MX2007016400A - Automotive articles prepared from filled tpo compositions, and methods of making the same - Google Patents

Abstract

An automotive part containing at least one component formed from a composition comprising the following:(i) a crystalline, isotactic propylene homopolymer, (ii) an ethylene/α-olefm elastomeric impact modifier, and (iii) a reinforcing grade of filler, for example, talc. The crystalline isotactic propylene homopolymer has a flex modulus of greater than about 1930 MPa and a heat deflection temperature (HDT) of greater than about 100°C;the ethylene/α-olefin interpolymer has a Tg of less than about -30°C, and a tan delta measured at 0.1 radians/s at 190°C of less than about 2;and the filler has a HDT reinforcing efficiency of at least about 2. The automotive part has an HDT of greater than about 100°C and a flex modulus of greater than about 1930 MPa.

Description

AUTOMOTIVE ARTICLES PREPARED FROM COMPOSECTIONS OF TPO FILLERS AND METHODS TO MAKE THEMSELVES REFERENCE TO PREVIOUS APPLICATION This application claims the benefit of provisional application no. 60/694150, filed June 24, 2005, incorporated herein by reference in its entirety.

FIELD OF THE INVENTION The present invention relates to automotive parts, such as an instrumental panel assembly, and methods for forming same. In particular, the invention relates to automotive parts formed from filled thermoplastic polyolefin (TPO) compositions. In one aspect, this invention relates to TPO compositions comprising a highly crystalline isotactic propylene homopolymer, an elastomeric ethylene / α-olefin impact modifier (EAO), and a reinforcing grade of a laminated filler, eg, talc. In another aspect, this invention relates to such filled TPO compositions having low gloss, good impact resistance at low temperature and flexural modulus and superior heat deflection temperature (HDT) properties. In still another aspect, this invention relates to automotive injection molded articles prepared from these TPO compositions.

