PRIORITY CLAIM

This application claims priority to and the benefit of U.S. Ser. No. 62/431,593, filed Dec. 8, 2016 and is incorporated by reference in its entirety.

FIELD OF THE INVENTION

The present invention relates to polypropylene-based thermoplastic polyolefin compositions having improved impact properties.

BACKGROUND OF THE INVENTION

Polypropylene-based Thermoplastic Olefin Compositions (TPO) are blends of polypropylene, an elastomer, optional propylene-based elastomers, and optional non-polymeric components such as fillers and other compounding ingredients. Included in the category of TPO compositions are so called impact copolymers (“ICP”) compositions, typically non-cured. Typically, TPOs are multiphase polymer blends where a polypropylene forms a continuous matrix phase and the elastomer component, generally derived from an ethylene containing interpolymer, is the dispersed component. The polypropylene matrix imparts tensile strength and chemical resistance to the TPO, while the ethylene polymer imparts flexibility and impact resistance. Typically, ICPs and TPOs have a dispersed phase which is not, or only modestly, cross-linked.

It has been observed that certain non-cross-linked TPO compositions have improved processability, and also improved mechanical properties, when the compositions contain high levels of isotactic polypropylene, for example, above 70 wt %. Generally, one of the problems with adding more isotactic polypropylene to any thermoplastic composition is a noticeable drop in ductility. For example, any improvement in a mechanical or impact property, such as Notched Izod, tends to be accompanied by an undesirably high loss of flexibility, for example, flexural modulus. Such a trade-off is of great concern for the makers of automotive parts, particularly car bumpers. Certain compositions described above provide a combination of (a) high Notched Izod together with (b) high flexural modulus. In addition to having superior mechanical properties, the compositions also have desirable molding properties, for example, sufficiently high MFR, without losing their superior impact strength and flexibility.

Traditionally, very low density ethylene-propylene copolymers and ethylene-propylene-diene terpolymers have been used as the modifier component in TPO compositions. These EP or EPDMs generally have a high molecular weight expressed in Mooney units. Recently, other ethylene-alpha olefin copolymers have been used, especially very low density ethylene-butene, ethylene-hexene and ethylene-octene copolymers which generally have a lower molecular weight expressed in Melt Index units. The density of these latter polymers is generally less than 0.900 g/cm³, indicative of only minimal residual crystallinity in the polymer. The major market for TPOs is in the manufacture of automotive parts, especially bumper fascia. Other applications include automotive interior components such as door skin, air bag cover, side pillars and the like. These parts are generally made using an injection molding process. To increase efficiency and reduce costs it is necessary to decrease molding times and reduce wall thickness in the molds. To accomplish these goals, manufacturers have turned to high melt flow polypropylenes (for example, Melt Flow Rates greater than about 35 g/10 min). These high melt flow rate (MFR) resins are low in molecular weight and consequently difficult to toughen, resulting in products that have low impact strength.

There is a need therefore for TPO manufacturers to be able to broaden the scope of polymers available to manufacture end use items with a better balance between the performance of the hetero phase composition in its end use, the processability during conversion of the molten compositions into the end use article and the cost of providing those properties.

References of interest include U.S. Pat. No. 6,245,856; U.S. Pat. No. 6,288,171; U.S. Pat. No. 6,232,402; U.S. Pat. No. 5,959,030; US 2009/053959; WO 97/20888; US 2015/0025209, EP 0 792 914, and WO 16/057124.

SUMMARY OF THE INVENTION

Disclosed herein is a thermoplastic polyolefin composition comprising a polypropylene having a melting point temperature (T_m) of greater than 130° C. and a melt flow rate (230° C./2.16 kg) within the range from 10 g/10 min to 80 g/10 min; an ethylene-propylene copolymer comprising within the range from 40 wt % to 80 wt % ethylene derived units and having a Mooney Viscosity (1+4, 125° C.) of greater than about 20 Mooney units, a Mw/Mn within the range from 1.8 to 4.0, and a weight average molecular weight (Mw) within a range of from 50,000 g/mole to 300,000 g/mole; and a propylene-based elastomer having within the range from 5 to 25 wt % ethylene derived units and having a melting point temperature (T_m) of less than 110° C. and a Mw/Mn within the range from 2.0 to 4.0; wherein the room temperature notch impact of the thermoplastic polyolefin composition is at least four times greater than the room temperature notch impact of a composition without the propylene-based elastomer.

It has been found surprisingly that use of low MFR propylene-based elastomers in the inventive compositions leads to unanticipated increase in the room temperature toughness of the blend.

DETAILED DESCRIPTION

Disclosed is a propylene-based TPO comprising at least polypropylene, an ethylene-propylene copolymer, and an inventive propylene-based elastomer. More particularly, the propylene-based TPO is a thermoplastic polyolefin composition comprising (or consisting essentially of) three different components, each of which may be a blend of two or more of the similar polymer compositions: a polypropylene having a melting point temperature (T_m) of greater than 130° C. and a melt flow rate (230° C./2.16 kg) within the range from 10 to 200 g/10 min; an ethylene-propylene copolymer comprising within the range from 30 40 to 80 wt % ethylene derived units and having a melt flow rate (230° C./2.16 kg) within the range from 0.1 to 20 g/10 min; and a propylene-based elastomer having within the range from 5 to 25 wt % ethylene derived units and having a melting point temperature (T_m) of less than 110° C.

The composition is preferably a non-cured blend, but, as described the claimed TPO compositions and those described herein are the melt-blend product (or “cooled” melt-blend, such that the polymers have been melted to the temperature of the highest melting component, at least, and intimately blended, then allowed to cool to form the composition) of the at least three different polymer components (polypropylene, ethylene-propylene copolymer, and propylene-based elastomer). Preferably, the polypropylene is present within a range of from 50 wt % to 90 wt %; and the ethylene-propylene copolymer is present within a range from 10 wt % to 40 wt %; and wherein the propylene-based elastomer is present to within a range from 1.0 wt % to 10 wt %, each based on the weight of all ingredients of the composition. Most preferably, from 55 wt % to 75 wt %, by weight of the composition, is the polypropylene and from 0.1 wt % to 5 wt %, by weight of the composition, is the propylene-based elastomer, the remainder of the composition being the ethylene-propylene elastomer and any common additives as is known in the art. There may be some chemical “reaction” between the primary components, but most likely there is only a physical change in the formation of a “continuous” phase primarily of polypropylene and a “discontinuous” phase or “discrete” phase comprising mostly the ethylene-propylene copolymer. The three primary components are described here.

Ethylene-Propylene Copolymer

The ethylene-propylene copolymer may be a single polymer composition or may in fact be comprised of a blend of two or more ethylene-propylene copolymers that have properties within the defined region of parameters described herein, and in any case have an aggregate density less than 0.900 g/cm³. For instance, if two or more ethylene α-olefin polymers are combined to form the ethylene-propylene copolymer, they may be the same or different in their selection of comonomers and/or the amount of comonomer or comonomer amounts and/or densities, but overall, as a blend fall within with the claimed range of parameter(s).

