Classifications

• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
  • C08L23/00—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers
  • C08L23/02—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers not modified by chemical after-treatment
  • C08L23/10—Homopolymers or copolymers of propene
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
  • C08L23/00—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers
  • C08L23/02—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers not modified by chemical after-treatment
  • C08L23/10—Homopolymers or copolymers of propene
  • C08L23/14—Copolymers of propene
  • C08L23/142—Copolymers of propene at least partially crystalline copolymers of propene with other olefins
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
  • C08J2300/00—Characterised by the use of unspecified polymers
  • C08J2300/22—Thermoplastic resins
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
  • C08L2205/00—Polymer mixtures characterised by other features
  • C08L2205/02—Polymer mixtures characterised by other features containing two or more polymers of the same C08L -group
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
  • C08L23/00—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers
  • C08L23/02—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers not modified by chemical after-treatment
  • C08L23/10—Homopolymers or copolymers of propene
  • C08L23/12—Polypropene
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
  • C08L2666/00—Composition of polymers characterized by a further compound in the blend, being organic macromolecular compounds, natural resins, waxes or and bituminous materials, non-macromolecular organic substances, inorganic substances or characterized by their function in the composition
  • C08L2666/02—Organic macromolecular compounds, natural resins, waxes or and bituminous materials
  • C08L2666/04—Macromolecular compounds according to groups C08L7/00 - C08L49/00, or C08L55/00 - C08L57/00; Derivatives thereof

Definitions

• the invention relates to a blend of at least two thermoplastic components differing in their crystallinities.
• the blend has a heterogeneous morphology with distinct phase separated zones of different composition and crystallinity present.
• the resulting blend with the defined morphology shows dramatic improvements in mechanical deformation recoverability when compared to its individual unblended components.
• the invention also relates to improvements in the flexibility of the blend. Changes in the relative amounts or the crystallinities of the blend components or the morphology of the blend affect the recoverability and the flexibility of the blend.
• the inventive blends designed for recoverability contains a dispersed phase of a greater crystallinity and a continuous phase of lesser crystallinity.
• the sizes of the individual domains of the dispersed phase are very small with the smallest length dimension for the dispersed phase being less than 5 ⁇ m. This phase size of the dispersed phase is maintained during processing even without crosslinking.
• the inventive blends designed for flexibility have a slightly wider range in morphology as the components of greater and lesser crystallinity can also be co-continuous.
• the components of the blend in both cases are also compatible to the extent that no compatibilizer needs to be added to attain and retain this fine morphology.
• this invention describes improving the mechanical deformation recoverability of the aforementioned blends by aging the blends and mechanically orienting the articles formed from these blends.
• One of the components is a polymer comprising predominately stereospecific polypropylene, preferably isotactic polypropylene. This is the component with greater crystallinity.
• a second component is a copolymer of propylene and a C 2 , C 4 - C o ⁇ -olefin, preferably ethylene. This is the component with lesser crystallinity.
• the propylene is polymerized substantially stereospecifically.
• the copolymer has a substantially uniform composition distribution preferably as a result of polymerization with a metallocene catalyst.
• said second component is an ethylene propylene copolymer, e.g. ethylene propylene semicrystalline elastomer.
• the copolymer is an ethylene propylene copolymer, e.g., ethylene propylene thermoplastic elastomer.
• the copolymer has a substantially uniform composition distribution preferably as a result of polymerization with a metallocene catalyst Composition distribution is a property of copolymers indicating a statistically significant intermolecular or intramolecular difference in the composition of the polymer. Methods for measuring compositional distribution are described later. Blends of isotactic polypropylene and ethylene propylene rubber are well known in the prior art. However, the traditional Ziegler-Natta catalysts cannot make ethylene propylene thermoplastic elastomers which simultaneously are uniform in compositional distribution, have substantially stereospecific propylene residues and have less than 35 wt. % ethylene.
• U.S. Patent No. 3,882,197 to Fritz et al. describes blends of stereoregular propylene/alpha-olefin copolymers, stereoregular propylene, and ethylene copolymer rubbers.
• U.S. Patent 3,888,949 Chi-Kai Shih assigned to E I Du Pont, shows the synthesis of blend compositions containing isotactic polypropylene and copolymers of propylene and an alpha-olefin, containing between 6 - 20 carbon atoms, which have improved elongation and tensile strength over either the copolymer or isotactic polypropylene.
• Copolymers of propylene and alpha-olefin are described wherein the alpha-olefin is hexene, octene or dodecene.
• the copolymer is made with a heterogeneous titanium catalyst resulting in copolymers with non-uniform composition distribution and a broad molecular weight distribution.
• Non-uniform intramolecular compositional distribution is evident in US Patent No.
• sequences describes a number of olefin monomer residues linked together by chemical formed during polymerization.
• E.G. Kontos discloses the formation of in situ blends of isotactic polypropylene and "stereo block" copolymers of propylene and another olefin of 2 to 12 carbon atoms, including ethylene and hexene.
• the copolymers of this invention are necessarily heterogeneous in intermolecular and intramolecular composition distribution. This is demonstrated by the synthesis procedures of these copolymers which involve sequential injection of monomer mixtures of different compositions to synthesize polymeric portions of analogously different compositions.
• SPC2 crystallizable propylene alpha olefin copolymer
• the SPC2 also has a narrow composition distribution and is made with a metallocene catalyst.
• the addition of SPC2 leads to a finer morphology and improvements in some of the properties of the blend of FPC and SPC.
• crystalline characterizes those polymers which possess high degrees of inter- and intra-molecular order, and which melt higher than 110°C and preferably higher than 115°C and more preferably higher than 130°C and preferably have a heat of fusion of at least 75 J/g, as determined by DSC analysis.
• crystallizable as used herein for SPC describes polymers which are mainly amorphous in the undeformed state, but can crystalize upon stretching or annealing. Crystallization may also be initiated by the presence of a crystalline polymer such as the FPC.
• These polymers have a melting point of less than 105° C or preferably less than 100°C and preferably have a heat of fusion of less than 75 J/g as determined by DSC.
• SPC2 describes those polymers that are substantially crystalline in the undeformed state. Further crystallization may also occur in the presence of the crystalline polymer such as FPC.