BACKGROUND OF THE INVENTION In general, the automotive industry has sought to form automotive assemblies that have both structural integrity and relatively low weight. For example, an instrument panel assembly of an automotive vehicle must exhibit sufficient structural integrity to support one or more peripheral components, such as airbag assemblies, steering columns or other panel parts, and at the same time, should maintain a low weight to help lower the overall weight for the vehicle. Talc-filled TPOs have gained widespread use in automotive exterior applications, such as fascias, and other applications, requiring a balance of stiffness, impact resistance, at temperatures below about -30 ° C, resistance to scratches and damage, and resistance deformation, at temperatures of approximately 100 ° C. The flexural modulus for these degrees of TPOs is usually between about 7030 and 14060 kg / cm2 (100,000 and 200,000 psi), and the HDT is usually below about 1 10 ° C. New materials have been developed for soft TPOs that can be used as an Instrument Panel (IP) skin in automobiles. These materials are designed to be thermoformed after either extrusion or calendering. Once formed, these skins exhibit the low gloss, impact resistance at low temperature, resistance to scratch and damage, and grain retention required. The thermoformed IP skins described above are placed on a structure made from polycarbonate / acrylonitrile-butadiene-styrene copolymer (PC / ABS) and urethane foam is injected between the skin and structure to create a "soft touch" instrument panel. PC / ABS has been chosen, despite its cost, due to its higher rigidity (typically 23199-24605 kg / cm2 (330,000-350,000 psi) of flexural modulus), and its higher resistance to deflection under load at elevated temperatures ( normally 120 ° C-130 ° C). Because the structure must also remain undamaged when a passenger-side air bag deploys, the structure must also be able to survive an air bag deployment at -20 ° C, preferably -30 ° C. Of continuous interest in the automotive industry is replacing the PC / ABS structure with lower cost polyolefin alternatives. Various polypropylene compositions are described in the following patents or applications. US Patent 6,759,475 discloses a crystalline polypropylene-based resin composition, which includes: (a) 3-65 percent, by weight, of a paraxylene soluble component of 23 ° C, (b) 35-97 percent, by weight, of a paraxylene soluble component of 135 ° C, and insoluble in paraxylene of 23 ° C and (c) 0-30 percent, by weight, of a paraxylene insoluble component of 135 ° C (for example, see summary). Component (a), soluble in paraxylene of 23 ° C, is substantially composed of an elastomeric constituent (a1) having a styrene content, or its derivative, in the range of 0-35 percent, by weight, and a viscosity intrinsic (?) in the range of 0.1 -5 dl / g. Component (b), soluble is paraxylene of 135 ° C and insoluble in paraxylene of 23 ° C, is substantially composed of a constituent of crystalline polypropylene (b1) having an isotactic proportion of pentada (mmmm) of 97 percent or greater, a molecular weight distribution (Mw / Mn) of 6 or greater and a molecular weight distribution (Mz / Mw) of 6 or greater. Component (c), insoluble in paraxylene of 1 35 ° C, is substantially composed of a filler (d). The US patent application no. 2004/0044107 describes a propylene resin composition having good molding capabilities and a good balance of physical properties, as well as good appearance, lower gloss and scratch resistance. These compositions can be used for car interior parts (for example, see summary). The polypropylene resin composition comprises the following components; a crystalline homopolypropylene having an MFR of 500 to 3,000 g / 1 0 min, a polypropylene consisting of a crystalline homopolypropylene and an ethylene-propylene copolymer rubber having 45 to 80 percent, by mass, of an ethylene content; a polypropylene, consisting of a homopolypropylene and an ethylene-propylene copolymer rubber having 25 percent, by mass, or more, below 45 percent, by mass, of an ethylene content; and an ethylene-to-olefin copolymer rubber (for example, see abstract). U.S. Patent 6,660,797 discloses a propylene-based composition for molded polypropylene resin articles, excellent in scratch resistance and castability, and well-balanced properties between high rigidity and alpha impact strength, and also provides a method for molding the propylene-based composition above, to provide high-performance industrial parts and automotive parts, and in particular automotive interior parts (for example, see summary ). A sample propylene-based resin composition contains the following components (A) and (B), as described below (for example, see column 2, lines 14-49). Component (A) is a propylene-based resin composed of the following components (a1), (a2) and (a3); 90 to 40 weight percent: (a1) propylene / ethylene block copolymer, composed of 60 to 83 weight percent crystalline homopolymer component (A1-1 unit) and 1.7 to 40 weight percent component copolymer ethylene / propylene random copolymer (a1 -2 unit), containing 30 to 52 weight percent ethylene, and having a weight average molecular weight of 230,000 to 600,000; and having a melt flow rate (230 ° C, 2.16 kg) of 1 5 to 150 g / 10 min, and number of gels of 100, or less, for those having a size of 50 μm or more, in the article molding of 25 cm2 (area) and 0.5 mm (thickness); 100 parts by weight; (a2) talc having an average particle size of 0.5 to 1 5 μm; 0 to 200 parts by weight; (a3) ethylene / α-olefin copolymer rubber, containing 20 to 50 weight percent α-olefin of 3 to 8 carbon atoms and having a melt flow rate (230 ° C, 2.16 kg) of 0.3 up to 100 g / 1 0 min; 0 to 20 parts by weight. Component (B) is a propylene-based resin material, composed of the following components (b1) and (b2); 10 to 60 percent; (b1) propylene homopolymer or propylene / ethylene block copolymer, having an orthodichlorobenzene insoluble component, below 120 ° C, responding for 8 weight percent or more of the insoluble component below 100 ° C, when fractionated with orthodichlorobenzene as the solvent, and wherein the insoluble component, below 1000 ° C, has a weight average molecular weight of 200,000 or more, and melt flow rate (230 ° C, 2.16 kg) of 0.3 up to 70 g / 10 min; 15 to 80 parts by weight; and (b2) falco or wollastonite having an average particle size of 0.5 to 1 5 μm; 20 to 85 parts by weight (for example, see column 2, lines 14-49). Additional polypropylene compositions are described in U.S. Patent 5,286,776 and U.S. Patent 6,667,359. Other polyolefin compositions and manufactured articles, such as automotive parts, prepared therefrom, are disclosed in US Publication Nos: 2005/0029692; 2004 / 0188885M; and 2004 / &0094986. Additional propylene-based polymers and compositions are described in US publication no. 2005/0272858 (see also international publication No. 2004033509) and US publication no. 2004/0122196. However, the compositions described in these references, and those discussed above, are complex and expensive due to the number of polymeric components in each composition and / or do not meet one or more of the desired rheological, mechanical or thermal properties of the inventive compositions described herein. Moreover, several of the compositions described in these references require a heterophasic polypropylene / (ethylene / polypropylene) rubber, which is not advantageous for low temperature impact properties. There is still a need for low cost, simple polyolefin compositions in polymeric formulations, and which can be used to form manufactured parts, such as automotive parts, which have excellent mechanical and thermal properties. There is a further need for filled TPO compositions that can be used to form reinforced, lightweight automotive parts, such as lightweight injection molded parts. There is also a need for such compositions to be used to form automotive parts with improved performance properties at low temperature and high temperature. These and other needs have been met by the following invention.