The added polymer (one differing in density and or amount or type of comonomer from the copolymer described above) may be one generally used conventionally as modifier in TPOs, and as such may be generally lower in density than the first polymer described above. The amounts of such added or second polymer depend on the balance of effects desired. Generally lower density polymer may enhance properties such as impact strength. Such polymers of lower density include, but are not limited to polymers of having a density of less than 0.900, or 0.895, or 0.890, or 0.885, and/or 0.860, or 0.865 g/cm³.

The ethylene-propylene copolymers (either a single polymer or blends) may be present in the composition as a disperse phase in a continuous phase of the polypropylene component. Thus, the amount of EP copolymer component should not exceed that needed to maintain its dispersed condition in the polypropylene component continuous phase. When such an upper limit is reached, (the upper boundary of maintaining a dispersed condition) additional amounts of ethylene-propylene copolymer will tend to result in the copolymer becoming a so-called “co-continuous phase” in which discrete, dispersed phase islands will coalesce into larger islands. This co-continuous state may be detrimental to physical properties, as the flexural modulus is lowered. To mitigate such effects, if larger amounts of EP copolymer are desired or required, a full or partial cross-linking can be elected. This full or partial cross-linking may decrease the tendency to co-continuity. Such cross-linking can be effected by chemical means (peroxide or sulfur or silane, azides, etc.) or by non-chemical means such as electron beam radiation. But preferably the TPO compositions described herein are not cross-linked, meaning that no agent is purposefully added that would effectuate a covalent linking between polymer chains or within the same polymer chain.

The sizes of the individual domains of the dispersed phase are generally small, with the smallest length dimension for the dispersed phase being less than 10 μm. This phase size of the dispersed phase may be maintained during processing even without cross-linking. The disperse phase is comprised of a mixture of the ethylene-propylene copolymer with some amount of the polypropylene component, due to thermodynamic mixing of polymers. The balance of the polymers not in this disperse phase makes up the continuous phase.

The one or more copolymers that make up the ethylene-propylene copolymer may be substantially free of propylene crystallinity, by which we intend <10 or <5 or <1 or 0 percent of propylene crystallinity is in the modifier component as determined by Differential Scanning calorimetry (DSC). The one or more ethylene-propylene copolymers may include C3 olefin derived units, in addition C4 to C20 derived units, and optionally the copolymers may contain diene derived units. Such combinations of ethylene and propylene as described above include, but are not limited to, copolymers such as ethylene-propylene; ethylene-propylene-butene-1; ethylene-propylene hexene-1; ethylene-propylene-pentene-1; ethylene-propylene-octene-1; and the like may be used as the polyethylene portion of the hetero phase polymer composition. The one or more α-olefin derived units may be present in the ethylene copolymer in an amount of greater than 30 mole percent based on the copolymer, or greater than 40 mole percent, or greater than 50 mole percent. If the optional diene is present, it may range from 0.5 wt % to 10 wt %, or from 0.5 wt % to 7 wt % (based on FTIR determination). The ethylene content of the copolymer may generally range from 30 wt % to 65 wt %, or at most 40 wt % to 60 wt % or more.

The copolymer generally may have a number average molecular weight of from 30,000 to 500,000 or may be greater than 50,000 and/or less than 100,000 g/mole. The Melt Index may be from 0.03 to 20 g/10 minutes. The copolymer may have a CDBI of at least 50%, or at least 60% or even 65% and a weight average molecular weight distribution of from 1.5 to 4.0, or at least 1.8 and/or less than 3.0. This homogeneity and molecular weight and compositional distribution, as indicated by the CDBI, reflects a reduction in the presence of lower molecular weight, and higher comonomer content impurities.

More particularly, the ethylene-propylene copolymer comprises within the range from 30 to 35 to 40, or 45 wt % to 55, or 60, or 65, or 80 wt % ethylene derived units, and has a melt flow rate (230° C./2.16 kg) within the range from 0.03, or 0.1, or 1, or 5 g/10 min to 8, or 10, or 12, or 20 g/10 min, a Mw/Mn within the range from 1.8, or 2.0 to 2.8, or 3.0, or 4.0, and a weight average molecular weight (Mw) within a range of from 50,000, or 60,000 g/mole to 120,000, or 200,000, or 300,000 g/mole. Also, most preferably, the ethylene-propylene copolymer has a melting point temperature (T_m) of less than 80 or 100° C. (first melt); preferably within a range of from −50, or −40, or −30, or −20° C. to 20, or 40, or 50, or 60° C. Also, most preferably the ethylene-propylene copolymer has a heat of fusion (H_f) of less than 40, or 50 J/g (first melt); preferably within a range of from 0 or 10, or 20 J/g to 40, or 50, or 60, or 70 J/g. Further, the ethylene-propylene copolymer most preferably has a glass transition temperature (T_g) within a range of from −80, or −60, or −50° C. to −30, or −20, or −10° C.

Such polymer can be produced using metallocene based catalyst or other single site catalysts systems in gas phase or solution processes. The metallocene based catalysts used for such polymerizations are generally of the metallocene-alumoxane, metallocene-ionizing activator type. Useful catalysts are those disclosed in EP 0 129 368; U.S. Pat. No. 5,026,798; and U.S. Pat. No. 5,198,401, each incorporated herein by reference. Most preferably, the ethylene-propylene copolymer is formed by a polymerization reaction between ethylene, an amount of comonomer selected from one or more of propylene, butylene, hexene and octene, and a bridged hafnocene or zirconocene, most preferably a bridged, unbalanced hafnocene or zirconocene. By “unbalanced” what is meant is that the two primary cyclopentadienyl ligands, or ligand isolobal to cyclopentadienyl, are not the same, such as a cyclopentadienyl-fluorenyl hafnocene or zirconocene, or a indenyl-fluorenyl hafnocene or zirconocene, etc.

The copolymer may or may not contain long chain branches, whose presence may be inferred from rheology type measurements such as melt tension and the internal energy of activation for melt flow. The ethylene-propylene copolymer may comprise polymers derived from cyclic mono-olefins such as styrene and both linear and cyclic dienes can also be used. For a discussion of such dienes, U.S. Pat. No. 6,245,846 is incorporated by reference. The ethylene-propylene copolymer can be linear, substantially linear, blocky or branched. For a discussion of such options, U.S. Pat. No. 6,245,846, which is incorporated by reference. Suitable ethylene-propylene copolymers for use in the invention include Vistalon™ ethylene-propylene-diene rubbers, commercially available from ExxonMobil Chemical Company.

Propylene-Based Elastomer

The polymer blends used to form the TPOs described herein comprise one or more propylene-based elastomers (“PBEs”). The PBE comprises propylene and from 5 to 25 wt % of one or more comonomers selected from ethylene and/or C₄-C₁₂α-olefins. The α-olefin comonomer units may be derived from ethylene, butene, pentene, hexene, 4-methyl-1-pentene, octene, or decene. In preferred embodiments the α-olefin is ethylene. In some embodiments, the propylene-based polymer composition consists essentially of propylene and ethylene, or consists only of propylene and ethylene. The embodiments described below are discussed with reference to ethylene as the α-olefin comonomer, but the embodiments are equally applicable to other copolymers with other α-olefin comonomers. In this regard, the copolymers may simply be referred to as propylene-based polymers with reference to ethylene as the α-olefin.

