the limitations specified for component (A), and blending the selected fraction in the appropriate amounts with a component (B). This method is obviously not as economical as the in-situ polymerization described above, but can nonetheless be used to obtain the polymer mixture of the invention.
Additives, such as antioxidants (for example, hindered phenolics, such as Irganox'"" 1010 or IrganoxTM 107fi supplied by Ciba Geigy and phosphates (for example, Irgafos'"" 168 also supplied by Ciba Geigy, Sandostab PEPQ'""
suppl'~ed by Sandoz)), cling additives (for example, PIB), tacki~ers, plasticizers, oils, peroxides (such as for wire and cable coating applications), pigments, colorants and fillers may also be inGuded in the polymer mixture of the present invention or in films formed from the same. Although generally not required, films, Coatings and moldings formed from the polymer mixture of the present invention may also contain additives to enhance antiblocking, mold release and coefficient of friction characteristics including, but not limited to, untreated and treated silicon dioxide, talc, calcium carbonate, and clay, as well as primary, secondary and substituted fatty acid amides, release agents, silicone coatings, etc. Still other additives, such as quaternary ammonium compounds alone or in combination with ethylene-acrylic acid (EAA) copolymers or other functional polymers, may also be added to enhance the antistatic characteristics of films, coatings and moldings formed from the polymer mixture of the invention and permit the use of these polymer mixtures in, for example, the heavy-duty packaging of electronically sensitive goods.
In a preferred embodiment, this invention relates to multi-component blends of l0 the following material: (1 ) polyolefin elastomers, single metallocene-based polymers, narrow comonomer composition and narrow molecular weight polymers, with (2) polyolefin plastomers, styrenic block copolymers, conventional LLDPE, HDPE, LDPE, and (3) petroleum-based oils {naphthenic and paraffinic oils). The finished products display lower hardness, yet have enhanced elevated temperature performance 15 compared to a single resin plus oil composition at the same melt index and density of the polymer phase. The polymer blend plus oil can include filters such as clay, calcium carbonate and talc, for example, to aid in lowering the cost of the composite and enhance the mechanical properties without Toss of the observed advantages of the blends.
2o The polymer mixture of this invention may further include recycled and scrap materials and difuent polymers (both encompassed by the expression "diluent materials"), to the extent that the desired performance properties are maintained.
Exemplary diluent materials include, for example, elastomers, rubbers and anhydride modified polyethylenes (for example, polybutylene and malefic anhydride grafted 25 LLDPE and HDPE) as well as with high pressure polyethylenes such as, for example, low density polyethylene (LDPE), EAA interpolymers, ethylene/vinyl acetate (EVA) interpolymers and ethylene/methacrylate (EMA) interpolymers, and combinations thereof. In some instances, it is preferable for the polymer mixture of this invention to contain less than 50 wt percent, more preferably less than 30 wt percent and even 30 more preferably less than 10 wt percent, diluent material, particularly when the diluent material is a styrene copolymer, more particularly when the diluent material is a styrene/butadiene rubber and even more particularly when the diluent material is a styrene/butadiene/styrene block copolymer (SBS).