• These polymers have a melting point of less than 115° C or preferably less than 100°C and preferably have a heat of fusion of less than 75 J/g as determined by DSC.
• the present invention is directed to blends with heterophase morphology formed by blending a FPC which is a predominately crystalline stereoregular polypropylene with a SPC which is a crystallizable copolymer of a C 2 , C 4 -C 2Q ⁇ -olefin (preferably ethylene) and propylene .
• Optional components of the blend are
• SPC2 a crystallizable copolymer of a C 2 , C 4 -C 2 o ⁇ -olefin (preferably ethylene), and process oil.
• Other optional components are fillers, colorants, antioxidants, nucleators and flow improvers.
• the crystalline polypropylene can be either homopolymer or copolymers with other alpha olefins.
• the FPC may also be comprised of commonly available isotactic polypropylene compositions referred to as impact copolymer or reactor copolymer. However these variations in the identity of the FPC are acceptable in the blend only to the extent that the FPC is within the limitations of the crystallinity and melting point indicated above.
• the FPC may also contain additives such as flow improvers, nucleators and antioxidants which are normally added to isotactic polypropylene to improve or retain properties. All of these polymers are referred to as the FPC.
• the SPC has a melting point of less than 105°C or preferably less than 100°C and preferably has a heat of fusion of less than 75 J/g.
• the SPC2 has a melting point of less than 115° C or preferably less than 100°C and preferably has a heat of fusion of less than 75 J/g.
• the SPC, and SPC2 are copolymer having isotactic propylene sequences.
• the FPC is predominately syndiotactic polypropylene, then the SPC, and the SPC2 if used, is a copolymer having syndiotactic sequences. Therefore, SPC and SPC2 have similar, preferably substantially identical, tacticity to the FPC. It is believed that this matching of stereoregularity increases the compatibility of the components and results in improved adhesion at the interface of the domains of the polymers of different crystallinities in the polymer blend composition.
• One preferable embodiment is blending isotactic polypropylene (FPC) with ethylene propylene copolymers (SPC) having 4 wt. % to 35 wt. % ethylene (to ensure high compatibility with the FPC). Both the FPC and the SPC have isotactic propylene sequences long enough to crystallize. Resulting blends of isotactic polypropylene with ethylene propylene copolymers according to the invention have improved properties as compared to isotactic polypropylene blends with prior art ethylene propylene rubbers.
• FPC isotactic polypropylene
• SPC ethylene propylene copolymers
• a preferred blend comprises 1% to 95% by weight of FPC and a SPC with greater than 65° o by weight propylene and preferably greater than 80% by weight propylene.
• a thermoplastic polymer blend composition of the invention comprises a FPC and a SPC with added process oil.
• the FPC comprises isotactic polypropylene, a reactor copolymer or an impact copolymer as described above and is present in an amount of 1% to 95% by weight and more preferably 2% to 70% by weight of the total weight of the blend.
• the balance of the polymer composition consists of a mixture of the process oil and the SPC and SPC2 if used
• the SPC is a random copolymer of ethylene and propylene having a melting point by DSC of 0°C to 105°C, preferably in the range 20°C to 90°C, more preferably in the range of 25°C to 70° C and an average propylene content by weight of at least 65% and more preferably at least 80%.
• This melting point is due to crystallizable propylene sequences, preferrably of isotactic polypropylene.
• the SPC is made with a polymerization catalyst which forms essentially or substantially isotactic polypropylene, when all or substantially all propylene sequences in the FPC are isotactic.
• the SPC is statistically random in the distribution of the ethylene and propylene residues along the chain. Quantitative evaluation of the randomness of the distribution of the ethylene and propylene sequences may be obtained by consideration of the experimentally determined reactivity ratios of the second polymer component or by 13 C NMR. This is according to the procedures described in the journal article by H. Kakugo, Y Naito, K. Mizunama and T. Miyatake in Macromolecules (1982), pages 1150-1152.
• the SPC is made with a single sited metallocene catalyst which allows only a single statistical mode of addition of ethylene and propylene by polymerization in a well mixed, continuous feed stirred tank reactor which provides a uniform polymerization environment for growth of all of the polymer chains of the SPC.
• the ratio of the FPC to the SPC of the blend composition of the present invention may vary in the range of 1 :99 to 95:5 by weight and more preferably in the range 2:98 to 70:30 by weight.
• the second polymer component may contain small quantities of a non-conjugated diene to aid in the vulcanization and other chemical modification of the blend of the first polymer component and the second polymer component.
• the amount of diene is preferably less than 10 wt. % and preferably less than 5 wt. %.
• the diene may be selected from the group consisting of those which are used for the vulcanization of ethylene propylene rubbers and are preferably ethylidene norbornene, vinyl norbornene and dicy clopentadiene .
• the SPC2 if used, has the same characteristics as the SPC described above.
• the SPC2 has a crystallinity and composition intermediate between the FPC and the SPC.
• the SPC2 is a copolymer of ethylene and propylene while the FPC is homopolymer of propylene.
• the SPC2 has the same type of crystallinity of propylene as in the FPC and SPC and an ethylene content in between FPC and SPC.
• the addition of SPC2 to the blend leads to a better dispersion of the phases in the blend compared to blends of the similar composition which do not have any SPC2.
• the relative amounts of SPC and SPC2 can vary between 95:5 to
• the ratio of the FPC to the sum of SPC and SPC2 may vary in the range of 1:99 to 95:5 by weight and more preferably in the range 2:98 to 70:30 by weight
• the invention is directed to a process for preparing thermoplastic polymer blend compositions.
• the process comprises:
• Blends directed to improvement in the elastic recovery have a continuous phase of lower crystallinity and a dispersed phase of the higher crystallinity.
• the domains of the dispersed phase are small with an average minimum axis less than 5 ⁇ m.
• the larger axis of the dispersed phase can be as large as lOO ⁇ m.
• the dispersed phase consists of a crystalline mixture of FPC with some amount of SPC2 and SPC due to thermodynamic mixing of polymers.
• the continuous phase consists of the balance of the polymers not included in the dispersed phase.