The PBE may include at least 5 wt %, at least 6 wt %, at least 7 wt %, or at least 8 wt %, or at least 9 wt %, or at least 10 wt %, or at least 12 wt % ethylene-derived units, where the percentage by weight is based upon the total weight of the propylene-derived and ethylene-derived units. The PBE may include up to 30 wt %, or up to 25 wt %, or up to 22 wt %, or up to 20 wt %, or up to 19 wt %, or up to 18 wt %, or up to 17 wt % ethylene-derived units, where the percentage by weight is based upon the total weight of the propylene-derived and ethylene-derived units. In some embodiments, the PBE may comprise from 5 wt % to 25 wt % ethylene-derived units, or from 7 wt % to 20 wt % ethylene, or from 9 wt % to 18 wt % ethylene-derived units, where the percentage by weight is based upon the total weight of the propylene-derived and ethylene-derived units.

The PBE may include at least 70 wt %, or at least 75 wt %, or at least 80 wt %, or at least 81 wt % propylene-derived units, or at least 82 wt %, or at least 83 wt % propylene-derived units, where the percentage by weight is based upon the total weight of the propylene-derived and α-olefin derived units. The PBE may include up to 95 wt %, or up to 94 wt %, or up to 93 wt %, or up to 92 wt %, or up to 90 wt %, or up to 88 wt % propylene-derived units, where the percentage by weight is based upon the total weight of the propylene-derived and α-olefin derived units.

The T_mof the PBE (as determined by DSC) may be less than 115° C., or less than 110° C., or less than 100° C., or less than 95° C., or less than 90° C. In some embodiments, the PBE may have two melting peaks as determined by DSC, as described in the subsequent paragraphs. In other embodiments, the PBE may have a single melting peak, where the first melt and second melt (described in the subsequent paragraph) are the same.

The PBE may be characterized by its heat of fusion (Hf), as determined by DSC. The PBE may have an Hf that is at least 0.5 J/g, or at least 1.0 J/g, or at least 1.5 J/g, or at least 3.0 J/g, or at least 4.0 J/g, or at least 5.0 J/g, or at least 6.0 J/g, or at least 7.0 J/g. The PBE may be characterized by an Hf of less than 75 J/g, or less than 70 J/g, or less than 60 J/g, or less than 50 J/g, or less than 45 J/g, or less than 40 J/g, or less than 35 J/g, or less than 30 J/g, or less than 25 J/g.

The DSC procedures for determining T_mand Hf of the PBE include the following. The polymer is pressed at a temperature of from 200° C. to 230° C. in a heated press, and the resulting polymer sheet is hung at ambient temperature of 20-23.5° C. in the air to cool. 6 to 10 mg of the polymer sheet is removed with a punch die. This 6 to 10 mg sample is annealed at room temperature (22° C.) for 80 to 100 hours. At the end of this period, the sample is placed in a DSC (Perkin Elmer Pyris One Thermal Analysis System) and cooled at a rate of about 10° C./min to −30° C. to −50° C. and held for 10 minutes at −50° C. The sample is heated at 10° C./min to attain a final temperature of 200° C. The sample is kept at 200° C. for 5 minutes. Then a second cool-heat cycle is performed, using the same conditions described above. Events from both cycles, “first melt” and “second melt”, respectively, are recorded. The thermal output is recorded as the area under the melting peak of the sample, which typically occurs between 0° C. and 200° C. It is measured in Joules and is a measure of the Hf of the polymer. Reference to melting point temperature herein refers to the first melt.

Preferably, the propylene-based elastomer has within the range from 12 wt % to 20 wt % ethylene derived units and having a melting point temperature (T_m) of less than 110° C. Most preferably, the propylene-based elastomer has a melting point temperature (T_m) within the range of from 80° C., or 90° C. to 110° C. (first melt).

The PBE can have a triad tacticity of three propylene units (mmm tacticity), as measured by 13C NMR, of 75% or greater, 80% or greater, 85% or greater, 90% or greater, 92% or greater, 95% or greater, or 97% or greater. In one or more embodiments, the triad tacticity may range from 75% to 99%, or from 80% to 99%, or from 85% to 99%, or from 90% to 99%, or from 90% to 97%, or from 80% to 97%. Triad tacticity is determined by the methods described in U.S. Pat. No. 7,232,871. The PBE may have a tacticity index m/r ranging from a lower limit of 4 or 6 to an upper limit of 8 or 10 or 12.

The PBE may have a % crystallinity of from 0.5% to 40%, or from 1% to 30%, or from 5% to 25%, determined according to DSC procedures.

The PBE may have a density of from 0.85 g/cm³to 0.92 g/cm³, or from 0.86 g/cm³to 0.90 g/cm³, or from 0.86 g/cm³to 0.89 g/cm³at 22° C., as measured per the ASTM D-792 test method.

The PBE can have a melt index (MI) (ASTM D-1238, 2.16 kg at 190° C.), of less than or equal to 100 g/10 min, or less than or equal to 50 g/10 min, or less than or equal to 25 g/10 min, or less than or equal to 10 g/10 min, or less than or equal to 9.0 g/10 min, or less than or equal to 8.0 g/10 min, or less than or equal to 7.0 g/10 min.

The PBE may have a melt flow rate (MFR), as measured according to ASTM D-1238 (2.16 kg weight at 230° C.), greater than 0.3 g/10 min or 1 g/10 min, or greater than 2 g/10 min, or greater than 5 g/10 min, or greater than 8 g/10 min, or greater than 10 g/10 min. The PBE may have an MFR less than 1,000 g/10 min, or less than 750 g/10 min, or less than 500 g/10 min, or less than 400 g/10 min, or less than 300 g/10 min, or less than 200 g/10 min, or less than 100 g/10 min, or less than 75 g/10 min, or less than 50 g/10 min. In some embodiments, the PBE may have an MFR from 1 to 100 g/10 min, or from 2 to 75 g/10 min, or from 5 to 50 g/10 min.

In some embodiments, the PBE may be a reactor grade polymer, as defined above. In other embodiments, the PBE may be a polymer that has been visbroken after exiting the reactor to increase the MFR.

Molecular weight (weight-average molecular weight, M_w, number-average molecular weight, M_n, and molecular weight distribution, M_w/M_nor MWD) was determined using a High Temperature Size Exclusion Chromatograph (either from Waters Corporation or Polymer Laboratories), equipped with a differential refractive index detector (DRI), an online light scattering (LS) detector, and a viscometer.

Three Polymer Laboratories PLgel 10 mm Mixed-B columns were used. The nominal flow rate was 0.5 cm³/min, and the nominal injection volume was 300 μL. The various transfer lines, columns and differential refractometer (the DRI detector) were contained in an oven maintained at 145° C.