BRIEF DESCRIPTION OF THE INVENTION The present invention provides automotive parts, and more particularly, automotive parts injection molded, such as panel assemblies. Such parts are relatively low in weight, although they maintain alpha structural integrity. In accordance with this invention, automotive structures are made from TPO compositions, comprising crystalline isotactic propylene homopolymer, an elastomeric impact modifier of EAO (or ethylene / α-olefin), and a laminated filler reinforcing grade, offer a low cost alternative to conventional PC / ABS resins. These TPO compositions are used to form parts having low brightness, good low impact resistance at about -30 ° C, as measured by Instrumented Dart Impact (ASTM D3763) and by Izod Notch Impact (ASTM D256), a flexural modulus greater than about 1930 MPa (ASTM D790-03, 1% secant modulus) and an HDT (ASTM D648-04, 0.455 MPa) greater than about 1 00 ° C. Such compositions comprise the following: (a) a highly crystalline isotactic propylene homopolymer, with a flexural modulus greater than about 1930 MPa (ASTM D790-03, 1% secant modulus), and an HDT greater than about 100 ° C (ASTM D648-04, 0.455 MPa), (b) an ethylene / α-olefin elastomeric impact modifier (or ethylene / α-olefin interpolymer), with a Tg less than -30 ° C, as measured by scanning calorimetry difference (DSC), a delta so less than about 2, measured at 190 ° C and 0.1 radians per second frequency with an Advanced Rheometric Expansion Systems rheometer (ARES), and an HDT measured by ASTM D648-04, at 0.455 MPa, which is greater than, or equal to, the peak melting temperature of the impact modifier by DSC, and (c) a laminated filler. In such compositions, the ratio of homopolymer to impact modifier (A: B) is between about 9: 1 and about 6: 4. Normally, the ARES rheometer is operated at 15 percent of tension. The DSC procedure for measuring the glass transition temperature (Tg) includes an initial equilibrium of fres minutes at 200 ° C, followed by a downward jump to -90 ° C, at 1 0 ° C / minute, followed by equilibrium for five minutes, and finally, followed by a jump up to 200 ° C at 1 0 ° C / minute. The amount of filler laminate in the TPO composition can vary widely, but usually enough filler is used, so that the compositions of this invention have a flexural modulus efficiency factor of about 3 or more, and an efficiency factor. of deflection by heat of approximately 1.5 or more. The factors are determined by the comparison methods described below. The fill ratio (C) to composition (A + B + C), or (C: (A + B + C)), is adjusted, as necessary, to achieve the desired modulus of flexure and HDT composition. The TPO compositions of this invention may comprise one or more different components, such as pigment and / or a scratch or damage resistant additive. The pigment is usually added as a color concentrate, and the molar articles made from these compositions exhibit good color, so that they may not need to be painted. Thus, the invention provides an automotive part comprising at least one component formed from a polyolefin composition having a deflection temperature heat (HDT) greater than about 100 ° C and flexural modulus greater than about 1930 MPa, the composition comprises: A) a crystalline isotactic propylene homopolymer having a flexural modulus greater than about 1930 MPa and an HDT greater than about 100 ° C; B) an ethylene / α-olefin interpolymer having a Tg less than about -30 ° C, a delta so measured at 0.1 radians / sec at 190 ° C less than about 2, an HDT that is greater than, or equal to, the peak melting temperature of the ethylene / α-olefin interpolymer, as measured by differential scanning calorimetry, and C) a laminated filler, and where The proportion by weight of homopolymer: interpol number (A: B) is between approximately 9: 1 and approximately 6: 4. In one aspect, the weight percentage of filler, based on the sum of weight of the propylene homopolymer, the ethylene / α-olefin interpolymer and filler, is greater than the weight percentage of the ethylene / α-olefin interpolymer, based on the weight sum of the propylene homopolymer and the ethylene / α-olefin interpolymer. In another aspect, the compositions further comprise at least one additive selected from a pigment, a flame retardant, a scratch and damage resistant additive, or combinations thereof. In a further aspect of the invention, the automotive part is selected from an instrument panel, a door panel, a fender, a body side mold, a lower trim molding, a armrest, a visor, a compartment cover or a sphere insulating. In another aspect, the propylene homopolymer has a modulus of bending greater than 2070 MPa and an HDT greater than 1 10 ° C, and more preferably a flexural modulus greater than 2210 MPa and an HDT greater than 120 ° C. In another aspect of the invention, the α-olefin of the ethylene / α-olefin interpolymer is a C3-C20 α-olefin, and more preferably a C4-C20 α-olefin. In a further aspect, the α-olefin of the ethylene / α-olefin interpolymer is selected from propylene, 1-butene, 1 -he ene or 1-ketene, and more preferably is selected from 1-butene, 1 -hexene or 1 -octene. In another aspect of the invention, the ethylene / α-olefin interpolymer has a Tg less than -30 ° C, preferably less than -40 ° C, and more preferably less than -50 ° C. In another aspect, the difference between the "HDT" and the "melting point, Tm", of the ethylene / α-olefin interpolymer is at least 4, preferably at least 6, and more preferably at least 8. In another aspect , the delta tan, measured at 190 ° C and 0.1 0 radians / second, of the ethylene / α-olefin interpolymer is 2 or less, and more preferably 1.8 or less. In another aspect of the invention, the filler is talc laminate. In a further aspect, the composition comprises a sufficient amount of the filler, so that the composition has a flexural modulus efficiency factor of 3 or more, and an HDT efficiency factor of 1.5 or more. In another aspect, the composition comprises 20 weight percent, and more preferably, 30 weight percent talc based on the total weight of the composition. In another aspect, the composition preferably comprises more than, or equal to, 30 percent, and more preferably greater than, or equal to, 35 percent by weight of talc, based on the total weight of the composition. In another aspect, the percentage by weight of filler, based on the "PSO sum of the propylene homopolymer, the ethylene / α-olefin interpolymer and filler", is greater than the weight percentage of the ethylene / interpolymer olefin, based on the "weight sum of the propylene homopolymer and the ethylene / α-olefin interpolymer". In a further aspect, the composition further comprises one or more different ethylene / α-olefin interpolymers. Still in a further aspect, the percentage by weight of filler, based on the "weight sum of the propylene homopolymer, the ethylene / α-olefin interpolymer, the different ethylene / α-olefin interpolymer (s), and filler "is greater than the weight percentage of the ethylene / α-olefin interpolymer and the different ethylene / α-olefin interpolymer (s), based on the "weight sum of the propylene homopolymer, the ethylene / α-olefin interpolymer and one or more different ethylene / α-olefin interpolymers." In another aspect, the automotive part, or at least one component thereof, is formed by injection molding. In a further aspect, injection molding is preformed using tool work designed for PC / ABS resins. In another aspect, the part is formed by injection molding, and wherein the shrinkage "out of the tool" of the part in the xy direction is 10 percent or less of the amount of shrinkage of the part in the x direction and within of the tool cavity. In another aspect, the automotive part is an instrumental panel. In still another aspect, the automotive part is a door panel.