Processes for making a molded article by injection molding comprise: .(A) heating a polymer mixture according to this invention to a temperature suitable for injection molding; (B) injecting the polymer mixture of step (A) into a mold to form the molded article; (C) cooling the polymer mixture of step (B); and (D) removing from the mold the molded article formed..in steps (B) and (C). This process may optionally include (E) crosslinking the polymer mixture.
Many ethylene polymers, including the preferred SLEPs, require significant cooling periods before they can be removed from the mold into which they were injec#ed at an elevated temperature. This causes a delay between injection into the to mold and removal of the molded article from the moki for each injection.
This results in prolonged cycle times between injections, which translates to tower productivity fw a given investment in injection molding equipment. There is thus a strong desire in the polymer intJustry to reduce this delay in cycle time. An important and unexpected advantage of this invention is that it reduces cooling time, and hence decreases cycle time, for a given crystallinity and melt index.
In a preferred embodiment of this aspect of the invention, the cooling time, and hence the cycle time, is less, preferably 20 percent less, more preferably b0 percent less, than the cooling time measured the same way under the same conditions (that is, same equipment, same starting and ending temperatuFes, same 2o degree of cooling after injection, etc.) for a single ethylene~olymer made oft-he same monomers as component (A), but having the same crystallinity and melt index as the polymer mixt~.-e in question. The cooling time of the polymer mixture may also be less, preferably 20 percent less, more preferably 50 percent less, than the cooling time predicted by the rule of mixtures, yielding a corresponding improvEment in cycle time.
The polymer mixtures of this invention can be shaped into a final shape and then crosslinked with known crosslinking agents to form vukanaed elastomeric products. The expression "vulcanized eiastomeric~products" as used herein means products having a crosslinking density of at least 5 percent gel as measured via ASTM D2765, Procedure A. Crosslinking agents include peroxide, sulfur, epoxy and other known heat-activated curing agents and electron beam, gamma-ray and other known radiation-activated cure systems.
If the crosslinking agent is a heat-activated substance, forexamp~e a,peroxide, sulfur, etc., then this agent is included in the polymer mixture of the present invention prior to the heating step (A) of the process of this invention. If the crosslinking agent is a radiation source, for example electron beam, then obviously the agent is not present until after fomning the molded article according to step (8) of this invention. Suitor as a crosslinking agent is used only with those olefinic polymers capable of being crosstinked with sulfur, for example those containing dime functionality, such es ethylenelpropyleneldiene terpolymer (EPDM). The various crosslinking agents can be used alone or in combination with one another. One embodiment in which more than one curing agent may be used is that in which a peroxide is included in the polymer mixture of step (A) as the free radical initiator to effect the grafting of the crflsslinker to tt~e ethylene polymer. In this embodiment, excess or residual peroxide from the grafting may be available for initiating crosslinking along with another crosslinking agent, for example an epoxy, electron beam, etc.
Suitable heat-activated crosslinking agents inGude free radical initiators, preferably organic peroxides, more preferably those with one hour half lives at is temperatures greater than 120 C. Examples of useful organic peroxides include 1,1~
di-t-butyl peroxy-3,3.'5-trimethylcyctohexane, dicumyl peroxide, 2,5-dimethyl-2;5-di(t-butyl peroxy) hexane. t-butyl-cumyi peroxide, di-t-butyl peroxide, and 2,5-dimethyl-2,5-di-(t-butyl peroxy) hexyne. flicumyl peroxide is a preferred agent.
Additional teachings regarding organic peroxide crosslinking agents are available in the 30 Handbook of Polymer Foams and Technology, pp. 188-204, Edited by D.
Klempner and K.C. Frisch, Hanser Publishers, Munich, Vienna. New York. Barcelona (t991).
coagents, that is promotors or co-initiators, include multifunctional vinyl monome's and polymers, iriallyl cyanurate and trimethylolpropane trimethacrylate, divinyl :5 benzene, acrylates and methacrylates of polyols, aHyl ak;ohol derivatives, and low molecular weight polybutadiene.
4. Formed Article Properties and Uses At temperatures above room temperature, the articles made from the 30 polymer mixtures according to the present invention exhibit improved properties both relative to a single ethylene polymer of equal crystallinity and substantially the same melt index (~ 20 percent) , and improvements greater than would be expected for the polymer mixtures under the rule of mixtures. Improved properties include higher softening point under toad and improved hardness, toughness.la0 percent modulus _ of elasticity, and compression set, particularly at temperatures greater than room temperature (that is, 25 C) such as temperatures in excess of 50 or 60 C.
These improved properties are achieved without requiring crosslinking of these polymer mixtures. Although these polymer mixtures may be crosslinked, they have utility and certain advantages without crosslinking. Advantages of the non-crosslinked products include ease of processing, flexibility in manufacturing methods, and recyclabifity of the polymer.
However, further improvements in these properties may be obtained through crosslinking the polymer mixtures of this invention beyond the gel point. As used herein, "crosslinking" and "crosslinked" include partially crossfinking (crossiinked) as well as fully crosslinking (crossiinked), as long as the crosslinking results in a gel which is verifiable via ASTM D2765, Procedure A. In some preferred embodiments, these polymer mixtures have a crosslinking density of at least 20 percent, more preferably at least 50 percent and even more preferably at least 80 percent, as is measured via ASTM D2765, Procedure A.
The preferred polymer mixtures according to the present invention have a softening point under load (defined above) greater than that which would be predicted based on the softening point under load, of a similar polymer of the same crystallinity and substantially the same MI (~ 20 percent) or, more preferably, greater than the 2o softening point under load predicted by the rule of mixtures based on the softening point under load of the individual polymer components of the mixture weight averaged together based on the relative wt percent amounts of each of those components in the mixture. Blends A through F according to this invention are shown to fulfill the first of these preferred embodiments in FIGURES 1 and 2 and blend A is 25 also shown to fulfill the second of these preferred embodiments as shown in FIGURE
3.
Preferably, the polymer mixtures according to the present invention have a softening temperature under load (1 N applied with a flat tip probe having a diameter of 1 mm) of at least 3 C, more preferably 5 C, even more preferably at least 10 C, 30 greater than the softening point predicted by the rule of mixtures. In one preferred embodiment, the polymer mixtures according to this invention have a softening point under load of at least 75 C, more preferably at least 80 C. FIGURE 2 shows a polymer mixture according to the present invention having a softening point under load more than 10 C greater than the softening point predicted by the rule of mixtures.
One measure of improved elevated temprature hardness is an increase in temperature for a given Shore A hardness. Preferred polymer mixtures according to the present invention have a Shore A hardness of 45 at a temperature higher than the temperature of a similar polymer of the same crystallinity at a Shore A
hardness of 45, and preferably higher than the temperature predicted based on the rule of mixtures. More preferably, the polymer mixtures according to the present invention have a temperature at Shore A hardness of 45 at least 3 C, preferably at least 5 C, to even more preferably at least 10 C, greater than the temperature at Share A
hardness of 45 for a similar polymer having the same crystallinity or the temperature predicted by the rule of mixtures. The former is illustrated by FIGURES 4 and 5, which show that blends A, G and H according to the present invention exhibit a Shore A hardness of 45 at a temperature higher than that of a polymer of the same density.
1s The 100 percent modulus (stress at 100 percent elongation) is also improved with mixtures according to the present invention, particularly at elevated temperatures. This improvement may also be measured relative to a similar polymer of the same crystallinity or preferably relative to the 100 percent modulus predicted by the rule of mixtures. When the 100 percent modulus for the polymer mixture 20 produced according to the present invention is measured at 60 C, a measurable improvement is obtained. The improvement is preferably at least by a factor of 1.5, more preferably at least a factor of 2, even more preferably at least by a factor of 4, relative to a similar polymer having the same crystallinity, preferably relative to the 100 percent modulus predicted under the rule of mixtures.
2s in a preferred embodiment, the 100 percent modulus of elasticity at 60 C is at least 120 psi, more preferably at least 140 psi.
At 60 C, toughness is also improved, preferably by the same factors and amounts as for 100 percent modulus.
Compression set (ASTM D395-85) 3o is also improved at elevated temperatures. At 70 C, compression set is improved by preferably at least 5 percent, more preferably by at least 10 percent, relative to a similar polymer having the same crystallinity, preferably relative to the compression set predicted by the rule of mixtures.

- In a preferred embodiment, the polymer mixtures of this invention have a compression set less than 90 percent more preferably less than 80 percent, at 70C.
Further improvement may be obtained by selecting component (A) having a lower Mn than the M~ of component (B). This is illustrated by FIGURE 6, which shows that a blend of a low crystallinity substantially linear ethylene 1-octene copolymer (SLEP 9) with a higher crystallinity substantially linear ethylene 1-octene copolymer (SLEP 6) ' having a lower melt index (that is, higher M~) has a lower compression set than a blend of substantially linear ethylene 1-octene copolymers in which the M"
relationship in the blend is reversed (SLEP 1/SLEP 10).
to Many useful fabricated articles benefit from the polymer mixtures disclosed herein. The polymer mixture of this invention may find utility in a variety of applications including, but not limited to adhesives, molded goods, profile extrusion parts, foams, fibers, films, sporting goods such as swimming fins, etc., elastic bands and elastic fibers such as for making disposable diapers, etc., shoe soles such as z5 foamed shoe soles, latex footwear, weather strips, gaskets, etc. For example, molding operations can be used to form useful fabricated articles or parts from the compositions disclosed herein, including various injection molding processes (for example, that described in Modern Plastics Encyclopedia/89, Mid October 1988 Issue, Voiume 65, Number 11, pp. 264-268, "Introduction to Injection Molding:
by H.
2o Randall Parker and on pp. 270-271, "injection Molding Thermoplastics" by Michael W. Green) and blow molding processes (for example, that described in Modern Plastics Encylcopedia/89, Mid October 1988 Issue, Volume 65, Number 11, pp.