Solvent for the SEC experiment is prepared by dissolving 6 g of butylated hydroxy toluene as an antioxidant in 4 L of Aldrich reagent grade 1,2,4 trichlorobenzene (TCB). The TCB mixture is then filtered through a 0.7 μm glass pre-filter and subsequently through a 0.1 μm Teflon filter. The TCB is then degassed with an online degasser before entering the SEC. Polymer solutions are prepared by placing the dry polymer in a glass container, adding the desired amount of TCB, then heating the mixture at 160° C. with continuous agitation for about 2 hr. All quantities are measured gravimetrically. The TCB densities used to express the polymer concentration in mass/volume units are 1.463 g/mL at room temperature and 1.324 g/mL at 135° C. The injection concentration ranges from 1.0 to 2.0 mg/mL, with lower concentrations being used for higher molecular weight samples. Prior to running each sample the DRI detector and the injector are purged. Flow rate in the apparatus is then increased to 0.5 mL/min, and the DRI was allowed to stabilize for 8-9 hr before injecting the first sample. The LS laser is turned on 1 to 1.5 hr before running samples.

The concentration, c, at each point in the chromatogram is calculated from the baseline-subtracted DRI signal, I_DRI, using the following equation:

c=K_DRII_DRI/(dn/dc),

where K_DRIis a constant determined by calibrating the DRI, and dn/dc is the same as described below for the LS analysis. Units on parameters throughout this description of the SEC method are such that concentration is expressed in g/cm³, molecular weight is expressed in kg/mol, and intrinsic viscosity is expressed in dL/g.

The light scattering detector used is a Wyatt Technology High Temperature mini-DAWN. The polymer molecular weight, M, at each point in the chromatogram is determined by analyzing the LS output using the Zimm model for static light scattering (M. B. Huglin, Light Scattering from Polymer Solutions, Academic Press, 1971):

[K₀c/ΔR(θ,c)]=[1/MP(θ)]+2A₂c,

where ΔR(θ) is the measured excess Rayleigh scattering intensity at scattering angle θ, c is the polymer concentration determined from the DRI analysis, A₂is the second virial coefficient, P(θ) is the form factor for a monodisperse random coil (described in the above reference), and K₀is the optical constant for the system:

K
o

=

4




π
2



n
2



(

dn
/
d




c

)

2

λ
4



N
A

,

in which N_Ais the Avogadro's number, and dn/dc is the refractive index increment for the system. The refractive index, n=1.500 for TCB at 135° C. and λ=690 nm. In addition, A₂=0.0015 and dn/dc=0.104 for ethylene polymers, whereas A₂=0.0006 and dn/dc=0.104 for propylene polymers.

The molecular weight averages are usually defined by considering the discontinuous nature of the distribution in which the macromolecules exist in discrete fractions i containing N_imolecules of molecular weight M_i. The weight-average molecular weight, M_w, is defined as the sum of the products of the molecular weight M_iof each fraction multiplied by its weight fraction w_i:

M_w≡Σw_iM_i=(ΣN_iM_i²/ΣN_iM_i),

since the weight fraction w_iis defined as the weight of molecules of molecular weight M_idivided by the total weight of all the molecules present:

w_i=N_iM_i/ΣN_iM_i

The number-average molecular weight, M_n, is defined as the sum of the products of the molecular weight M_iof each fraction multiplied by its mole fraction x_i:

M_n≡Σx_iM_i=ΣN_iM_i/ΣN_i,

since the mole fraction x_iis defined as N_idivided by the total number of molecules:

x_i=N_i/ΣN_i

In the SEC, a high temperature Viscotek Corporation viscometer is used, which has four capillaries arranged in a Wheatstone Bridge configuration with two pressure transducers. One transducer measures the total pressure drop across the detector, and the other, positioned between the two sides of the bridge, measures a differential pressure. The specific viscosity, η_S, for the solution flowing through the viscometer is calculated from their outputs. The intrinsic viscosity, [η], at each point in the chromatogram is calculated from the following equation:

η_S=c[η]+0.3(c[η])²,

where c was determined from the DRI output.

The branching index (g′, also referred to as g′(vis)) is calculated using the output of the SEC-DRI-LS-VIS method as follows. The average intrinsic viscosity, [η]_avg, of the sample is calculated by:

[
η
]

avg

=

∑



c
i



[
η
]

i

∑



c
i

,

where the summations are over the chromatographic slices, i, between the integration limits.

The branching index g′ is defined as:

g
′

=

[
η
]

avg

kM
v
α

,

where k=0.000579 and α=0.695 for ethylene polymers; k=0.0002288 and α=0.705 for propylene polymers; and k=0.00018 and α=0.7 for butene polymers.

The PBE may have a g′ index value of 0.95 or greater, or at least 0.97, or at least 0.99, wherein g′ is measured at the Mw of the polymer using the intrinsic viscosity of isotactic polypropylene as the baseline.

The PBE may have a weight average molecular weight (Mw) of from 50,000 to 5,000,000 g/mol, or from 75,000 to 1,000,000 g/mol, or from 100,000 to 500,000 g/mol, or from 125,000 to 300,000 g/mol. Most preferably, the weight average molecular weight (Mw) of the propylene-based elastomer is at least 150,000 g/mole; or within a range from 150,000, or 200,000 g/mole to 300,000, or 400,000, or 500,000 g/mole.

The PBE may have a number average molecular weight (Mn) of from 2,500 to 2,500,000 g/mol, or from 5,000 to 500,000 g/mol, or from 10,000 to 250,000 g/mol, or from 25,000 to 200,000 g/mol. The PBE may have a Z-average molecular weight (Mz) of from 10,000 to 7,000,000 g/mol, or from 50,000 to 1,000,000 g/mol, or from 80,000 to 700,000 g/mol, or from 100,000 to 500,000 g/mol. The molecular weight distribution (MWD, equal to Mw/Mn) of the PBE may be from 1 to 40, or from 1 to 15, or from 1.8 to 5, or from 1.8 to 3.

Optionally, the propylene-based polymer compositions may also include one or more dienes. In embodiments where the propylene-based polymer compositions comprises a diene, the diene may be present at from 0.05 wt % to 6 wt % diene-derived units, or from 0.1 wt % to 5.0 wt % diene-derived units, or from 0.25 wt % to 3.0 wt % diene-derived units, or from 0.5 wt % to 1.5 wt % diene-derived units, where the percentage by weight is based upon the total weight of the propylene-derived, alpha-olefin derived, and diene-derived units.