The invention also provides methods for making inventive automotive parts. In a further aspect, a method comprises injection molding a composition comprising a polypropylene homopolymer, an ethylene / α-olefin interpolymer and a laminated filler. The invention also provides automotive parts comprising a combination of two or more aspects or embodiments as described herein. The invention also provides methods for making such automotive parts, said methods comprising a combination of two or more aspects or embodiments as described herein.

DETAILED DESCRIPTION OF THE INVENTION The present invention provides automotive parts, such as panel assemblies, from the compositions as described herein. Panel mounts, such as an instrument panel or door panel, have at least one frame, and may also contain a dye, a welded joint, a mechanical fastener, a combination thereof, or other forms of attachment to secure a or more parts of additional components. The panel assemblies may optionally contain, or be attached to, at least one reinforcing structure. The reinforcing structure is preferably configured to assist in supporting one or more peripheral components, and / or may serve as a bridge for two or more portions of the frame, and / or may serve to increase the rigidity of the frame. framework. The main frame of the panel assembly can be configured in a variety of shapes and sizes, and can include covers, shelves, slots or other openings or support surfaces. The main frame is preferably configured to laterally extend through, partially or substantially, a complete infernal cabin area of a transport vehicle. It is also preferable that the frame includes one or more openings (eg, cavities, through holes or the like) to accommodate peripheral components, such as airbags, audio equipment, markers, navigation systems, climate control component, power supply, sensors, storage receptacles or other peripheral components. The frame can be configured appropriately to receive the components, and secure them in place with a slotted joint, a click fit, a quick connector or some other mechanical joint, with or without, the use of a bracket, seal or other intermediate structure to absorb energy. The automotive parts are formed from the thermoplastic compositions, as described herein. Polypropylene is the primary polymer component of such compositions, and ultimately determines the maximum flexural modulus and HDT that can be achieved. Conventional propylene homopolymer has a flexural modulus (1% drying) less than about 1502 MPa (220.4 kpsi) and an HDT less than 90 ° C and is not rigid enough nor retains its rigidity at a temperature high enough to be useful in these compositions. To achieve the combined objectives of low brightness, low temperature impact resistance, improved flexural modulus (e.g., greater than about 1 520 MPa, 1% sequential), and improved HDT (e.g., greater than about 90 ° C) , preferably, the polypropylene is highly crystalline, isotactic homopolymer with a flexural modulus greater than about 1930 MPa (280 kpsi) and an HDT greater than about 1000 ° C. The most preferred grades of isotactic, highly crystalline homopolymer have a flexural modulus greater than about 2070 MPa (300 kpsi) and a HDT greater than about 1 10 ° C. The most preferred grades of highly crystalline isotactic homopolymer polypropylene have a flexural modulus greater than about 2210 MPa (320 kpsi) and an HDT greater than about 120 ° C. In one embodiment, the propylene homopolymer has an HDT greater than about 90 ° C, preferably greater than about 100 ° C, more preferably greater than about 10 ° C, still more preferably greater than about 120 ° C, and most preferably greater than about 1 30 ° C. In another embodiment, the propylene homopolymer has a flexural modulus greater than about 1720 MPa (250 kpsi), preferably greater than about 1930 MPa (280 kpsi), more preferably greater than about 2210 MPa (320 kpsi), and very preferably greater than about 2210 MPa (320 kpsi). The superior resistance to impact at low temperature is contributed by the modification of the highly crystalline isotactic homopolymer polypropylene with an elastomeric impact modifier of EAO (or ethylene / α-olefin). To provide the necessary impact strength at -30 ° C, the EAO elastomeric impact modifier has a glass transition temperature (Tg) of less than -30 ° C, more preferably less than -40 ° C, and most preferably less -50 ° C. In addition, two other characteristics of the elastomeric impact modifier affect the properties of the composition. First, because the EAO elastomeric impact modifier will be above its melting point long before the highly crystalline, isotactic propylene homopolymer begins to melt, it is desirable to select a grade with an HDT significantly higher than its point. of fusion. Table 1 below shows the delta obtained by subtracting the DSC ™ peak melting temperature from the HDT measured in various EAO elastomers. Preferred degrees of EAO elastomeric impact modifiers have a positive delta, more preferred degrees have a delta of 4 or more, even more preferred degrees have a delta of 6 or more, and the most preferred grades have a delta of 8 or more .