• Blends directed to low flexural modulus may have in addition, a heterogeneous phase morphology with continuous phases of lower and greater crystallinity.
• Commonly available propylene reactor copolymers consisting of a single phase blend of isotactic polypropylene and copolymers of propylene and ethylene are not included within the scope of the invention since they are a single phase with no prominent dispersed or continuous phases.
• Polypropylene blends made by a combination of a FPC and a SPC of the present invention that give a heterophase morphology in which the crystalline polymer is the continuous phase in are excluded from the invention.
• the benefits of the invention are included improvement in the elastic recovery and the flexural modulus of the blend. These improvements are most apparent as a function of the 500% tensile modulus of the blend. Historically, the examples of the prior art have been able to duplicate the improvements in the blend but only for compositions with a very low 500% tensile modulus
• Figure 1 shows the morphology of a blend of this invention. Specifically, Figure 1 shows the morphology of sample H7 in Example 6 below.
• Figure 2 shows the morphology of a blend of this invention. Specifically, Figure 2 shows the morphology of sample K7 in Example 6 below.
• Figure 3 shows the morphology of a blend of this invention which includes SPC2. Specifically, Figure 3 shows the morphology of sample BB7 in Example 6 below.
• Figure 4 and Figure 5 show the stress strain elongation data for blends of this invention.
• Figure 6 shows the elastic recovery of annealed/aged blends of this invention.
• Figure 7 shows the elastic recovery of oriented blends of this invention.
• Figure 8 shows the dependence of the flexural modulus of the blend of this invention as a correlated function of the 500% tensile modulus.
• the blend compositions of the present invention generally are comprised of two components: (1) a crystalline FPC comprising isotactic polypropylene and (2) a crystallizable SPC comprising an alpha-olefin (other than propylene) and propylene copolymer.
• a particular embodiment of the invention contains a crystallizable SPC2 comprising an alpha-olefin (other than propylene) and propylene copolymer.
• a particular embodiment of the invention may comprise process oil as an additional component.
• the blend also has a heterogeneous phase morphology where a more crystalline polymer mixture consisting essentially of all the FPC and some of the SPC and SPC2 is dispersed in domains in a continuous phase of a less crystalline polymer mixture containing the balance of the blend.
• the size of the dispersed domains is small and the morphology is stable in the absence of a compatibilizer.
• compositions of the invention are free of, or substantially free of, compatibilizers.
• the First Polymer Component (FPC) is the First Polymer Component (FPC)
• the FPC component i.e., the polypropylene polymer component may be homopolypropylene, or copolymers of propylene, or some mixtures thereof.
• the FPC has the following characteristics.
• the polypropylene of the present invention is predominately crystalline, i.e., it has a melting point generally greater than 110°C, preferably greater than 115°C, and most preferably greater than 130°C. Preferably, it has a heat of fusion greater than 75 J/g.
• the polypropylene can vary widely in composition.
• substantially isotactic polypropylene homopolymer or propylene copolymer containing equal to or less than 10 weight percent of other monomer, i.e., at least 90% by weight propylene can be used.
• the polypropylene can be present in the form of a graft or block copolymer, in which the blocks of polypropylene have substantially the same stereoregularity as the propylene-alpha-olefin copolymer, so long as the graft or block copolymer has a sharp melting point above 110°C, preferably above 115°C, and more preferably above 130°C, characteristic of the stereoregular propylene sequences.
• the propylene polymer component may be a combination of homopolypropylene, and/or random, and or block copolymers as described herein.
• the percentage of the copolymerized alpha-olefin in the copolymer is, in general, up to 9% by weight, preferably 2% to 8% by weight, most preferably 2% to 6%> by weight.
• the preferred alpha-olefms contain 2 or from 4 to 12 carbon atoms.
• the most preferred alpha-olefin is ethylene.
• One or two or more alpha-olefins can be copolymerized with propylene.
• Exemplar.- alpha-olefins may be selected from the group consisting of ethylene; butene-1 ; pentene-l,2-methylpentene-l,3-methylbutene-l; hexene-1,3- methylpentene- 1.4-methylpentene- 1 ,3 ,3 -dimethylbutene- 1 ; heptene- 1 ; hexene- 1 ; methylhexene-1; dimethylpentene-1 trimethylbutene-1; ethylpentene-1; octene-1 methylpentene-1: dimethylhexene-1; trimethylpentene-1; ethylhexene-1 methylethylpentene-1; diethylbutene-1; propylpentane-1; decene-1; methylnonene-1 nonene-1; dimethyloctene-1; trimethylheptene-1; ethyloctene-1;
• the molecular weight of the FPC can be between 10,000 to 5,000,000 with a polydispersity index (PDI) between 1.5 to 40.0
• thermoplastic polymer blend compositions of the present invention may comprise from 1% to 95% by weight of FPC. According to a preferred embodiment, the thermoplastic polymer blend composition of the present invention may comprise from 2% to 10% by weight of the FPC. According to the most preferred embodiment, the compositions of the present invention may comprise from 2% to 40% by weight of the FPC. An even more preferred embodiment of the invention contains 2% to 25% by weight of FPC in the blend.
• the polymer is a propylene homopolymer obtained by homopolymerization of propylene in a single stage or multiple stage reactor.
• Copolymers may be obtained by copolymerizing propylene and an alpha-olefin having 2 or from 4 to 20 carbon atoms, preferably ethylene, in a single stage or multiple stage reactor.
• Polymerization methods include high pressure, slurry, gas, bulk, or solution phase, or a combination thereof, using a traditional Ziegler-Natta catalyst or a single-site, metallocene catalyst system.
• the catalyst used is preferably one which has a high isospecificity.
• Polymerization may be carried out by a continuous or batch process and may include use of chain transfer agents, scavengers, or other such additives as deemed applicable.
• the SPC of the polymer blend compositions of the present invention comprises a crystallizable copolymer of propylene and another alpha-olefin having less than 10 carbon atoms, preferably ethylene.
• the SPC has the following characteristics: (A)
• the SPC of the present invention preferably comprises a random copolymer having a narrow compositional distribution. While not meant to be limited thereby, it is believed that the narrow composition distribution of the second polymer component is important.