218, "Extrusion-Blow Molding" by Christopher Irwin), profile extrusion, calandaring, and pultrusion (for example, pipes). Rotomolded articles can also benefit from the 25 novel compostions described herein. Rotomolding techniques are well know to those skilled in the art and include, for example, those described in Modern Plastics Encyclopedia/89, Mid October 1988 Issue, Volume 65, Number 11, pp. 296-301, "Rotational Molding" by R.L. Fair.
Fibers (for example, staple fibers, melt blown fibers or spunbonded fibers) 30 using, for example, systems as disclosed in U.S. Patent No. 4,340,563, U.S.
Patent No. 4,663,220, U.S. Patent No. 4,668,566, or U.S. Patent No. 4,322,027, and get spun fibers (for example, the system disclosed in U.S. Patent No. 4,413,110), both woven and nonwoven fabrics (for example, spunlaced fabrics disclosed in U.S.
Patent No. 3,485,706) or structures made from such fibers (including, for example, blends of these fibers with other fibers, for example, PET or cotton)) can also be made from the novel compositions disclosed herein.
Film and film structures particularly benefit from the novel compositions described herein and can be made using conventional hot blown film fabrication techniques or other biaxial orientation processes such as tenter frames or double bubble processes. Conventional hot blown film processes are described, for example, in The Encvclouedia of Chemical Technologv, Kirk-Othmer, Third ~dition, John Wiley & Sons, New York, 1981, vol. 16, pp. 416-417 and Vol. 18, pp. 191-192.
Biaxial orientation film manufacturing process such as described in a "double bubble"
to process as in U.S. Patent 3.456,044 (Pahlke), and the processes desuibed in U.S.
Patent 4,352,849 (Mueller), U.S. Patent 4,597,920 (Golike), U.S. Patent 4,820,°S57 (Warren), U.S. Patent 4,837,084 (Warren), U.S. Patent 4,865;902 (Golike et al.), U.S.
Patent 4,927,708 (Herran et al.), U.S. Patent 4,952,451 Mueller), U:S. Patent 4,963,419 (Lustig et al.), and U.S. Patent 5,059,481 (Lustig et al.), can also be used to make film structures from the novel compostions described herein. The film structures can also be made as described in a tenter-frame technique, such as that used for oriented polypropylene.
Other multi-layer film manufacturing techniques for food packaging applications are described in Packagin4 Foods Wdh Plastics, by Wilmer A.
Jenkins 2o and James P. Harrington (1991), pp. 19-27, and in "Coextrusion Basics' by Thomas I.
Butler, Film Extrusion Manual: Process. Materials. Properties pp. 31-80 (published by the TAPPI Press (1992)).
The films may be monolayer or muftilayer films. The film made from the novel compostions can also be coextruded with the other layers) or the film can be laminated onto another layers) in a secondary operation, such as that described in Packaging Foods Wdh Plastics, by Wilmer A. Jenkins and James P. Harrington (1991) or that described in "Coextrusion For Barrier Packaging' by W.J.
Schrenk and C.R. Finch, Society of Plastics Engineers RETEC Proceedings, June 15-17 (1981), pp. 211-229. If a monolayer film is produced via tubular film (that is, blown film techniques) or fiat die (that is, cast film) as described by K.R. Osbom and W.A.
Jenkins in "Plastic Films, Tehcnology and Packaging Applications' (Technomic Publishing Co., Inc. (1992), then the film must go through an additional post-extrusion step of adhesive or extrusion lamination to other packaging material layers to form a multilayer - structure. If the film is a coextrusion of two or more layers (also described by Osborn and Jenkins), the film may still be laminated to additional layers of packaging materials, depending on the other physical requirements of the final film.
"Laminations vs. Coextrusion" by D. Dumbleton (Converting Magazine (September 1992), also discusses lamination versus coextrusion. Monolayer and coextruded films can also go through other post extrusion techniques, such as a biaxial orientation process.
Extrusion coating is yet another technique for producing multilayer film structures using the novel compositions described herein. The novel compositons 1o comprise at least one Payer of the film structure. Similar to cast film, extrusion coating is a flat die technique. A sealant can be extrusion coated onto a substrate either in the form of a monolayer or a coextruded extrudate.
Generally for a multifayer film structure, the novel compostions described herein comprise at least one layer of the total multilayer film structure.
Other layers of the multilayer structure include but are not limited to barrier layers, an/or tie layers, and/or structural layers. Various materials can be used for these layers, with some of them being used as more than one layer in the same film structure. Some of these materials include: foil, nylon, ethylenelvinyl alcohol (EVOH) copolymers, polyvinylidene chloride (PVDC), polyethylene terephhalate (PET), oriented polypropylene (OPP), ethyfene/vinyl acetate (EVA) copolymers, ethylene/acrylic acid (EAA) copolymers, ethylene/methacrylic acid {EMAA) copolymers, LLDPE, HDPE, LDPE, nylon, graft adhesive polymers (for example, malefic anhydride grafted polyethylene), and paper. Generall, the multilayer film structures comprise from 2 to 7 layers.
The following examples are illustrative of certain specific embodiments of this invention.
EXAMPLES
Materials The polymers in Table I below were made via solution process using 3o the appropriate catalyst. Table f describes the properties of the various polymers used. Table II describes the compositions and densities of blends A-H and the comparative blend. The data on these blends is presented in FIGURES 1-6. _ WO 97/26297 PCT/US97lO1I80 - TABLE I
Polymer Characterization Polymer Melt Index Crystallinity Designation Polymer Type* (g/l0min.) percent) SLEP 1 Homog./POE 1.0 - 14.0 SLEP 2 Homog./POE 0.5 g.g SLEP 3 Homog./POP 1.6 32.5 SLEP 4 Homog./POE 1.0 21.5 SLEP 5 Homog./POE 1.0 25.2 SLEP 6 Homog.iPOP 1.0 38.2 SLEP 7 Homog./POP 1.0 4g.g SLEP 8 Homog./POE 3.0 17.8 SLEP 9 Homog./POE 30 14.0 SLEP 10 Homog./POP 30 38.2 LLDPE1 Heterogen. PE -- 35.3 *POE means polyolefin elastomer, POP means polyolefin plastomer.
All are ethylene 1-octene copolymers.