Table 1: Tg and delta parameters (HDT - Tm) of selected impact modifiers Engage elastomers are ethylene-octene copolymers and ENR elastomers are ethylene-butene copolymers. The Dow Chemical Company manufactures both EAO elastomers. Secondly, the delta tan of the elasfomer, measured at 0.1 radians per second (rad / s) at 190 ° C, correlates with the brightness of the finished injection molded part. The smaller the delta tan, the lower the brightness. The delta tan and the viscosity in Poises, measured under these conditions, are shown in Table 1 above. The correlation between tan delta and brightness at 20 degrees (Minolta brightness meter, ASTM D523), measured on impact modified comparison formulations, using a variety of different EAOs, is shown in Table 2 below. The data in this table is based on compounds containing a polymer blend of 70 parts by weight of J707PT (a Mitsui Chemicals impact copolymer polypropylene of 35 MFR with 30 parts by weight of various EAOs available from the Dow Chemical Company). The polymer blend is tested without filler and with the addition of 1.0 percent by weight of ABT-2500 laminated falco from Specialty Minerals. Neither the impact copolymer nor the talc meet the criteria of this invention, but serve to demonstrate how an EAO with such a low delta at 190 ° C and 0.1 radians / second, can dramatically reduce the brightness of 20 degrees of a glossy system of another way. These data show that the choice of elasfomer has the greatest effect in lowering the brightness of polypropylene through the addition of filler (here falco). Polypropylene can vary widely, including both homopolymer and copolymer and both nucleated and non-nucleated polymers. He High MFR polypropylene is normally very bright, and the addition of EAO has some effect to decrease gloss in a flat finish.

Table 2: Effect of EAO with delta as low at 190 ° C and 0.1 rad / s at 20 degree brightness The preferred degrees of elastomeric EAO impact modifiers have Tg and delta properties as described above, and also have a delta as measured at 1 90 ° C and 0.1 radians / second of about 2 or less, more preferably about 1.8 or less and most preferably about 1.6 or less. The low gloss obtained by using an EAO elastomeric impact modifier with the delta as described above makes it possible to provide a part that is colored during the molding process through the use of a color concentrate. This process of colored in mold saves a step of painted, when the compound has an acceptably low brightness. Because the paint is widely known to improve the resistance of the part to deterioration from scratch and damage, the color concentrate is also modified frequently with materials that reduce the surface friction and reduce the surface deterioration caused by scratching and damage. Common additives known in the art are silicon-based materials, such as polydimethyl siloxanes of high molecular weight, waxy materials that bloom to the surface, such as erucamide, and some specialty materials containing a combination of hard and strong plastic, such as nylon, with active surface agents.

Propylene Homopolymer The propylene homopolymer can be a linal or a nucleated homopolymer, or a combination thereof. The propylene homopolymer desirably has a melt flow rate (MFR) (230 ° C / 2.16 kg of weight) from 0.1 to 150, preferably from 1 to 1 00 g / 10 min, more preferably from 3 to 75 g / 10 min, even more preferably from 5 to 50 g / 10 min.