In one or more embodiments, the PBE can optionally be grafted (i.e., “functionalized”) using one or more grafting monomers. As used herein, the term “grafting” denotes covalent bonding of the grafting monomer to a polymer chain of the PBE. The grafting monomer can be or include at least one ethylenically unsaturated carboxylic acid or acid derivative, such as an acid anhydride, ester, salt, amide, imide, acrylates or the like. Illustrative monomers include but are not limited to acrylic acid, methacrylic acid, maleic acid, fumaric acid, itaconic acid, citraconic acid, mesaconic acid, maleic anhydride, 4-methyl cyclohexene-1,2-dicarboxylic acid anhydride, bicyclo(2.2.2)octene-2,3-dicarboxylic acid anhydride, 1,2,3,4,5,8,9,10-octahydronaphthalene-2,3-dicarboxylic acid anhydride, 2-oxa-1,3-diketospiro(4.4)nonene, bicyclo(2.2.1)heptene-2,3-dicarboxylic acid anhydride, maleopimaric acid, tetrahydrophthalic anhydride, norbornene-2,3-dicarboxylic acid anhydride, nadic anhydride, methyl nadic anhydride, himic anhydride, methyl himic anhydride, and 5-methylbicyclo(2.2.1)heptene-2,3-dicarboxylic acid anhydride. Other suitable grafting monomers include methyl acrylate and higher alkyl acrylates, methyl methacrylate and higher alkyl methacrylates, acrylic acid, methacrylic acid, hydroxy-methyl methacrylate, hydroxyl-ethyl methacrylate and higher hydroxy-alkyl methacrylates and glycidyl methacrylate. Maleic anhydride is a preferred grafting monomer. In one or more embodiments, the grafted PBE comprises from 0.5 wt % to 10 wt % ethylenically unsaturated carboxylic acid or acid derivative, more preferably from 0.5 wt % to 6 wt %, more preferably from 0.5 wt % to 3 wt %; in other embodiments from 1 wt % to 6 wt %, more preferably from 1 wt % to 3 wt %. In a preferred embodiment, wherein the graft monomer is maleic anhydride, the maleic anhydride concentration in the grafted polymer is preferably in the range of 1 wt % to 6 wt %, preferably at least 0.5 wt %, and highly preferably 1.5 wt %.

In some embodiments, the PBE is a reactor blend of a first polymer component and a second polymer component. Thus, the comonomer content of the PBE can be adjusted by adjusting the comonomer content of the first polymer component, adjusting the comonomer content of second polymer component, and/or adjusting the ratio of the first polymer component to the second polymer component present in the propylene-based polymer composition. In such embodiments, the first polymer component may comprise propylene and ethylene and have an ethylene content of greater than 10 wt % ethylene, or greater than 12 wt % ethylene, or greater than 13 wt % ethylene, or greater than 14 wt % ethylene, or greater than 15 wt % ethylene, and an ethylene content that is less than 20 wt % ethylene, or less than 19 wt % ethylene, or less than 18 wt % ethylene, or less than 17 wt % ethylene, or less than 16 wt % ethylene, where the percentage by weight is based upon the total weight of the propylene-derived and ethylene derived units of the first polymer component. In such embodiments, the second polymer component may comprise propylene and ethylene and have an ethylene content of greater than 2 wt % ethylene, or greater than 3 wt % ethylene, or greater than 4 wt % ethylene, or greater than 5 wt % ethylene, or greater than 6 wt % ethylene, and an ethylene content that is less than 10 wt % ethylene, or less than 9. wt % ethylene, or less than 8 wt % ethylene, or less than 7 wt % ethylene, or less than 6 wt % ethylene, or less than 5 wt % ethylene, where the percentage by weight is based upon the total weight of the propylene-derived and ethylene derived units of the second polymer component. In such embodiments, the PBE may comprise from 3 wt % to 25 wt % of the second polymer component, or from 5 wt % to 20 wt % of the second polymer component, or from 7 wt % to 18 wt % of the second polymer component, or from 10 wt % to 15 wt % of the second polymer component, and from 75 wt % to 97 wt % of the first polymer component, or from 80 wt % to 95 wt % of the first polymer component, or from 82 wt % to 93 wt % of the first polymer component, or from 85 wt % to 90 wt % of the first polymer component, based on the weight of the PBE.

Polymerization of the PBE is conducted by reacting monomers in the presence of a catalyst system described herein at a temperature of from 0° C. to 200° C. for a time of from 1 second to 10 hours. Preferably, homogeneous conditions are used, such as a continuous solution process or a bulk polymerization process with excess monomer used as diluent. The continuous process may use some form of agitation to reduce concentration differences in the reactor and maintain steady state polymerization conditions. The heat of the polymerization reaction is preferably removed by cooling of the polymerization feed and allowing the polymerization to heat up to the polymerization, although internal cooling systems may be used.

Further description of exemplary methods suitable for preparation of the PBEs described herein may be found in U.S. Pat. No. 6,881,800; U.S. Pat. No. 7,803,876; U.S. Pat. No. 8,013,069; and U.S. Pat. No. 8,026,323.

The triad tacticity and tacticity index of the PBE may be controlled by the catalyst, which influences the stereoregularity of propylene placement, the polymerization temperature, according to which stereoregularity can be reduced by increasing the temperature, and by the type and amount of a comonomer, which tends to reduce the level of longer propylene derived sequences.

Too much comonomer may reduce the crystallinity provided by the crystallization of stereoregular propylene derived sequences to the point where the material lacks strength; too little and the material may be too crystalline. The comonomer content and sequence distribution of the polymers can be measured using ¹³C nuclear magnetic resonance (NMR) by methods well known to those skilled in the art. Comonomer content of discrete molecular weight ranges can be measured using methods well known to those skilled in the art, including Fourier Transform Infrared Spectroscopy (FTIR) in conjunction with samples by GPC, as described in Wheeler and Willis, 47 APPLIED SPECTROSCOPY 1128-1130 (1993). For a propylene ethylene copolymer containing greater than 75 wt % propylene, the comonomer content (ethylene content) of such a polymer can be measured as follows: A thin homogeneous film is pressed at a temperature of 150° C. or greater, and mounted on a Perkin Elmer PE 1760 infrared spectrophotometer. A full spectrum of the sample from 600 cm⁻¹to 4000 cm⁻¹is recorded and the monomer wt % of ethylene can be calculated according to the following equation: Ethylene wt %=82.585-111.987X+30.045X², where X is the ratio of the peak height at 1155 cm⁻¹and peak height at either 722 cm⁻¹or 732 cm⁻¹, whichever is higher. For propylene ethylene copolymers having 75 wt % or less propylene content, the comonomer (ethylene) content can be measured using the procedure described in Wheeler and Willis. Reference is made to U.S. Pat. No. 6,525,157, whose test methods are also fully applicable for the various measurements referred to in this specification and claims and which contains more details on GPC measurements, the determination of ethylene content by NMR and the DSC measurements.

The catalyst systems used for producing the PBE may comprise a metallocene compound. In any embodiment, the metallocene compound may be a bridged bisindenyl metallocene having the general formula (In¹)Y(In²)MX₂, where In¹and In²are identical substituted or unsubstituted indenyl groups bound to M and bridged by Y, Y is a bridging group in which the number of atoms in the direct chain connecting In¹with In²is from 1 to 8 and the direct chain comprises C, Si, or Ge; M is a Group 3, 4, 5, or 6 transition metal; and X₂are leaving groups. In¹and In²may be substituted or unsubstituted. If In¹and In²are substituted by one or more substituents, the substituents are selected from the group consisting of a halogen atom, C₁to C₁₀alkyl, C₅to C₁₅aryl, C₆to C₂₅alkylaryl, and Si-, N- or P-containing alkyl or aryl. Each leaving group X may be an alkyl, preferably methyl, or a halide ion, preferably chloride or fluoride. Exemplary metallocene compounds of this type include, but are not limited to, μ-dimethylsilylbis(indenyl) hafnium dimethyl and μ-dimethylsilylbis(indenyl) zirconium dimethyl.