TABLE !I
Blend Composition Wt _ percent of Components in Blend ~

Component A B C D E F G H C-1 Blend 14.0 17.8 17.8 17.8 17.8 17.8 17.8 25.2 25.2 Crystallinity Eguipment and Procedures The polymer blends were prepared in a Haake Torque Rheometer using a mixing bowl having total capacity of either 40 grams or 200 grams. The mixing was 1o carried out at 190 C at 60 rpm for about 6 minutes.
Softening point under Toad determinations were made using a ThermoMechanical Analyzer made by Perkin-Efmer, model TMA-7, with a flat probe diameter of 1.0 mm was used. The samples were melt pressed at 190 C for 3 minutes and then air-cooled to room temperature. The samples had thicknesses of - about 3 mm. A small circle of about 8 mm diameter was cut and placed onto the sample holder in the TMA. The samples were heated at a rate of 5 C/min from 25 C
onwards under a constant probe force of 1 N. Probe penetration as a function of - temperature was measured. The temperature at the probe penetration of 1 mm was taken as the softening point under load of the materials.
SLEP/SLEP and SLEP/LLDPE blends exhibited higher softening point under load and lower compression set at 70 C compared to single component SLEP resin at equivalent density.
FIGURE 1 shows that an SLEP 2lSLEP 3 blend according to the present invention exhibits a higher softening point under load than a single SLEP
having the same density, SLEP 1 (o,~). The disparity in resistance to probe penetration is even greater at one-tenth constant probe force as shown by the 1 cN plots.
FIGURE 2 shows that resistance to probe penetration is improved at elevated temperature relative to a single polymer of the same density (SLEP 8) over a wide range of component (A) to component (B) weight ratios and density differences. In this illustration, the optimum crystaliinity difference is 18.5 percent gel illustrated by blend D according to this invention.
FIGURE 3 shows that the softening point under load of the SLEP 2/SLEP 3 blend according to the present invention ( ) is higher than the softening point under load under the rule of mixtures represented by the straight line correlation from the softening point of SLEP 2 (60 C at 0 wt percent SLEP 3} to the softening point of SLEP 3 (95 C at 100 wt percent SLEP 3).
The Shore A hardness versus temperature method is an extension of the ASTM 2240 Shore A method at room temperature. The following procedure was used to obtain Shore A hardness versus temperature data: A blend obtained using the above mixing procedure was melt pressed at 190 C and held at 190 C for 3 minutes. The sample was removed and immediately placed between two platens cooled using water at room temperature. The samples had thickness of about 125 mm. A sample piece of about 2" X 1.5" (5 cm X 3.8 cm) was obtained from the . 30 plaque and the room temperature hardness was measured. The same sample piece was then placed on a metal plate in a forced air oven. The hardness of the samples was obtained at higher temperatures in 5 C increments from 40 C onwards. The temperature at Shore A hardness of 45 approximated the softening point under load of these samples. Each Shore A hardness measurement is based on the maximum - Shore A hardness shown on a hand held durometer when the durometer is first pressed against the sample.
FIGURE 4 shows that blends (A) and (G) according to the present invention exhibit a Shore A hardness of 45 at a higher temperature than the single polymer of the same density, SLEP 1. it also shows that blend (A), which is a blend of two homopolymers, exhibits a Shore A hardness of 45 at a higher temperature than blend ' (G), which is a blend of a homogeneous polymer with a heterogeneous polymer (LLDPE1).
FIGURE 5 shows that blend (H) according to the present invention exhibited 1o a Shore A hardness of 45 at a temperature about 10 C higher than SLEP 1 having the same density and at a temperature about 3 C higher than comparative blend in which the M~ are reversed for the high and low density polymers in a 50:50 blend.
Compression set testing was carried out according to ASTM D395-85. The sample to be tested was molded into plaques of 120 and 60 mm thickness and then punched out into disks having the required thickness (0.49 f 0.02 inch (1.2 ~
0.05 cm)) and diameter (1.14 ~ 0.01 inch (2.90 ~ 0.02 cm)). The disks were stacked and the original thickness, to, was measured. The stack was then placed on mylar in a compression device having a 3/8 inch (1 cm) (t~) spacer bar and subjected to compression for 22 hours at 70 C by placing the device in a circulating air oven. The 2o samples were then removed from the compression device and allowed to cool for 30 minutes. The final thickness, t;, was then measured.
Compression set was calculated based on the equation:
CB= [(to - t;)/(tfl - tn) x 100 in which CB equals compression set expressed as percentage of the original deflection.
FIGURE 6 shows compression set at 70 C data for five ratios of low density polymer to high density polymer for two pairs of polymer components. The combination of the low density, fow M~ polymer with the higher density, higher M"
(SLED 9/SLEP 6) has a Lower compression set at 70 C at all blend ratios than the combination in which the M" was greater for the low density polymer. Lower compression set means better elastic recovery.
Blends which consist of the listed polymer components having the same or different melt indices (molecular weights) and a density of at least 0.01 g/cc are prepared to determine if higher loading of processing/extender oil could be incorporated in the mixture without blooming (oil loss over time). The blend plus oil composites are compared to pure polymer plus oil composites having the same final melt index and density of the polymer phase.
The blend composites are prepared in a small scale internal mixer (Haake System 90) and can be made via any internal or continuous process that allows addition of multiple ingredients such as BanburyT"" type mixers, single or twin screw extruders, etc. The blends can also be prepared via multiple reactor configurations.
The elevated tempefature pe-rformance of the blends can be enhanced by incofporating copolymers made with higher alpha-olefins (such as octane)compared 1o to copolymer blends that contain propylene as a comonomer. The specific example below shows that blends of polymers with oil have higher tensile strengths at ambient tem~pe~ature (23 C) and at elevated temperature X60 ~C) zompared to blends of propylene and octane copolymers and having same final melt index, density and oil content.
IS The applications for the softer polymers include extrusion and injection articles, FDA-compliant packaging, wire and cable insulation, automotive application and footwear.
Examt~le A
A polyolefin elastomer, EG8100 having a melt index of 1.0 g/10min and a 2o density of 0.87 glcc is blended with a polyolefin plastomer, AffINITYT'~' PL1880, having a melt index of 1.0 g110min and a density of 0.902 glcc in a 53:47 ratio to give an overall melt index of 1.0 g/10min and a density of fl.885 g/cc. The BLEND
(IabeNed in FIGURE 7) is compared to a pure ENGAG~T"" ~-68003 (labelled QUR~
in FIGURE 7) having a melt index of 1.0 g/10min and a density of 0.885 g~c.
25 The oil used is a United States Pharmacopoein (USP) white mineral oil, DuoprimeT"" 200, supplied by LyondeH Petrochemical.
The compound is mixed on a Haake Torque Rheometer System 90 with a Rheomix 3000 mixing head and roller type blades. The temperature is zontrolled at 100 C. The polymer is added to the mixer and run at 30 ftPM for 5 minutes.
'The 3o speed is increased to 50 RPM to add the oil. The oil is added slowly #v avoid losing torque during mixing. After all the oil is added, the mixer speed is reduced 40 ~ RPM
and mixed for 5 minutes.
After removing the compound from the mixer, a portion of the sample is compression molded into a 125 mil .(0.32) plaque at 100 C using 133 kN rtoFCe on a ~ 7.6 cm x 17.8 cm (3 inch x 7 inch) sample. The sample is pressed for 1 minute with no pressure to preheat the sample, then for 2 minutes at the specified force.
The samples are cooled at the same force in the cooling section of the press at 23 C for 2 minutes.
Oil blooming is determined by cutting the compression molded samples into 2 each, 1. 5 inch x 3-inch (3.8 cm X 8 cm) plaques and weighing the cigarette paper (to the nearest 0.0001 g) before placing the paper between the plaques. The paper used TM.
is Bugler Premium No. 1 size, imported by Brown and Williamson Tobacco Corp., z0 Louisville, Kentucky 40232.
The paper is very thin, so any excess oil that exudes to the surface will be absorbed by the paper and a weight change will be observed. The plaque and paper "sandwich" is allowed to equilibrate for 24 hours at standard lab conditions (72 f and 50 percent relative humidity).
The paper is weighed after the first 24 hours to determine if the paper has absorbed any oil. An increase in the weight of the cigarette paper by 2 percent or greater constitutes a loss of oil by bleeding. FIGURE 7 illustrates the improvement in oil loading and effect on Shore A hardness.
Examale B .
This example relates to filled systems which include polymer blend, oil and talc. The compounds are prepared in a BanburyT"" "BR" internal mixer. The capacity of the mixer was 1573 cm' and the loading remained constant at 75 percent full including all ingredients. Table III lists the formulations of the compounds tested.