All individual values and subranges from 0.1 to 150 g / 10 min are included herein and described herein. This homopolymer of polypropylene desirably also has a melting point greater than 145 ° C. In another embodiment, the propylene component has a melting point, Tm, from 130 ° C to 180 ° C, preferably from 140 ° C to 1 70 ° C. In another embodiment, the polypropylene homopolymer has a crystallization temperature, Te, greater than, or equal to, 1 10 ° C, preferably greater than, or equal to, 120 ° C, and more preferably greater than, or equal to, , 130 ° C, and most preferably greater than, or equal to, 140 ° C. As used herein, "nucleate" refers to a polymer that has been modified by the addition of a nucleating agent, such as Millad®, a dibenzyl sorbitol commercially available from Milliken. Other conventional nucleating agents can also be used. It is noted that the laminated filler, such as a falco, can act as a nucleant, and may make the addition of another nucleating agent unnecessary. Polymerization processes, used to produce high melting polymers, include the pulping process, which is run at approximately 50-90 ° C and 0.5-1.5 MPa (5-15 atm) and both liquid monomer processes and of gas phase, in which extra care must be taken for the removal of amorphous polymer. Polypropylene can also be prepared by using any of a variety of single site, mephalocene, and restricted geometry catalysts along with its associated processes. The polymerizations can take place in a stirred tank reactor, a gas phase reactor, a simple continuously stirred tank reactor, and a simple paste loop reactor and other suitable reactors. In a preferred embodiment, the polypropylene homopolymer is prepared in a continuous, simple, continuous phase-stirred (propylene condensed) reactor, using a Ziegler-Natta catalyst, which includes a kind of catalytic active metal of titanium, supported in a magnesium chloride support, and suspended in a mineral oil. The suspended catalyst can be pumped directly to the reactor. Hydrogen can be used as a chain transfer agent to control molecular weight. The polymerizations can take place in a stirred tank reactor, a gas phase fluidized bed reactor, a simple continuous stirred tank reactor, and a single paste circuit reactor. Such polymerizations and the resulting polypropylene homopolymers are described in US publication no. 2005/0272858 (see also international publication No. 2004033509) and US publication no. 2004/01221 96. Each of these fres applications is incorporated herein, in its entirety, by reference. In one embodiment, the propylene homopolymer has a molecular weight distribution (Mw / Mn) from 2 to 6, more preferably from 2 to 5 and most preferably from 3 to 5. All individual values and subranges from 2 to 6 are included herein and described herein. In another embodiment, the molecular weight distribution is less than or equal to, 6 and more preferably less than or equal to, 5.5, and more preferably less than, or equal to 5. In another embodiment, the prolene homopolymer has a density from 0.88 to 0.92 g / cm 3, and preferably from 0.89 to 0.91 g / cm 3. All individual values and subranges from 0.88 to 0.92 g / cm3 are included herein and described herein. In another modality, the propylene homopolymer has a number average molecular weight, (Mn) from 10,000 g / mol to 200,000 g / mol, more preferably from 1 5,000 g / mol to 150,000 g / mol, and most preferably from 30,000 g / mol to 1 00,000 g / mol. All individual values and subranges from 10,000 g / mol to 200,000 g / mol are included herein and described herein. In another embodiment, the propylene homopolymer has a weight average molecular weight, (Mw) from 80,000 g / mol to 400,000 g / mol, more preferably from 1,00,000 g / mol to 300,000 g / mol and most preferably from 120,000 g / mol. mol up to 200,000 g / mol. All individual values and subranges from 80,000 g / mol to 400,000 g / mol are included herein and described herein.