Suitable PBEs for use in the present invention include Vistamaxx™ grades available from ExxonMobil Chemical, including Vistamaxx™ 6102, 6202, 3020, and 3980.

It has been found surprisingly that the use of a PBE with a low MFR and correspondingly high molecular weight leads to greatest improvement in the room temperature notched Izod impact strength of the polymeric blend where the IPP component is the preferred high MFR and low MW. Such improvements are unanticipated based on the prior data.

Polypropylene

The “polypropylene” that is preferably used in the compositions is a homopolymer or copolymer comprising from 60 wt % or 70 wt % or 80 wt % or 85 wt % or 90 wt % or 95 wt % or 98 wt % or 99 wt % to 100 wt % propylene-derived units; comprising within the range of from 0 wt % or 1 wt % or 5 wt % to 10 wt % or 15 wt % or 20 wt % or 30 wt % or 40 wt % C₂and/or C₄to C₁₀α-olefin derived units; and can be made by any desirable process using any desirable catalyst as is known in the art, such as a Ziegler-Natta catalyst, a metallocene catalyst, or other single-site catalyst, using solution, slurry, high pressure, or gas phase processes. Certain polypropylenes that find use as the compositions have within the range from 0.2 wt % or 0.5 wt % to 1 wt % or 2 wt % or 5 wt % ethylene-derived units. Polypropylene copolymers are useful polymers in certain embodiments, especially copolymers of propylene with ethylene and/or butene, and comprise propylene-derived units within the range of from 70 wt % or 80 wt % to 95 wt % or 98 wt % by weight of the polypropylene. In any case, useful polypropylenes have a DSC melting point (ASTM D3418) of at least 130° C. or 140° C. or 150° C. or 160° C. or 165° C., or within a range of from 130° C. or 135° C. or 140° C. to 150° C. or 160° C. or 170° C. A “highly crystalline” polypropylene is preferred in certain embodiments of the inventive compositions, and is typically isotactic and comprises 100 wt % propylene-derived units (propylene homopolymer) and has a relatively high melting point of from greater than (greater than or equal to) 130° C. or 140° C. or 145° C. or 150° C. or 155° C. or 160° C. or 165° C.

The term “crystalline,” as used herein, characterizes those polymers which possess high degrees of inter- and intra-molecular order. Preferably, the polypropylene has a heat of fusion (H_f) greater than 60 J/g or 70 J/g or 80 J/g, as determined by DSC analysis. The heat of fusion is dependent on the composition of the polypropylene; the thermal energy for the highest order of polypropylene is estimated at 89 J/g, that is, 100% crystallinity is equal to a heat of fusion of 89 J/g. A polypropylene homopolymer will have a higher heat of fusion than a copolymer or blend of homopolymer and copolymer. Also, the polypropylenes useful in the inventive compositions may have a glass transition temperature (ISO 11357-1, Tg) preferably between −20° C. or −10° C. or 0° C. to 10° C. or 20° C. or 40° C. or 50° C. Preferably, the polypropylenes have a Vicat softening temperature (ISO 306, or ASTM D 1525) of greater than 120° C. or 110° C. or 105° C. or 100° C., or within a range of from 100° C. or 105° C. to 110° C. or 120° C. or 140° C. or 150° C., or a particular range of from 110° C. or 120° C. to 150° C.

Preferably, the polypropylene has a melt flow rate (“MFR”, 230° C., 2.16 kg, ASTM D1238) within the range from 10, or 18 g/10 min to 40, or 50, or 60, or 80, or 120 or 150 or 200 g/10 min. Also, the polypropylene may have a molecular weight distribution (determined by GPC) of from 1.5 or 2.0 or 2.5 to 3.0 or 3.5 or 4.0 or 5.0 or 6.0 or 8.0 in certain embodiments. Suitable grades of polypropylene that are useful in the compositions described herein include those made by ExxonMobil, Lyondell Basell, Total, Borealis, Japan Polypropylene, Mitsui, and other sources. A description of semi-crystalline polypropylene polymers and reactor copolymers can be found in “Polypropylene Handbook”, (E. P. Moore Editor, Carl Hanser Verlag, 1996).

In embodiments of the inventive compositions, the polypropylene component may be a so-called impact copolymer (ICP). Such ICPs are themselves two phase systems, however in the present heterophase blends, each of the two individual phases of the ICP may generally blend with the respective phase of the blend, i.e., crystalline and/or amorphous. As indicated, an ICP can be in the polypropylene component as part—or all—of the polypropylene component, used in combinations with the other components of the hetero phase composition. The polypropylene homopolymer portion of the ICPs have melt flow rates (MFR) (determined by the ASTM D1238 technique, condition L) in the range of from 15 to 200, or at least 15 and/or less than 120 dg/min. Exemplary α-olefins for the rubber portion of the ICP, may be selected from one or more of ethylene, propylene; and C4 to C20 α-olefins such as 1-butene; 1-pentene, 2-methyl-1-pentene, 3-methyl-1-butene; 1-hexene, 3-methyl-1-pentene, 4-methyl-1-pentene; 3,3-di methyl-1-butene; 1-heptene; 1-hexene; methyl-1-hexene; dimethyl-1-pentene; trimethyl-1-butene; ethyl-1-pentene; 1-octene; methyl-1-pentene; dimethyl-1-hexene; trimethyl-1-pentene; ethylhexene-1; methylethyl-1-pentene; diethyl-1-butene; 1-propyl-1-pentene; 1-decene; methyl-1-nonene; 1-nonene; dimethyl-1-octene; trimethyl-1-heptene; 1-ethyl-1-octene; methylethyl-1-butene; diethyl-1-hexene; 1-dodecene, and 1-hexadodecene.

Suitably, if ethylene is the α-olefin in the rubber phase of the ICP, it may be present in the range of from 25 wt % to 70 wt %, or at least 30 wt % and/or less than 65 wt % based on the weight of the rubber phase. The rubber phase may be present in the ICP in the range of from 4 wt % to 20 wt %, or at least 6 wt % or 10 wt % and/or less than 18 wt %, all based on the total weight of the ICP. The MFR of the ICP may be in the range of from 15 to 60, or may be at least 20 and/or less than 50 or less than 40 dg/min.

The ICP may be a physical blend of iPP and EP rubber, or a so-called reactor blend. In any case, the ICP is a blend of polypropylene and one or more elastomeric polymers of the ethylene α-olefin type, generally ethylene propylene elastomeric polymers. The ICP useful in embodiments of our invention may be prepared by conventional polymerization techniques such as a two-step gas phase process using Ziegler-Natta catalysis. For example, see U.S. Pat. No. 4,379,759 which is fully incorporated by reference. The ICPs of embodiments of our invention are preferably produced in reactors operated in series, and the second polymerization, may be carried out in the gas phase. The first polymerization may be a liquid slurry or solution polymerization process. Metallocene catalyst systems may be used to produce the ICP compositions useful in embodiments of our invention. Current particularly suitable metallocenes are those in the generic class of bridged, substituted bis(cyclopentadienyl) metallocenes, specifically bridged, substituted bis(indenyl) metallocenes known to produce high molecular weight, high melting, highly isotactic propylene polymers. Generally speaking, those of the generic class disclosed in U.S. Pat. No. 5,770,753 (fully incorporated herein by reference) should be suitable.