• the intermolecular composition distribution of the polymer is determined by thermal fractionation in a solvent.
• a typical solvent is a saturated hydrocarbon such as hexane or heptane. This thermal fractionation procedure is described below.
• approximately 75% by weight and more preferably 85% by weight of the polymer is soluble in one or two adjacent fractions with the balance of the polymer in immediately preceding or succeeding fractions.
• Each of these fractions has a composition (wt. % ethylene content) with a difference of no greater than 20 wt. % (relative) and more preferably 10 wt. % (relative) of the average wt. % ethylene content of the whole second polymer component.
• the second polymer component is narrow in compositional distribution if it meets the fractionation test outlined above.
• the SPC preferably has a single melting point.
• the melting point is determined by DSC.
• the SPC of the present invention has a melting point between 105°C and 0°C.
• the melting point of SPC is between 90°C and
• the melting point of the SPC of the composition of the present invention is between 70°C and 25°C.
• the second polymer component of the present inventive composition comprises crystallizable propylene sequences.
• the crystallinity of the second polymer component is, preferably, according to one embodiment, from 1% to 65% of homoisotactic polypropylene, preferably between 3% to 30%, as measured by the heat of fusion of annealed samples of the polymer.
• the molecular weight of the SPC can be between 10,000 to 5,000,000 with a polydispersity index (PDI) between 1.5 to 40.0.
• the second polymer component preferably has a narrow PDI between 1.8 to 5. It is preferred if the SPC has a Mooney Viscosity at 125°C less than 100, more preferably less than 75 and more preferably less than 60.
• the low levels of crystallinity in the SPC are obtained by incorporating from 5% to 35% by weight alpha-olefin, preferably from 6% to 30% by weight alpha-olefin, and most preferably, it comprises from 8% to 25% by weight alpha- olefin and even more preferably between 8% to 20% by alpha-olefin. These composition ranges for the SPC are preferred to obtain the objectives of the present invention.
• Alpha olefins comprise one or more members of the group C 2 , C 4 -C 20 ⁇ - olefin.
• the blends of the FPC and SPC are thermoplastic and do not have the phase separated morphology required for the tensile recovery properties of the blends.
• the blends At alpha-olefin compositions higher than the above higher limits for the SPC, the blends have poor tensile strength and a phase separated morphology with a coarse dispersion. It is believed, while not meant to be limited thereby, the SPC needs to have the optimum amount of polypropylene crystallinity to crystallize with the FPC for the beneficial effects of the present invention.
• the preferred alpha-olefin is ethylene.
• compositions of the present invention may comprise from 5% to 99% by weight of the SPC and from 30% to 98% by weight of the SPC. Most preferably, they comprise from 60% to 98% and even more preferably 75% to 99% by weight of the SPC.
• More than one SPC may be used in a single blend with a FPC.
• Each of the SPC is described above and the number of SPC in this embodiment is less than three and more preferably, two.
• the different SPC differ in the crystallinity.
• the SPC2 is more crystalline than the SPC.
• the SPC2 has, preferably, according to one embodiment, from 20% to 65%, and more preferably between 25% to 65% of the crystallinity of homoisotactic polypropylene as measured by the heat of fusion of annealed samples of the polymer.
• the SPC and the SPC2 may also differ in their molecular weight.
• the SPC and SPC2 differ in the alpha-olefin content consistent with the use of two SPC with different crystallinity.
• the preferred alpha-olefin is ethylene. It is believed that the use of SPC2 in conjunction with a blend of a FPC and a SPC acts as an interfacial agent in these blends.
• the resultant morphology consists of a finer dispersion of the highly crystalline component with the continuous phase of the less crystalline phase. Such a morphology leads to in the elastic recovery properties of the blends.
• the second polymer component may also comprise a copolymer of atactic propylene and isotactic propylene. Such crystallizable homopolymers of propylene have been described by R. Waymouth in U. S. Patent 5,594,080, which is included herein by reference.
• the second component of the composition of the present invention may comprise a diene.
• the SPC, and SPC2 if used are copolymers having isotactic propylene sequences. If the FPC is predominately syndiotactic polypropylene, then the SPC, and the SPC2 if used, is a copolymer having syndiotactic sequences.
• SPC and SPC2 have similar, preferably substantially identical, tacticity to the FPC. It is believed that this matching of stereoregularity increases the compatibility of the components results in improved adhesion of the domains of the polymers of different crystallinities in the polymer blend composition. Furthermore, good compatibility is only achieved in a narrow range of copolymer composition for the SPC. Narrow intermolecular and intramolecular compositional distribution in the copolymer is preferred. The aforementioned characteristics of the SPC, and SPC2 if used, are preferably achieved by polymerization with a chiral metallocene catalyst.
• the SPC is made with a polymerization catalyst which forms essentially or substantially isotactic polypropylene when all or substantially all propylene sequences in the FPC are isotactic. Nonetheless, the polymerization catalyst used for the formation of SPC will introduce stereo- and regio- errors in the incorporation of propylene. Stereo errors are those where the propylene inserts in the chain with a tacticity that is not isotactic. A regio error in one where the propylene inserts with the methylene group or the methyldiene group adjacent to a similar group in the propylene inserted immediately prior to it. Such errors are more prevalent after the introduction of an ethylene in the SPC.
• the fraction of propylene in isotactic stereoregular sequences is less than 1 for SPC and decreases with increasing ethylene content of the SPC.
• the introduction of these errors in the introduction of propylene, particularly in the presence of increasing amounts of ethylene are important in the use of these ethylene propylene copolymers as the SPC. Notwithstanding the presence of these errors, the SPC is statistically random in the distribution of ethylene.
• the SPC is made with a polymerization catalyst which forms essentially or substantially isotactic polypropylene, when all or substantially all propylene sequences in the FPC are isotactic.
• the SPC is statistically random in the distribution of the ethylene and propylene residues along the chain. Quantitative sequences may be obtained by consideration of the experimentally determined reactivity ratios of the second polymer component or by 13 C NMR.
• the SPC is made with a single sited metallocene catalyst which allows only a single statistical mode of addition of ethylene and propylene in a well-mixed, continuous monomer feed stirred tank polymerization reactor which allows only a single polymerization environment for all of the polymer chains of the SPC.