Ethylene / α-olefin interpolymer The compositions of the invention comprise at least one ethylene / α-olefin interpolymer, which optionally can contain a diene. "Interpolymer", as used herein, refers to a polymer having at least two monomers polymerized therein. It includes, for example, copolymers, terpolymers and tetrapolymers. In particular it includes, a polymer prepared by polymerizing ethylene with at least one comonomer, usually an alpha olefin (α-olefin) of 3 to 20 carbon atoms (C3-C20), preferably 4 to 20 carbon atoms (C4-C20) ), more preferably 4 to 12 carbon atoms (C4-C12) and even more preferably 4 to 8 carbon atoms (C4-C8). The α-olefins include, but are not limited to, 1-butene, 1-pentene, 1 -hexene, 4-methyl-1-pentene, 1-heptene and 1-ketene. Preferred α-olefins include 1-butene, 1-pentene, 1-hexene, 4-methyl-1-pentene, 1-heptene and 1-ketene. The α-olefin is desirably a C4-C8 α-olefin. The interpolymers include ethylene / butene (EB), ethylene / hexene-1 (EH) copolymers, ethylene / octene (EO) copolymers, modified ethylene / α-olefin / diene interpolymers (EAODM), such as modified interpolymers of ethylene / propylene / diene (EPDM) and ethylene / propylene / octene terpolymers. Preferred copolymers include copolymers of EB, EH and EO. Suitable diene monomers include conjugated and non-conjugated dienes. The unconjugated diolefin may be a straight chain, branched or cyclic hydrocarbon diene of C6-C1 5. Illustrative non-conjugated dienes are straight chain acyclic dienes, such as 1,4-hexadiene and 1,5-heptadiene; branched chain acyclic dienes, such as, 5-methyl-1,4-hexadiene, 2-methyl-1,5-hexadiene, 6- methyl-1,5-heptadiene, 7-methyl-1,6-octadiene, 3,7-dimethyl-1,6-octadiene, 3,7-dimethyl-1,7-octadiene, 5,7-dimethyl-1, 7-octadiene, 1, 9-decadiene and mixed isomers of dihydromyrzene; single ring alicyclic dienes, such as 1,4-cyclohexadiene, 1,5-cyclooctadiene and 1,5-cyclododecadiene; fused and bridged ring alicyclic dienes of multiple rings, such as, tetrahydroindene, methyl fefrahydroindene; alkenyl, alkylidene, cycloalkylenyl and cycloalkuliden norbornenes, such as, 5-methyl-2-norbornene (MNB), 5-ethylidene-2-norbornene (ENB), 5-vinyl-2-norbornene, 5-propenyl-2-norbornene, 5-isopropylidene-2-norbornene, 5- (4-cyclopentenyl) -2-norbornene and 5-cyclohexylidene-2-norbornene. Preferred non-conjugated dienes include ENB, 1,4-hexadiene, 7-methyl-1,6-octadiene and more preferably the diene is ENB. Suitable conjugated dienes include 1,3-pentadiene, 1,3-butadiene, 2-methyl-1,3-butadiene, 4-methyl-1,3-pentadiene or 1,3-cyclopentadiene. Although the preferred interpolymers are substantially free of any diene monomer that normally induces LCB, one can include such a monomer, if the costs are acceptable, and the desirable interpolymer properties, such as processability, tensile strength and elongation, do not degrade an unacceptable level. Such diene monomers include, but are not limited to, dicyclopentadiene, NBD, methyl norbornadiene, vinyl norbornene, 1,6-octadiene, 1,7-octadiene and 1,9-decadiene. When added, such monomers may be added in an amount within the range of more than zero up to 3 weight percent, more preferably more than zero up to 2 weight percent, based on the weight of interpolymer.

The ethylene / α-olefin interpolymers of the invention can be branched and / or unbranched interpolymers. The presence or absence of branching in the ethylene / α-olefin interpolymers, and if the branching, the amount of branching, is present, can vary widely, and may depend on the desired processing conditions and the desired polymer properties. The nature of the ethylene / α-olefin (EAO) branching is not critical to the practice of this invention and as such, it may vary at convenience. Preferably, the branch is long chain branching (LCB). The ability to incorporate LCB into polymer backbones has been known and practiced for many years. In US Pat. No. 3,821,143, a 1,4-hexadiene was used as a branching monomer to prepare ethylene / propylene (diene) polymers having LCB Such branching agents are sometimes referred to as branching agents H. US Patents 6,300,451 and 6,372,847 also use various type H branching agents to prepare polymers having LCB In US Pat. No. 5,278,272, it was found that restricted geometry catalysts (CGC) have the ability to incorporate vinyl terminated macromonomers into the polymer backbone to form the LCB polymers Such branching is referred to as T-type branching. Each of these patents (US Patents 3,821, 143; 6,300,451; 6,372,847 and 5,278,272) is incorporated herein by reference in its entirety.