TABLE III
8anburyr"'MaurialPhR SP.GR VolumeVol GntnsWt rcem reent 51319-32-?Resin 100 0.87 114.9474.9 768.3466.7 S.Gr 0.98 rcem ( >um IM, 0.87Ot7 25 0.852 29.34 19.1 192.0916.7 WN[g] 1152.52 lcc rcent rcem Tak 25 2.7 9.26 6.0 192.0916.7 Load 7.08 Factor cem tcem 150 153.54 Cdunber~7575 percent rcent Full 51319-32-7PF1140 20 0.895 22.35 14.6 163.2413.3 S.Gr 0.97 rcem rcem 0.6MØ87DEG818080 0.86 93.02 60.4 612.9753.3 Wt"(gJ 1149.32 /tc rcent rcem Oil 25 0.852 29.34 19.1 191.5516.7 Load 7.66 Factor rcem reent Blend Tak 25 27 9.26 0.0 191.3516.7 rata reent 130 163.7 Chamber 75 ~ percem 75 petrem Full The rheological characterization was made in a Rheometric dynamic Mechanical Spectrometer RMS-800. The tests were run at 130 C over a frequency of 0.1 to 100 Hertz. The frequency is equivalent to the apparent shear fate by using the Cox-Mertz rule. FIGURE 8 shows that the Blend compound has a higher viscosity due to the lower 12 of the blend (Calculated Blend Iz=0.6 gI10 min compared 1o to an IZ = 1 g110 min in the single resin compound)_ The ambient temperature stress-strain behavior of the single resin system compared to the blend is shown in FIGURE 9, The compounds were measured using an lnstron Model 1123 universal tester. The rate was 2 inches (5 cm) per minute and the sample geometry was similar to ASTM C-178 with a shorter .(0.25 ~5 inch (0.63 cm)) guage length FIGURE 10 shows the effect of blending on the Shore A hardness of the compound as a function of temperature. The blended tampound retains its hart~.ness at higher temperatures compared to the single resin system. This is an ~exampte of the improved under load softening temperature (ULST) in a polymer blend with oil 2o including filler for cost savings.
The dynamic modulus as a function of temperature is shown in flGUf~~ 11.
The blend shows an increase in the temperature at which the modulus drops off significantly.
The data in Table (V below shows the level of oil thatcan be incorpora#ed in 25 the blend depends on the melt index of the polymer components (Polymer A
and Polymer B) in the blend. Sample 51319-26-3 showes oil bloom while the same melt index and calculated overall density blend (51319-30-6) with the same level of SheIIfIexT"" 371 oil does not show oil bloom. This effect is not noticed until higher level of oil (70 phr or greater) is added to the blends.

- TABLE IV
Effect Of Oil Loading And Molecutar Weight Of The Blend Components _ 51319-51319- 51319-51319-26-51319-51319-26-51319-26-PolymerIMI, IMI, IMI, 1MI, 1MI, 30MI,30M1, 1MI, 1MI, A 0.8850.87 0.885 0.87 0.87 0.87 0.87 0.87 0.87 Polymer- 1MI, - 1MI, 1MI, IMI, 1MI, 30MI, 30MI, B 0.902 0.902 0.902 0.9020.902 0.902 0.902 Composite1MI, 1MI, IMI, 1MI, 1MI, 6MI, 6MI, SMI, SMI, 0.8850.885 0.885 0.885 0.885 0.8850.885 0.885 0.885 Oil 0 0 50 50 70 50 70 SO 70 Phr Mixing 2500 2494 490 790 584 310 95 270 226 TRQ

Tem 115 100 110 106 103 100 102 105 99 Oil None None ExcessiveNone ModerateNone ModerateNone None Bleed Tensile4278.33844 - 2039 1552 869 635 1338 998 Elon 1985.51720 - 2921 2884 2230 2113 2830 2871 Tou 3873330636 29807 22422 7240 8704 20600 15883 h Hardness87 88.3 - 69.9 62.1 65.6 56.9 b6.1 58.5 Measuredh atic d durometerpe wit the test ty A
automstan The elevated temperature resistance to penetration was measured by thermomechanical analysis (TMA). The effect of an additional component to the blend improves the elevated temperature performance of the compound. Addition of to the filler had no effect on the TMA results. FIGURE 12 shows the TMA of the binary and ternary polymer blend compounds.
FIGURE 13 shows the stress-strain behavior of the blends made with the different comonomer in the lower density component (with oil) run at room temperature . FIGURE 14 shows the stress-strain behavior of the same blends (with oil} run at 60 C. At both temperatures, the blend that contained the octene copolymer showed improved tensile properties. FIGURE 15 shows the peak stress at ambient and elevated temperature stress-strain analysis.
The effect of blending poymers with different density (crystallinity content) to get the same MI and density as a straight resin also shows an advantage in the 2o blend's ability to retain oil to lower temperatures before bleed-out as observed by the cigarette paper weight gain method. Table V below lists the samples, the target MI
and density of the polymer and blends and the observations made during the experiments. The samples are allowed to equilibrate at the temperature fisted in the table and the weight gain of the cigarette paper monitored. A "Y" in the table means that the paper increases in weight by a value greater than 2 percent and the excess oil bleeds out of the sample.