• one means for carrying out a process of the present invention for the production of the copolymer second polymer component is as follows: (1) liquid propylene is introduced in a stirred-tank reactor, (2) the catalyst system is introduced via nozzles in either the vapor or liquid phase, (3) feed ethylene gas is introduced either into the vapor phase of the reactor, or sparged into the liquid phase as is well known in the art, (4) the reactor contains a liquid phase composed substantially of propylene, together with dissolved alpha-olefin, preferably ethylene, and a vapor phase containing vapors of all monomers, (5) the reactor temperature and pressure may be controlled via reflux of vaporizing propylene (autorefrigeration), as well as by cooling coils, jackets, etc., (6) the polymerization rate is controlled by the concentration of catalyst, temperature, and (7) the ethylene (or other alpha-olefin) content of the polymer product is determined by the ratio of ethylene to propylene in
• a typical polymerization process consists of a polymerization in the presence of a catalyst comprising a chiral bis (cyclopentadienyl) metal compound and either 1) a non-coordinating compatible anion activator, or 2) an alumoxane activator.
• a catalyst comprising a chiral bis (cyclopentadienyl) metal compound and either 1) a non-coordinating compatible anion activator, or 2) an alumoxane activator.
• An exemplary catalyst system is described in U.S. Patent No. 5,198,401 which is herein incorporated by reference for purposes of U.S. practices.
• the alumoxane activator is preferably utilized in an amount to provide a molar aluminum to metallocene ratio of from 1 :1 to 20,000:1 or more.
• the non- coordinating compatible anion activator is preferably utilized in an amount to provide a molar ratio of biscyclopentadienyl metal compound to non-coordinating anion of 10:1 to 1:1.
• the above polymerization reaction is conducted by reacting such monomers in the presence of such catalyst system at a temperature of from -
• While the process of the present invention includes utilizing a catalyst system in the liquid phase (slurry, solution, suspension or bulk phase or combination thereof), gas phase polymerization can also be utilized.
• the catalyst systems When utilized in a gas phase, slurry phase or suspension phase polymerization, the catalyst systems will preferably be supported catalyst systems. See, for example, U.S. Patent No. 5,057,475 which is incorporated herein by reference for purposes of U.S. practice.
• Such catalyst systems can also include other well-known additives such as, for example, scavengers. See, for example, U.S. Patent No. 5,153,157 which is incorporated herein by reference for purposes of U.S. practices.
• These processes may be employed without limitation of the type of reaction vessels and the mode of conducting the polymerization.
• the liquid phase process comprises the steps of contacting ethylene and propylene with the catalyst system in a suitable polymeriza- tion diluent and reacting the monomers in the presence of the catalyst system for a time and at a temperature sufficient to produce an ethylene-propylene copolymer of the desired molecular weight and composition.
• Process oil can be optimally added to the polymer blend compositions of the present invention.
• the addition of process oil in moderate amounts lowers the viscosity and flexibility of the blend while improving the properties of the blend at temperatures near and below O ⁇ C. It is believed that these benefits arise by the lowering of the Tg of the blend comprising the mixture of the FPC and the SPC. Additional benefits of adding process oil to the blend of the FPC and the SPC include improved processability and a better balance of elastic and tensile strength are anticipated.
• the process oil is typically known as extender oil in the rubber application practice.
• the process oils can consist of (a) hydrocarbons consisting of essentially of carbon and hydrogen with traces of heteroatoms such as oxygen or (b) essentially of carbon, hydrogen and at least one heteroatom such as dioctyl phthalate, ethers and polyethers.
• the process oils have a boiling point to be substantially involatile at 200°C.
• These process oils are commonly available either as neat solids or liquids or as physically absorbed mixtures of these materials on an inert support (e.g. clays, silica) to form a free flowing powder. We believe that all forms of these process oils are equally applicable to the description and the practice of the invention.
• the process oils usually include a mixture of a large number of chemical compounds which may consist of linear, acyclic but branched, cyclic and aromatic carbonaceous structures.
• Another family of process oils are certain low to medium molecular weight (Molecular weight (M n ) ⁇ 10,000) organic esters and alkyl ether esters.
• M n low to medium molecular weight
• Examples of process oils are Sunpar 150 and 220 from The Sun Manufacturing Company of Marcus Hook, PA, USA and Hyprene ® V750 and
• Hyprene V1200 from Ergon, Post Office Box 1639, Jackson, MS 39215-1639, USA. and IRM 903 from Calumet Lubricants Co., 10234 Highway 157, Princeton, LA 71067-9172, USA. It is also anticipated that combinations of process oils each of which is described above may be used in the practice of the invention. It is important that in the selection of the process oil be compatible or miscible with the polymer blend composition of the FPC and the SPC in the melt to form a homogenous one phase blend. It is also preferred if the process oil is substantially miscible in the SPC at room temperature.
• the addition of the process oils to the mixture comprising the FPC and the SPC maybe made by any of the conventional means known to the art. These include the addition of all or part of the process oil prior to recovery of the polymer as well as addition of the process oil, in whole or in part, to the polymer as a part of a compounding for the interblending of the FPC and the SPC.
• the compounding step may be carried out in a batch mixer such as a mill or an internal mixer such as Banbury mixer.
• the compounding operation may also be conducted in a continuous process such as a twin screw extruder.
• the FPC and SPC physical mixture may include process oil in the range of from 1 to 200, preferably in the range of from 2 to 50 parts by weight of process oil per hundred parts of total polymer (FPC plus SPC).
• the blends of FPC and SPC and other components may be prepared by any procedure that guarantees an intimate mixture of the components.
• the components can be combined by melt pressing the components together on a Carver press to a thickness of 0.5 millimeter (20 mils) and a temperature of 180°C, rolling up the resulting slab, folding the ends together, and repeating the pressing, rolling, and folding operation 10 times.
• Internal mixers are particularly useful for solution or melt blending. Blending at a temperature of 180°C to 240°C in a Brabender Plastograph for 1 to 20 minutes has been found satisfactory.
• Still another method that may be used for admixing the components involves blending the polymers in a Banbury internal mixer above the flux temperature of all of the components, e.g.,
• the polymer blend compositions of the present invention may comprise other additives.