Suitable polypropylene for use in the present invention include PP3155 (MFR of 36 g/10 min, measured at 230° C. and 2.16 kg) and PP 9999SS (MFR of 60 g/10 min, measured at 230° C. and 2.16 kg), commercially available from ExxonMobil Chemical Company.

Composition

Additives may by present in the compositions described herein and are preferably present, if at all, to an extent that does not negatively influence the impact or modulus of the composition or components made from the composition. By “consisting essentially of”, what is meant is that the composition may include one or more additives as is known in the art as long as the claimed properties are not altered such that they fall outside the scope of those claimed properties; and by “consisting of” what is meant is that the compositions include additives to a level no greater than 1 wt % or 2 wt % or 3 wt % of the total weight of the composition, or alternatively, additives are not measurably present. The “additives” include fillers (especially, silica, glass fibers, talc, etc.) colorants, whitening agents, cavitation agents, antioxidants, anti-slip agents, antifogging agents, nucleating agents, and other additives common in TPO compositions useful in automotive components. Other useful additives include stabilizers and mold release agents. Primary and secondary antioxidants include, for example, hindered phenols, hindered amines, and phosphates. Nucleating agents include, for example, sodium benzoate and talc. Dispersing agents such as AcroWax C can also be included. Slip agents include, for example, oleamide and erucamide. Catalyst deactivators are also commonly used, for example, calcium stearate, hydrotalcite, and calcium oxide.

The inventive compositions are most often described as a combination of its components and the properties of those components, but preferably the composition has a total ethylene content within the range of 6, or 10, or 12 to 16, or 18, or 20, or 24 wt %. The composition can be used to form any number of articles, which typically includes melt blending the components described herein and forming them into articles either before or after allowing the melt to cool. The “cooled melt blend” is thus the reaction product of melt blending the components, taking into account the possibility that there could be some transformation of one or more of the components facilitated by the heating and/or mixing process.

Useful Articles.

Preferred compositions herein are particularly useful for automotive applications, preferably for making molded high impact automotive parts such as car bumpers, e.g., bumper fascia. These compositions are blends, preferably physical blends, which have high impact and improved ductility.

Examples of automotive articles that can be made from one or more of the compositions described above or elsewhere herein include exterior or interior car components. More specific embodiments of such automotive articles include bumper fascia, fender liners, wheel well covers, body side moldings, pillar trim, door trim panels, consoles, instrument panel end-caps, instrument panel trims, airbag covers, glove box bins, rear quarter panels, lift gate panels, seat back covers, airbag components, airbags, instrument panel covers, dash board skins, air dams and headliner cartridges.

It has been observed that certain compositions described above and elsewhere herein have improved processability, and also improved mechanical properties, particularly compositions that contain high levels of isotactic polypropylene, e.g., above 70 wt. %. Generally speaking, one of the problems with adding more isotactic polypropylene to any thermoplastic composition is a noticeable drop in ductility. For example, any improvement in a mechanical or impact property such as Notched Izod tends to be accompanied by an undesirably high loss of flexibility, e.g., flexural modulus. Such a trade-off is of great concern for the makers of automotive parts, particular car bumpers. Certain compositions described above provide a combination of: (a) high Notched Izod together with (b) high flexural modulus. In addition to having superior mechanical properties, the compositions also have desirable molding properties, e.g., sufficiently high MFR, without losing their superior impact strength and flexibility.

Certain compositions described above or elsewhere herein include one or more additives; or one or more additives selected from the group consisting of a lubricant, antistatic agent, slip agent, anti-block agent, colorant, metal deactivator, mold release agent, filler, reinforcement, fluorescent whitening agent and biostabilizer. In certain compositions described above or elsewhere herein, the composition includes a pigment, which may in certain compositions be one or more colored pigments.

In certain instances, highly amorphous, very low density ethylene-propylene copolymers (EP) or ethylene-propylene-diene terpolymers (EPDM) have been used as the modifier component in TPOs or TPVs. Those EP or EPDMs may tend to have a high viscosity expressed in Mooney units. One of the markets for TPOs is automotive parts, especially bumper fascia. Other applications include automotive interior components such as door skin, air bag cover, side pillars and the like. These parts are generally made using an injection molding processes. In forming those parts, there is an ongoing need not only for desirable mechanical properties, e.g., impact strength and flexibility, but also for processability, e.g., in connection with molding times and wall thicknesses in the molds.

The various descriptive elements and numerical ranges disclosed herein for the inventive compositions can be combined with other descriptive elements and numerical ranges to describe the invention(s); further, for a given element, any upper numerical limit can be combined with any lower numerical limit described herein, including the examples. The features of the invention are demonstrated in the following non-limiting examples.

EXAMPLES

The thermoplastic olefin compounds of embodiments of the invention were formulated in 16 mm Thermo Prism twin screw extruder. Compounding in the twin screw extruder was accomplished using an intense mixing screw element. The batch size was 1000 gm. The temperature profile in the various extruder zones was ramped progressively from 170° C. to 210° C. The compounds discharged from the extruder were pelletized.

Standard test specimens conforming to ASTM specifications were prepared through injection molding on a Nissei Injection Molder, Model NS20-2A. The nozzle, front and rear temperatures of the injection molding equipment were maintained at 190° C. The mold temperature was kept constant at 40° C. The total cycle time was 54 seconds and the injection pressure was 4 MPa. A family mold containing various ASTM specimen cavities was used. The ExxonMobil Test method is described in T. C. Yu “Impact Modification of Polypropylenes with Exact Plastomers”, SOC. OF PLASTICS ENGINEERS, ANTEC (May 1994).

For this test method, Notched Izod Impact Testing based on ASTM D256/A was used to study impact behavior. This test continuously measures the applied force and time during the impact event. The electronically collected data points are next processed through a computer to provide graphic representation of both force and energy as a function of displacement.

An Izod Impact tester, Ceast Impactor II, was used to gather the data. It consists of a solid monolithic metal structure housing the components to be used for testing, such as hammers, vices or supports. A touch-screen multi-function display is placed on the structure base left side and used by operator for test parameter input and result review.

The test specimens are generally cut from injection molded ASTM Tensile Bar. At least 5 specimens are prepared for the test. The specimens shall be free of twist and shall have mutually perpendicular, parallel surfaces. The surfaces and edges shall be free from scratches, pits, sink marks and flash. Test specimens should be conditioned at 23±2° C. and as close to 50±10% relative humidity for not less than 40 hours after notching and prior to testing. The test shall be conducted in the same atmosphere that is used for conditioning, unless for sub-ambient temperature, an additional overnight acclimatization period (at least 6 hours) at the requirement temperature is needed.