TABLE V
Low Temperature Oit Loss Experimental Resuits Description . Temerature(C) Tar et Melt Index (MI) 23 5 0 -12 -23 and Densi [ /cc]

53215-26-16IMI, 0.895 g/cc StraightY
Resin + 15 percent ' oil 53215-26-181MI. 0.895 /cc Blend N N Y
+ 15 ercent oiI

53215-26-11IMI, 0.885 g/cc StraightY
Resin + 30 percent oil 53215-26-14IMI. 0.885 /cc Blend N Y
+ 30 rcent oil 53215-26-4IMF, 0.87 g/cc StraightN Y
Resin + 50 percent oil 53215-26-81MI. 0.87 /ec Blend N N N N Y
#I + 50 ercent oil 53215-26-19tMI, 0.87 /cc Blend N N N Y
#2 + 50 ercent oil 53215-26-31MI, 0.87 g/cc StraightN N N N Y
Resin + 30 percent oil 53215-26-17~1MI. 0.87 g/cc Blend N N N N N
#I + 30 percent oil TABLE VI
Comr'onents of the Blends Listed inTable 3 Sam le Blend Co_m~onents 53215-26-18 IMI, 0.885 /cc + 1MI, 0.9_15~/cc 53215-26-14 IMI, 0.87 /cc + 1.6MI, 00.895 /cc 53215-26-8 0.5MI, 0.863 /cc + 1.6MI, 0.895 1cc 53215-26-I9 0.5MI, 0.858 /cc + 1MI, 0.915 /cc 53215-26-I7 0.5MI, 0.863 g/cc + 1.6MI, 0.895 !cc The results show that the blends are able to go to lower temperatures before the oil bleeds out compared to the same MI and density single polymer compound.
i5 FIGURE 16 shows that at temperatures the in-reactor polymer blend retains Shore A hardness substantially better than the individual polymer components.
This property is displayed even when 30 percent oil is added to the blend. This shows that softness can be increased and polymer consumption can be reduced by adding oil to the blends according to this invention and still achieve sufficient hardness at elevated temperatures.
Illustrative examples of how to make ultra-low molecular weight ethylene polymers are provided below.

Catalyst Preparation Part 1: Preparation of TiCl3_ D( ME)~,5 The apparatus (referred to as R-1) was set-up in the hood and purged with nitrogen; it consisted of a 10 L glass kettle with flush mounted bottom valve, 5-neck head, teflon gasket, clamp, and stirrer components (bearing, shaft, and paddle). The necks were equipped as follows: stirrer components were put on the center neck, and the outer necks had a reflex condenser topped with gas inlet/outlet, an inlet for solvent, a thermocouple, and a stopper. Dry, deoxygenated dimethoxyethane (DME) was added to the flask (approx. 5.2 L). In the drybox, 300 g of TiCl3 was weighed into an equalizing powder addition funnel; the funnel was capped, removed from the drybox, and put on the reaction kettle in place of the stopper. The TiCl3 was added over about 10 minutes with stirring. After the addition was completed, additional DME was used to wash the rest of the TiCl3 into the flask. This process was then repeated with 325 g of additional TiCl3, giving a total of 625 g. The addition funnel was replaced with a stopper, and the mixture heated to reflex. The color changed from purple to pale blue. The mixture was heated for about 5 hours, cooled to .room temperature, the solid was allowed to settle, and the supernatant was decanted from the solid. The TiCl3(DME)1,5 was left in R-1 as a pale blue solid.
Part 2: Preparation of f(Me4C )SiMe~N-t-BulfM~1C11~
The apparatus (referred to as R-2) was set-up as described for R-1, except that flask size was 30 L. The head was equipped with seven necks; stirrer in the center neck, and the outer necks containing condenser topped with nitrogen inlet/outlet, vacuum adapter, reagent addition tube, thermocouple, and stoppers. The flask was loaded with 7 L of toluene, 3.09 kg of 2.17 M i-PrMgCI fn Et20, 250 mL of THF, and 1.03 kg of (Meq,CSH)SiMe2NH-t-Bu. The mixture was then heated, and the ether allowed to boil off into a trap cooled to -78 °C. After three hours, the temperature of the mixture had reached 80 °C, at which time a white precipitate formed. The temperature was then increased to 90 °C over 30 minutes and held at this temperature for 2 hours. At the end of this time, the heater was turned off, and 2 L of DME was added to the hot, stirring solution, resulting in the formation of additional precipitate. The solution was allowed to cool to room temperature, the material was allowed to settle, and the supernatant was decanted from the solid. An additional wash was done by adding toluene, stirring for several minutes, allowing the - solids to settle, and decanting the toluene solution. The j(Me4C5)SiMe2N-t-Bu]jMgCl]2 was left in R-2 as an off-white solid.
Part 3: Preparation of f(r~5-Me4C5)SiMe?N-t-BulTi(h4-1,3-pentadiene) The materials in R-1 and R-2 were slurried in DME (the total volumes of the s mixtures were approx. 5 L in R-1 and 12 L in R-2). The contents of R-1 were transferred to R-2 using a transfer tube connected to the bottom valve of the flask and one of the head openings in the 30 L flask. The remaining material in R-1 was washed over using additional DME. The mixture darkened quickly to a deep redlbrown color. After 15 minutes, 1050 mL of 1,3-pentadiene and 2.60 kg of 2.03 M
n-BuMgCi in THF were added simultaneously. The maximum temperature reached in the flask during this addition was 53 °C. The mixture was stirred for 2 hours, then approx. 11 L of solvent was removed under vacuum. Hexane was then added to the flask to a total volume of 22 L. The material was allowed to settle, and the liquid layer (12 L) was decanted into another 30 L glass kettle {R-3). An additional 15 liters of is product solution was collected by adding hexane to R-2, stirring for 50 minutes, again allowing to settle, and decanting. This material was combined with the first extract in R-3. The solvent in R-3 was removed under vacuum to leave a redlblack solid, which was then extracted with toluene. This material was transferred into a storage cylinder. Analysis indicated that the solution (11.75 L) was 0.255 M in titanium; this is 2o equal to 3.0 moles of j(r15-Me4C5)SIMe2N-t-Bu]Ti(~4-1,3-pentadiene) or 1095 g.
This is a 74 percent yield based on the titanium added as TiCl3.
Synthesis of the Ultra-low Molecular Weight Polymer The polymer products of Examples 1 and 2 were produced in a solution polymerization process using a well-mixed recirculating loop reactor. They were each 25 stabilized with 2000 ppm IRGANOX 1076 hindered polyphenol stabilizer (available from Ciba-Geigy Corporation) and 35 ppm deionized wafer (as a catalyst kill agent).
The ethylene and the hydrogen (as well as any ethylene and hydrogen which are recycled from the separator, are combined into one stream before being introduced into the diluent mixture, a mixture of Cg-C10 saturated hydrocarbons, for 30 example, ISOPAR E (available from Exxon Chemical Company) and the comonomer 1-octene.