• Various additives may be present to enhance a specific property or may be present as a result of processing of the individual components.
• Additives which may be incorporated include, for example, fire retardants, antioxidants, plasticizers, pigments, vulcanizing or curative agents, vulcanizing or curative accelerators, cure retarders, processing aids, flame retardants, tackifying resins, and the like. These compounds may include fillers and/or reinforcing materials.
• additives which may be employed to enhance properties include antiblocking agents, coloring agent.
• Lubricants, mold release agents, nucleating agents, reinforcements, and fillers may also be employed. Nucleating agents and fillers tend to improve rigidity of the article.
• the list described herein is not intended to be inclusive of all types of additives which may be employed with the present invention. Upon reading this disclosure, those of skill in the art will appreciate other additives may be employed to enhance properties of the composition.
• the polymer blend compositions of the present invention may be modified to adjust the characteristics of the blend as desired.
• the morphology of the blend is shown in Transmission Electron Microscopy of the blends.
• samples were exposed to vapors of 1% aqueous RuO for 3 days.
• the RuO 4 penetrates the amorphous zones of the continuous, less crystalline phase of the polymer while the more crystalline domains composed largely of the FPC are essentially unaffected.
• Within the continuous zone the RuO 4 stained the microzones of amorphous polymer while the lamellae of crystalline polymer are visible by contrast.
• the blend was cryomicrotomed at -196°C to thin sections approximately 0.3 to 3 ⁇ m thick. Several sections were analyzed for each sample until a section was found where the crystalline domains was unstained while the continuous phase was stained to distinguish it from the dispersed phase and to observe the microstructure of the lamellae of polymer.
• the blends of the current invention with good elastic recovery from tensile deformation had a microstructure with clearly dispersed microdomains of the crystalline phase. This is shown in Figure 1.
• the composition and elastic recovery properties of the blend is shown as H7 in the Tables below.
• the domains are elongated with approximate dimensions of 0.2 ⁇ m x 1 ⁇ m.
• Figure 2 shows a different blend of the invention, designated as K7 in the Tables below, with the dispersed phase having dimensions of 0.6 ⁇ m x 2.0 ⁇ m.
• the addition of SPC2 to this blend is shown in the micrograph BB7 ( Figure 3) shows the reduction in the size of the dispersed phase to elongated particles having 0.2 ⁇ m for each dimension. SPC2 is therefore believed to act as an agent for reducing the size of the dispersion of the crystalline phases in the dispersed continuous phase. This is the morphological effect of adding SPC2 to the blend of a FPC and SPC.
• the blends of the current invention have tensile elongation in excess of 700%). This elongation is determined for blends at 20in/min according to the procedure described in ASTM D790. The data is reported in engineering units with no correction to the stress for the lateral contraction in the specimen due to tensile elongation.
• the stress-strain elongation properties of the insitu and the corresponding physical blends was evaluated using dumbbell shaped sample.
• the samples were compression molded at 180° C to 200° C for 15 minutes at a force of 15 tons into a plaque of dimensions of 6 in x 6 in.
• the cooled plaques were removed and the specimens were removed with a die.
• the stress strain evaluation of the samples was conducted on an Instron 4465 tester, made by Instron Corporation of 100 Royall Street, Canton, MA.
• the digital data was collected in a file collected by the Series IX Material Testing System available from Instron Corporation and analyzed using Excel 5, a spreadsheet program available from Microsoft Corporation of Redmond, WA.
• Figure 4 and Figure 5 show the stress strain elongation data for blends containing one FPC and one SPC or two SPC respectively.
• compositions comprising the FPC and the SPC optionally containing SPC2 and/or amounts of process oil can be made which have excellent elastic recovery from tensile deformation.
• These elastic blends have a morphology of containing a crystalline phase dispersed in the continuous crystallizable phase.
• the dispersed crystalline phase contains the majority of the FPC and some of the SPCs due to thermodynamic mixing while the continuous phase consists of the balance of the polymer blend.
• Elastic recovery from tensile deformation is a tension set from 200%) extension of less than 40%, more preferably less than 25% and more preferably less than 15%>.
• compositions of the invention also have a range of tensile strength from 300psi to 5000psi.
• the composition of the invention has a tension set from
• extension equal to or less than 0.02M + 5, preferably equal to or less than
• thermal annealing of the polymer blend is conducted by maintaining the polymer blends or the articles made from a such a blend at temperature between room temperature to a maximum of 160°C or more preferably to a maximum of 130°C for a period between 5 minutes to less than 7 days.
• a typical annealing period is 3 days at 50°C or 5 minutes at 100°C.
• the annealing time and temperature can be adjusted for any particular blend composition comprising a FPC and one or two SPC by experimentation.
• Mechanical orientation can be done by the temporary, forced extension of the polymer blend along one or more axis for a short period of time before it is allowed to relax in the absence of the extensional forces. It is believed that the mechanical orientation of the polymer leads to reorientation of the crystallizable portions of the blend of the first and the second polymer.
• Oriented polymer blends is conducted by maintaining the polymer blends or the articles made from a such a blend at an extension of 10% to 400%) for a period of 0.1 seconds to 24 hours.
• a typical orientation is an extension of 200%> for a momentary period at room temperature.
• the elastic recovery of oriented blends of this invention is shown in Figure 7.
• articles can contain the composition of the invention after the composition has been oriented, and wherein the tension set from 200%) extension equal to or less than 0.011M + 3, preferably equal to or less than 0.0057M
• Annealing and orientation of the blend of the FPC and SPC lead to improvement in the tensile recovery properties of the blend. This is shown in the data in Tables below where the tension set recovery values for the blends described in the invention are described for the blends as made, after annealing and after orientation as described in the procedures above. The data show that the elastic recovery properties are enhanced.
• compositions comprising the FPC and the SPC containing optional amounts of process oil can be made which have low flexural modulus.
• These blends have a crystalline phase dispersed in the continuous crystallizable phase.
• the crystalline phase contains the majority of the FPC and some of the SPCs due to thermodynamic mixing while the continuous phase consists of the balance of the polymer blend.