In the Izod test, the specimen is supported like a built-in beam and broken by a single pendulum oscillation at a determined distance from the specimen holding and the central impact line. Its impact strength is determined from the energy that is adsorbed by the sample. The sample that is hold in a cantilevered beam configuration differentiates the Izod impact test from the Charpy impact test. Impact energy absorbed in breaking a notched specimen, referred to the original cross-sectional area of the specimen at the notch, with the pendulum striking the face containing the notch.

Izod Impact of Compositions

The polypropylene resins selected for this study were combined with the ethylene-propylene copolymer and a propylene-based elastomer to form a TPO, the TPO having a melt flow rate in range of 20 to 35 dg/min, and a total ethylene content in the polymer nominally in the range of 6 or 10 or 12 to 16 or 18 or 20 or 24 wt %, while the ethylene in the EP copolymer phase was from 45 wt % to 55 wt %. The ethylene-propylene copolymer used throughout the examples is Vistalon™785, commercially available from ExxonMobil Chemical Company. Vistalon™ 785 has an ethylene content of 49 wt %, a Mooney Viscosity (ML 1+4, 125° C.) of 30 MU, and a MFR of 0.35 g/10 min.

The propylene-based elastomer used throughout the examples are Vistamaxx™ performance polymers, commercially available from ExxonMobil Chemical Company, including Vistamaxx 6202, 6102, 3020, and 3980. Vistamaxx™ 6202 is a propylene-ethylene copolymer having a density of 0.863 g/cm³, melt index (at 190° C., 2.16 kg) of 9.1 g/10 min, MFR of 20 g/10 min, and ethylene content of 15 wt %. Vistamaxx™ 6102 is a propylene-ethylene copolymer having a density of 0.862 g/cm³, melt index (at 190° C., 2.16 kg) of 1.4 g/10 min, MFR of 3 g/10 min, and ethylene content of 16 wt %. Vistamaxx™ 3020 is a propylene-ethylene copolymer having a density of 0.874 g/cm³, melt index (at 190° C., 2.16 kg) of 1.1 g/10 min, MFR of 3 g/10 min, and ethylene content of 11 wt %. Vistamaxx™ 3980 is a propylene-ethylene copolymer having a density of 0.878 g/cm³, melt index (at 190° C., 2.16 kg) of 3.7 g/10 min, MFR of 8 g/10 min, and ethylene content of 9 wt %. Also, throughout the examples, the polypropylene used is an isotactic PP, either “iPP 1” or “iPP 2”, which are, respectively, PP3155 (MFR of 36 g/10 min, measured at 230° C. and 2.16 kg) and PP 9999SS (MFR of 60 g/10 min, measured at 230° C. and 2.16 kg), commercially available from ExxonMobil Chemical Company. The melting point temperatures of the polypropylene are 166±1.5° C. with a heat of fusion of 90 to 97 J/g by DSC.

The following examples are TPO's formed with (inventive) or without (comparative) a propylene-based Vistamaxx copolymer.

Inventive Example 1

The composition includes 68.5 wt % iPP 1, 3.5 wt % of the propylene-based elastomer, and 28.5 wt % Vistalon′785. The polymers were mixed in two stages on a twin screw extruder and then injection molded into bars which were tested for notched Izod impact at room temperature (22° C.). The results are tabulated in Table 1.

Comparative Example 1

The comparative example, not including the propylene-based elastomer, includes 68.5 wt % iPP 1 and 31.5 wt % ethylene-propylene copolymer. The samples were mixed and tested as Inventive Example 1. The results are tabulated in Table 1.

TABLE 1

Notched Impact for TPOs (with the propylene-based

elastomer) with iPP 1

Notched Impact at

Sample
Formulation
22° C. (ft-lb/in)

1-1
68.5 wt % iPP 1
1.8

(Comparative)
31.5 wt % Vistalon 785

1-2
68.5 wt % iPP 1
34.5

28.5 wt % Vistalon 785

3.5 wt % Vistamaxx 6202

1-3
68.5 wt % iPP 1
10.7

28.5 wt % Vistalon 785

3.5 wt % Vistamaxx 6102

1-4
68.5 wt % iPP 1
9.0

28.5 wt % Vistalon 785

3.5 wt % Vistamaxx 3020

1-5
68.5 wt % iPP 1
9.7

28.5 wt % Vistalon 785

3.5 wt % Vistamaxx 3980

As indicated by Table 1, replacing 3.5 wt % Vistalon 785 with Vistamaxx (see Samples 1-2 through 1-5), room temperature notch impact performance improved at least four-fold compared to impact performance for TPO formulations without Vistamaxx (see Comparative Sample 1-1). Formulation 1-2 having Vistamaxx 6202 (high ethylene content with higher MFR/low molecular weight Vistamaxx), room temperature notch impact performance improved close to twenty-fold compared to impact performance for Comparative Sample 1-1.

Inventive Example 2

The composition includes 68.5 wt % iPP 2, 3.5 wt % of the propylene-based elastomer, and 28.5 wt % Vistalon 785. The polymers were mixed in two stages on a twin screw extruder and then injection molded into bars which were tested for notched Izod impact at room temperature (22° C.). The results are tabulated in Table 2.

Comparative Example 2

The comparative example, not including the propylene-based elastomer, includes 68.5 wt % iPP 2 and 31.5 wt % ethylene-propylene copolymer. The samples were mixed and tested as Inventive Example 2. The results are tabulated in Table 2.

TABLE 2

Notched Impact for TPOs (with the propylene-based

elastomer) with iPP 2

Notched Impact at

Sample
Formulation
22° C. (ft-lb/in)

2-1
68.5 wt % iPP 2
1.0

(Comparative)
31.5 wt % Vistalon 785

2-2
68.5 wt % iPP 2
4.2

28.5 wt % Vistalon 785

3.5 wt % Vistamaxx 6202

2-3
68.5 wt % iPP 2
38.0

28.5 wt % Vistalon 785

3.5 wt % Vistamaxx 6102

2-4
68.5 wt % iPP 2
33.4

28.5 wt % Vistalon 785

3.5 wt % Vistamaxx 3020

2-5
68.5 wt % iPP 2
9.8

28.5 wt % Vistalon 785

3.5 wt % Vistamaxx 3980

Generally, TPO formulations with high MFR isotactic polypropylene are preferred to TPOs with low MFR iPP. Surprisingly, Comparative 2-1 of Table 2 having high MFR iPP (iPP 2 has a MFR of 60 g/10 min) had a less preferred room temperature notch impact performance than Comparative 1-1 of Table 1 having a much lower MFR iPP (iPP 1 has a MFR of 35 g/10 min). The results of Table 2 illustrate that replacing 3.5 wt % Vistalon 385 with Vistamaxx improves room temperature notch impact performance. Specifically, adding low MFR Vistamaxx grades to TPO formulations (e.g., Sample 2-3 and 2-4 having Vistamaxx 6102 with a MFR of 3 g/10 min and Vistamaxx 3020 with a MFR of 3 g/10 min) improved room temperature notch impact performance by more than thirty-fold as compared to impact performance for Comparative Sample 2-1.

For all jurisdictions in which the doctrine of “incorporation by reference” applies, all of the test methods, patent publications, patents and reference articles are hereby incorporated by reference either in their entirety or for the relevant portion for which they are referenced.