- The metal complex and cocatafysts are combined info a single stream and are also continuously injected into the reactor. The catalyst is as prepared in the Catalyst Description set forth above, the primary cocatalyst is tri{pentafluorophenyl)borane, available from Boulder Scientific as a 3 wt percent solution in ISOPAR-E mixed hydrocarbon, and the secondary cocatalyst is triisobutyl aluminum-modified ' methyialumoxane (MMAO Type 3A), available from Afczo Nobel Chemical Inc. as a solution in heptane having 2 wt percent aluminum.
Sufficient residence time is allowed for the metal complex and cocatalyst to react prior to introduction into the polymerization reactor. The reactor pressure is held constant at about 475 psig. After polymerization, the reactor exit stream is introduced into a separator where the molten polymer is separated from the unreacted comonomer{s), unreacted ethylene, unreacted hydrogen, and difuent mixture stream, which are in turn recycled for combination with fresh comonomer, ethylene, hydrogen, and diiuent, for introduction into the reactor. The molten polymer is subsequently strand chopped or pelletized, and, after being cooled in a water bath or pefletizer, the solid pellets are collected. Table 111 describes the polymerization conditions and the resultant polymer properties.

TABLE VII
Ex. 1 Ex. 2 Ethylene fresh feed rate (lbs/hr) 140 140 (kg/hr) (63.5) (63.5) Total ethylene feed rate (lbs/hr) 146.17 146.5 (kg/hr) (66.30) (66.30) Fresh octene feed rate (lbs/hr) 49.5 12.67 (kg/hr) (22.5) (5.75) Total octene feed rate (lbs/hr) 112 32.9 (kg/hr) (50.5) (14.9) Total octene concentration (weight percent)11.4 3.36 Fresh hydrogen feed rate (standard cm'/min)5350 16100 Solvent and octene feed rate (lbs/hr) 839.4 840 (kg/hr) (381) (381) Ethylene conversion rate (wt percent) 90.3 88.26 Reactor temperature (C) 119.8 134.3 Feed temperature (C) 15 15.3 Catalyst concentration (ppm) 70 70 Catalyst flow rate (lbs/hr) 1.265 4.6 (kg/hr) (0.57) (2.1) Primary cocatalyst concentration (ppm) 2031 1998 Primary cocatalyst flow rate (lbs/hr) 1.635 5.86 (kg/hr) (0.74) (2.66) Primary cocatalyst to catalyst molar ratio 3.48 2.897 Secondary cocatalyst concentration (ppm) 198 198 Secondary cocatalyst flow rate (lbs/hr) 1.258 3.7 (kg/hr) (0.57) (1.7) Secondary cocatalyst to catalyst molar ratio4.986 4.037 Product density (g/cm') 0.8925 0.9369 Product melt viscosity at 350F (centipoise)4,000 400 at 177C (Pas) (4.000) (0.400) Polymer melt index (Iz at 190C) 1,900* 14,000 Polymer Mn 8,900* 4,700*

Although the invention has been described in considerable detail through the preceding specific embodiments, it is to be understood that these embodiments are for purposes of illustration only. Many variations and modifications can be made by one skilled in the art without departing from the spirit and scope of the invention.

Claims

CLAIMS:

1. A polymer mixture comprising (A) at least one homogeneously branched ethylene polymer having a crystallinity in the range from 0 to 50 percent and (B) at least one ethylene polymer having a crystallinity in the range from 5 to 80 percent which is at least 7 percent greater than the crystallinity of component (A) provided that (1)(a) when component (A) has a crystallinity greater than or equal to 21.5 percent and a melt index less than or equal to 10 dg/min., component (B) is a homogeneous polymer and (b) when the crystallinity of component (B) is greater than 21.5 percent, component (B) is present in an amount less than 40 wt percent, (2) the number average molecular weight of component (B) is greater than or equal to the number average molecular weight of polymer (A), (3) component (B) comprises at least one interpolymer of ethylene with at least one comonomer selected from the group consisting of vinyl esters of a saturated carboxylic acid wherein the acid moiety has up to 4 carbon atoms, unsaturated mono- or dicarboxylic acids of 3 to 5 carbon atoms, a salt of the unsaturated acid, esters of the unsaturated acid derived from an alcohol having 1 to 8 carbon atoms, and mixtures thereof, and (4) at least one of the ethylene polymer components of the polymer mixture comprises an ultra-low molecular weight ethylene polymer having a crystallinity from 0 to 80 percent, a melt viscosity at 350°F up to 8200 cp and a molecular weight distribution from 1.5 to 2.5, wherein the polymer mixture has an overall crystallinity in the range from 6 to 50 percent and when component (B) does not comprise interpolymer (B)(3) and none of the ethylene polymer components of the polymer mixture comprise the ultra-low molecular weight ethylene polymer, the polymer mixture has a molecular weight distribution not greater than 3 when the overall crystallinity is greater than or equal to 21.5 percent.