• Low flexural modulus is a 1% secant modulus less than 60 kpsi in/in, more preferably less than 30 kpsi in/in and more preferably less than 15 kpsi in/in
• flexural modulus of the blend is judged on two criteria: (a) extensibility to 500%) elongation with a measurable modulus and (b) 1% secant flexural modulus. Comparative blends often cannot be extended to 500%) extension for evaluation of the 500%) modulus and thus cannot be compared to the blends of the current invention.
• the flexible blends of the current invention fulfill both of these conditions. Generally for all blends the flexural modulus deteriorates with increase in the 500%) tensile modulus. Thus flexural modulus is judged relative to the tensile modulus of the blend for a 500%) extension.
• the blends of the current invention have a lower flexural modulus, as indicated by low tension set, than blends of the comparative blends at comparable 500%) tensile modulus. These properties are available over a wide range of composition and relative amounts of the FPC and the SPC. In the examples shown below we show examples of numerous blends of composition of the FPC and the SPC which have the above favorable combination of properties. The dependence of the flexural modulus of the blend of this invention as a correlated function of the 500%) tensile modulus is shown Figure 8.
• the composition of the invention has a flexural modulus in kpsi.in/in equal to or less than 0.013M -1.3, preferably equal to or less than 0.0083M-1.6, more preferably equal to or less than 0.0062M -2.5 wherein M is
• articles can contain the composition of the invention after the composition has been oriented, and wherein the flexural modulus in kpsi.in/in equal to or less than 0.013M -1.3, preferably equal to or less than 0.0083M-1.6, more preferably equal to or less than 0.0062M -2.5 wherein M is
• Mooney Viscosity was measured as ML (1+4) at 125°C in
• composition of the second polymer component was measured as ethylene Wt. %> according to the following technique.
• a thin homogeneous film of the second polymer component, pressed at a temperature of or greater than 150°C was mounted on a Perkin Elmer PE 1760 infra red spectrophotometer.
• a full spectrum of the sample from 600 cm-1 to 400 cm-1 was recorded and the ethylene
• Mn and Mw molecular weight
• Mw molecular weight distribution
• MWD molecular weight distribution
• Composition distribution of the second polymer component was measured by the thermal fractionation as described below. About 30 gms of the second polymer component was cut into small cubes about 1/8" on the side. This is introduced into a thick walled glass bottle closed with screw cap along with 50 mg of Irganoxl076, an antioxidant commercially available from Ciba - Geigy Corporation. Then, 425 ml of hexane (a principal mixture of normal and isomers) is added to the contents of the bottle and the sealed bottle is maintained at about 23°C for 24 hours. At the end of this period, the solution is decanted and the residue is treated with additional hexane for an additional 24 hours.
• hexane a principal mixture of normal and isomers
• the two hexane solutions are combined and evaporated to yield a residue of the polymer soluble at 23°C.
• To the residue is added sufficient hexane to bring the volume to 425 ml and the bottle is maintained at about 31°C for 24 hours in a covered circulating water bath.
• the soluble polymer is decanted and the additional amount of hexane is added for another 24 hours at about 31°C prior to decanting.
• fractions of the second polymer component soluble at 40°C, 48°C, 55°C and 62°C are obtained at temperature increases of approximately 8°C between stages.
• Blends were made by mixing a total of 72g of all components, including the first polymer component, the second polymer component, the optional amounts of process oil and other ingredients in a Brabender intensive mixture for 3 minutes at a temperature controlled to be within 185°C and 220°C.
• High shear roller blades were used for the mixing and approximately 0.4g of Irganox-1076, an antioxidant available from the Novartis Corporation, was added to the blend.
• the mixture was removed and pressed out into a 6" x 6" mold into a pad 025" thick at 215°C for 3 to 5 minutes. At the end of this period, the pad was cooled and removed and allowed to anneal for 1 day.
• Test specimens of the required dumbbell geometry were removed from this pad and evaluated on an Instron 4465 tester equipped with Instron Series IX Software for Windows to produce the mechanical deformation data.
• the Instron Tester and associated equipment is available form The Instron Corporation in Canton, MA.
• the testing was done at a travel rate of 20 " /min and all data is reported in engineering stress and strain term with values of the stress uncorrected for the contraction in the cross section of the sample being tested.
• Samples were aged by allowing them to stand at room temperature prior to testing. Samples were aged for 5, 10, 15, 20 and 25 days prior to testing on the Instron. Significant difference in the tensile strength and tension set were observed between samples aged 1 days versus those aged for 5 or more days.
• Tset 100*(L2-Ll)/Ll Flexural modulus was determined for samples of the blend by ASTM procedure D790 at room temperature.
• the polymerization catalyst dimethyl silyl bridged bis-indenyl Hafnium dimethyl activated 1:1 molar ratio with N', N'- Dimethyl anilinium-tetrakis(pentafluorophenyl)borate was introduced at the rate of at 0.0135 g/hr.
• a dilute solution of triisobutyl aluminum was introduced into the reactor as a scavenger of catalyst terminators: a rate of approximately 111 mole of scavenger per mole of catalyst was adequate for this polymerization. After five residence times of steady polymerization, a representative sample of the polymer produced in this polymerization was collected.
• the solution of the polymer was withdrawn from the top, and then steam distilled to isolate the polymer.
• the polymerization rate was measured at 3.7 Kg/hr.
• the polymer produced in this polymerization had an ethylene content of 14%, ML (1+4) 125C of 13.1 and had isotactic propylene sequences.
• Variations in the composition of the polymer were obtained principally by changing the ratio of ethylene to propylene.
• Molecular weight of the polymer was varied by either changing the reactor temperature or by changing the ratio of total monomer feed rate to the polymerization rate.
• Dienes for terpolymerization were added to the mixed feed stream entering the reactor by preparing the diene in a hexane solution and metering it in the required volumetric amount.
• Example 2 Comparative ethylene/propylene polymerization where the propylene residues are atactic. Polymerizations were conducted in a 1 liter thermostated continuous feed stirred tank reactor using hexane as the solvent. The polymerization reactor was full of liquid.
• the residence time in the reactor was typically 7 - 9 minutes and the pressure was maintained at 400kpa.