2. The polymer mixture of claim 1, wherein the crystallinity of component (B) is at least 10%.

3. The polymer mixture of claim 1 or 2, wherein component (A) is at least one substantially linear ethylene polymer ("SLEP") wherein the SLEP has i. a melt flow ratio, I10/I2>=5.63, ii. a molecular weight distribution, M w/M n, as determined by gel permeation chromatography and defined by the equation:
(M w/M n)<=(I10/I2)-4.63, iii. a gas extrusion rheology such that the critical shear rate at onset of surface melt fracture for the SLEP is at least 50 percent greater than the critical shear rate at the onset of surface melt fracture for a linear ethylene polymer, wherein the SLEP and the linear ethylene polymer comprise the same comonomer or comonomers, the linear ethylene polymer has an I2, M w/M n and density within ten percent of the SLEP and wherein the respective critical shear rates of the SLEP and the linear ethylene polymer are measured at the same melt temperature using a gas extrusion rheometer, and iv. a single differential scanning calorimetry, DSC, melting peak between -30 and 150°C.

4. The polymer mixture of claim 3, wherein component (B) is at least one SLEP wherein the SLEP has i. a melt flow ratio, I10/I2>=5.63, ii. a molecular weight distribution, M w/M n, as determined by gel permeation chromatography and defined by the equation:
(M w/M n)<=(I10/I2)-4.63, iii. a gas extrusion rheology such that the critical shear rate of onset of surface melt fracture for the SLEP is at least 50 percent greater than the critical shear rate at the onset of surface melt fracture for a linear ethylene polymer, wherein the SLEP and the linear ethylene polymer comprise the same comonomer or comonomers, the linear ethylene polymer has an I2, M w/M n and density within ten percent of the SLEP and wherein the respective critical shear rates of the SLEP and the linear ethylene polymer are measured at the same melt temperature using a gas extrusion rheometer, and iv. a single differential scanning calorimetry, DSC, melting peak between -30 and 150°C.

5. The polymer mixture of claim 3 or 4, wherein the SLEP has 0.01 to 3 long chain branches/1000 carbons.

6. The polymer mixture of claim 5, wherein the SLEP
has up to 1 long chain branch/1000 carbons.

7. The polymer mixture of claim 1 or 2, wherein component (A) has less than 0.01 long chain branch/1000 carbons.

8. The polymer mixture of any one of claims 1 to 7, wherein at least one of component (A) or component (B) is an interpolymer of ethylene and at least one .alpha.-olefin selected from the group consisting of 1-propylene, 1-butene, 1-isobutylene, 1-hexene, 4-methyl-1-pentene, 1-pentene, 1-heptene and 1-octene.

9. The polymer mixture of claim 8, wherein at least one of component (A) or component (B) is a copolymer of ethylene and 1-octene.

10. The polymer mixture of any one of claims 1 to 9, wherein at least one component (A) or component (B) is a terpolymer of ethylene, propylene and a non-conjugated diene.

11. The polymer mixture of claim 10, wherein the non-conjugated diene is selected from the group consisting of 1,4-hexadiene, dicyclopentadiene, 5-ethylidene-2-norbornene, 5-methylene-2-norbornene, 7-methyl-1,6-octadiene, piperylene, and 4-vinylcyclohexene.

12. The polymer mixture of any one of claims 1 to 11 wherein the weight ratio of component (A) to component (B) is in the range from 30:70 to about 95:5.

13. The polymer mixture of any one of claims 1 to 12, further comprising:
(C) at least one homogeneously branched ethylene polymer having a crystallinity between the crystallinities of components (A) and (B) and having a crystallinity which differs from the crystallinities of components (A) and (B) by at least 7%.

14. ~The polymer mixture of claim 13, wherein the crystallinity of component (B) is at least 30% greater than the crystallinity of component (A).

15. ~The polymer mixture of claim 13, wherein component (A) and component (C) are each at least one substantially linear ethylene polymer ("SLEP") wherein the SLEP has i. a melt flow ratio, I10/I 2>=5.63, ii. a molecular weight distribution, M w/M n, as determined by gel permeation chromatography and defined by the equation:
(M w/M n) <= (I10/I2) -4.63, iii, a gas extrusion rheology such that the critical shear rate at onset of surface melt fracture for the SLEP is at least 50 percent greater than the critical shear rate at the onset of surface melt fracture for a linear ethylene polymer, wherein the SLEP and the linear ethylene polymer comprise the same comonomer or comonomers, the linear ethylene polymer has an I2, M w/M n and density within ten percent of the SLED and wherein the respective critical shear rates of the SLEP and the linear ethylene polymer are measured at the same melt temperature using a gas extrusion rheometer, and iv. a single differential scanning calorimetry, DSC, melting peak between -30 and 150°C.

16. ~The polymer mixture of any one of claims 13 to 15, wherein the combined weight of components (A) and (B) is at least 60 weight-percent of the combined weight of the polymers in the polymer mixture.

17. ~The polymer mixture of any one of claims 1 to 16 further comprising an oil.

18. ~A process for making a molded article comprising:

(A) heating a polymer mixture according to any one of claims 1 to 17 to a temperature suitable for injection molding;
(B) injecting the polymer mixture of step (A) into a mold to form the molded article; and (C) removing from the mold the molded article formed in step (B).

19. ~The process of claim 18 further comprising:
(B1) cooling the polymer mixture of step (B), wherein the cooling time period of step (B1) is at least 20 percent less than the cooling time period of step (B1) conducted under the same conditions with a single ethylene polymer made of the same monomer components as component (A) having the same crystallinity and melt index as the polymer mixture.

20. ~The process of claim 18 or 19 wherein component (A) of the polymer mixture is a substantially linear ethylene polymer as defined in claim 3.

21. ~The process of any one of claims 18 to 20 wherein, in step (A) of the process, component (A) is produced in a first reaction vessel, component (B) is produced in a second reaction vessel operating simultaneously with the first reaction vessel and interconnected with the first reaction vessel such that component (A) is continuously mixed with component (B) as components (A) and (B) are being produced.

22. ~A molded article obtained by forming a polymer mixture of any one of claims 1 to 17 into a shape and causing the shaped polymer mixture to become fixed in shape.

23. ~The article of claim 22 wherein the shaped polymer mixture has at least two differential scanning calorimetry melting peaks and lacks a differential scanning calorimetry peak above 115°C.

24. ~The article of claim 22 or 23 wherein the shaped polymer mixture has a softening point under load of at least about 80°C, a 100% modulus of elasticity of at least 140 psi, a compression set of less than 80% at 70°C, an overall crystallinity less than 21.5% and a crosslink density less than 20% gel.

25. ~The article of claim 22 or 23 wherein the shaped polymer mixture has a crosslink density of at least 50% gel.