• Hexane, ethene and propene were metered into a single stream and cooled before introduction into the bottom of the reactor. Solutions of all reactants and polymerization catalysts were introduced continuously into the reactor to initiate the exothermic polymerization. Temperature of the reactor was maintained at 45 °C by changing the temperature of the hexane feed and by using cooling water in the external reactor jacket. For a typical polymerization, the temperature of feed was about -10°C. Ethene was introduced at the rate of 45 gms/min and propene was introduced at the rate of 310 gms/min.
• the polymerization catalyst dimethyl silyl bridged (tetramethylcyclopentadienyl) cyclododecylamido titanium dimethyl activated 1:1 molar ratio with N', N'- Dimethyl anilinium-tetrakis(pentafluorophenyl)borate was introduced at the rate of 0.002780 gms/hr.
• a dilute solution of triisobutyl aluminum was introduced into the reactor as a scavenger of catalyst terminators: a rate of approximately 36.8 mole per mole of catalyst was adequate for this polymerization. After five residence times of steady polymerization, a representative sample of the polymer produced in this polymerization was collected.
• the solution of the polymer was withdrawn from the top, and then steam distilled to isolate the polymer.
• the rate of formation of the polymer was 258 gms/hr.
• the polymer produced in this polymerization had an ethylene content of 14.1 wt. %, ML@125 (1+4) of 95.4. Variations in the composition of the polymer were obtained principally by changing the ratio of ethene to propene. Molecular weight of the polymer could be increased by a greater amount of ethene and propene compared to the amount of the polymerization catalyst. These polymers are described as aePP in the Tables below.
• Example 1 In the manner described in Example 1 above, several second polymer components of the above specification were synthesized. These are described in the table below. Table 1 describes the results of the GPC, composition, ML and DSC analysis for the polymers.
• Table 1 Analysis of the second polymer component and the comparative polymers Table 2 describes the solubility of the second polymer component
• Table 3 describes the composition of the fractions of the second polymer component obtained in Table 2. Only fractions which have more than 4%> of the total mass of the polymer have been analyzed for composition.
• Table 3 Composition of fractions of the second polymer component obtained in Table 2. The experimental inaccuracy in determination of the ethylene content is believed to about 0.4 wt. %> absolute.
• Blends were made in all composition of Table 4 according to the procedure described above.
• Blends of a First Polymeric Component, Escorene 4292, a homoisotactic poh-propylene available from Exxon Chemical Co., Houston TX and one Second Polymeric component (identified as SPCl in Table 4) were made using the procedure as described above The blends were made in a different composition range as shown by the table above. All of the compositions are within have the properties of this invention. Properties of the blend were measured as molded.
• blends of a First Polymeric Component, Escorene 4292, a homoisotactic polypropylene available from Exxon Chemical Co., Houston TX and two Second Polymeric component (identified as SPCl and SPC2 in Table 5) were made using the procedure as described above.
• the SPC2 has a ML(1+4)@125 of 14 and an ethylene content of 7.3 wt. %>.
• the composition and the ML of the SPCl are indicated in the Table for the various SPCl used.
• the blends were made in a different composition range as shown by the table above. All of the compositions are within have the properties of this invention. Properties of the blend were measured as molded.
• Table 6 Hysteresis and Tension set for Binary Blends of one FPC and one SPC and Ternary Blend of one FPC and two SPC described in Table 4 and 5 as (1) new, (2) after annealing at room temperature for 21 days and (3) after momentary orientation to 200%.
• Blends were made in all composition of Table 7 according to the procedure described above.
• blends of a First Polymeric Component, Escorene 9272, a reactor copolymer available from Exxon Chemical Co., Houston TX having an ethylene content of 5 wt %> and 2.9 MFR and two Second Polymeric component (identified as SPCl and SPC2 in Table 7) were made using the procedure as described above.
• the SPCl has a ML(1+4)@125 of 11 and an ethylene content of 14.5 wt %.
• the SPC2 has a ML(1+4)@125 of 21 and an ethylene content of 5.8 wt %.
• the blends were made in a different composition range as shown by the table above. All of the compositions are within have the properties of this invention. Properties of the blend were measured as molded.
• Table 8 Hysteresis and Tension set for Binary Blends of one FPC and one SPC and Ternary Blend of one FPC and two SPC described in Table 7 as (1) new, (2) after annealing at room temperature for 21 days and (3) after momentary orientation to
• Blends were made in all composition of Table 7 according to the procedure described above.
• blends of a First Polymeric Component, Escorene 7132, a impact copolymer available from Exxon Chemical Co., Houston TX having an ethylene content of 9 wt %> and 2.0 MFR and two Second Polymeric component (identified as SPCl and SPC2 in Table 7) were made using the procedure as described above.
• the SPCl has a ML(1+4)@125 of 11 and an ethylene content of 14.5 wt %.
• the SPC2 has a ML(1+4)@125 of 21 and an ethylene content of 5.8 wt %>.
• the blends were made in a different composition range as shown by the table above. All of the compositions are within have the properties of this invention. Properties of the blend were measured as molded.
• Table 10 Hysteresis and Tension set for Binary Blends of one FPC and one SPC and Ternary Blend of one FPC and two SPC described in Table 9 as (1) new, (2) after annealing at room temperature for 21 days and (3) after momentary orientation to 200%.
• Blends were made in all composition of Table 11 according to the procedure described above.
• blends of a First Polymeric Component, Escorene 4292, a isotactic homopolymer available from Exxon Chemical Co., Houston TX having 0.9 MFR and two Second Polymeric component (identified as SPCl and SPC2 in Table 7) were made using the procedure as described above.
• the SPCl has a ML(1+4)@125 of 11 and an ethylene content of 14.5 wt %.
• the SPC2 has a ML(1+4)@125 of 21 and an ethylene content of 5.8 wt %.
• Sunpar 150 is a process oil available from Sun Refining Company.
• the blends were made in a different composition range as shown by the table above. All of the compositions are within have the properties of this invention. Properties of the blend were measured as molded.
• Table 12 Hysteresis and Tension set for Ternary Blend of one FPC and two SPC and a process oil described in Table 11 as (1) new, (2) after annealing at room temperature for 21 days and (3) after momentary orientation to 200%.

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