The '272 patent shows that such CGCs are unique in their ability to incorporate large unsaturated molecules into a polymer backbone. The amount of LCB that can be incorporated by these CGCs is usually from 0.01 LCB / 1000 carbon atoms to 3 LCB / 1000 carbon atoms (both branched and skeleton carbon atoms). Preferably, the type of LCB in the interpolymers used in the practice of this invention is T-type branching, as opposed to H-type branching. The T-type branching is usually obtained by copolymerization of ethylene or other alpha-olefins with unsaturated end-chain macromonomers in the presence of a restricted geometry catalyst under the appropriate reactor conditions, such as those described in WO 00/26268 (equivalent U.S.A., U.S. Patent 6,680,361, incorporated herein by reference in its entirety). If extremely high levels of LCB are desired, branching type H is the preferred method, because the T-type branch has a practical upper limit to the degree of LCB. As discussed in WO 00/26268, as the level of branching type T increases, the efficiency or performance of the manufacturing process decreases significantly, until the point where production becomes economically non-viable is reached. LCB type T polymers can be produced by catalysts of restricted geometry, without measurable gels, but with very high levels of LCB type T. Because the macromonomer being incorporated into the growing polymer chain has only one site of reactive unsaturation, the resulting polymer only contains side chains of varying lengths and at different intervals along the polymer backbone. Type H branching is usually obtained by copolymerization of epylene or other alpha-olefins with a diene having two reactive double bonds with a non-mephalocene type of catalyst in the polymerization process. As the name implies, the diene joins one polymer molecule to another polymer molecule through a diene bridge; the resulting polymer molecule resembles an H that could be described as more of a crosslinking than a long chain branching. Type H branching is normally used when extremely high levels of branching are desired. If too much diene is used, the polymer molecule can form so much branching or cross-linking that the polymer molecule is no longer soluble in the reaction solvent (in a solution process), and consequently falls out of solution, resulting in the formation of gel particles in the polymer. Additionally, the use of type H branching agents can deactivate the metallocene catalysts and reduce the catalyst efficiency. Thus, when branching agents type H are used, the catalysts used are usually non-mephalocene catalysts. The catalysts used to prepare branched polymers type H in US 6,372,847 (incorporated herein by reference in their entirety) are vanadium type catalysts. Suitable ethylene interpolymers include polymers ENGAGEM R, AFFIN ITYM R, and NORDEL R available from Dow Chemical Company and VISTALONMR and EXACT R polymers available from ExxonMobil Chemical Company, and TAFMER R polymers available from Mitsui Chemical. Preferred ethylene interpolymers include ENGAGEMR and AFFI N ITYM R polymers available from Mitsui Chemical. In another embodiment, the ethylene / α-olefin interpolymer has a molecular weight distribution (Mw / Mn) from 1 to 5, more preferably from 1.5 to 4 and most preferably from 2 to 4. 3. All individual values and subranges from 1 to 5 are included herein and described herein. In another embodiment, the ethylene / α-olefin interpolymer has a density from 0.80 to 0.90 g / cm3, preferably from 0.82 to 0.88 g / cm3, and more preferably from 0.87 g / cm3. All individual values and subranges from 0.80 to 0.90 g / cm3 are included herein and described herein. In another embodiment, the ethylene / α-olefin interpolymer has a density less than or equal to 0.875 g / cm 3, preferably less than or equal to 0.86 g / cm 3, and more preferably less than or equal to 0.85 g / cm3. In another embodiment, the ethylene / α-olefin interpolymer has a melt index, 12 (190 ° C / 2.16 kg) from 0.05 to 10 g / 10 min, preferably from 0.1 to 5 g / 10 min, and more preferably from 0.2 to 2 g / 1 0 in, or 0.5 to 1 g / 10 min. All individual values and subranges from 0.5 to 10 g / 10 min are included in this and described herein. In another embodiment, the elastomer component has a melt index, 12, of 1 g / 10 min or smaller, preferably 0.5 g / 10 min or less, and more preferably 0.3 g / 10 min or less. In another embodiment, the ethylene / α-olefin interpolymer has a number average molecular weight (Mn), from 40,000 g / mol to 200,000 g / mol, more preferably from 50,000 g / mol to 150,000 g / mol, and most preferably from 60,000 g / mol to 100,000 g / mol. All individual values and subranges from 40,000 g / mol to 200,000 g / mol are included herein and described herein. In another embodiment, the ethylene / α-olefin interpolymer has a weight average molecular weight, (Mw) from 80,000 g / mol to 400,000 g / mol, more preferably from 1,00,000 g / mol to 300,000 g / mol, and very preferably from 120,000 g / mol to 200,000 g / mol. All individual values and subranges from 80,000 g / mol to 400,000 g / mol are included herein and described herein. In another embodiment, the ethylene / α-olefin interpolymer has a Tg less than -30 ° C, preferably less than -40 ° C, and more preferably less than -50 ° C. In another embodiment, the ethylene / α-olefin interpolymer is a substantially linear, homogeneously branched, or homogeneously branched linear ethylene / α-olefin interpolymer. Processes for preparing homogeneous polymers are described in U.S. Patent 5,206,075; U.S. Patent 5,241, 031; and international patent application WO 93/03093; each of which is incorporated herein by reference in its entirety. Additional dls regarding the production of ethylene / a-copolymers homogeneous olefins are described in U.S. Patent 5,206,075; U.S. Patent 5,241, 031; PCT international publication number WO 93/03093; PCT International Publication No. WO 90/03414; the four incorporated in the present in their entirety, by reference. The terms "homogeneous" and "homogeneously branched" are used in reference to an ethylene / α-olefin polymer (or interpolymer), in which the comonomer (s) is randomly distributed within a given polymer molecule, and substantially all the Polymer molecules have the same proportion of ethylene-to-comonomer (s). Homogeneously branched ethylene interpolymers include linear ethylene interpolymers and linear subsfunctional epylene lowerpolymers. Included among linear homogeneous branched epylene inferpolymers are the ethylene inferpolymers, which lack long chain branching, but have short chain branches, derived from the comonomer polymerized in the interpolymer, and which are homogeneously distributed, both within the same polymer chain as between different polymer chains. That is, homogeneous branched linear epylene inferpolymers lack long chain branching, just as is the case with linear low density polyethylene polymers or linear alpha density polyethylene polymers, made using uniform branching distribution polymerization processes. , as described, for example, by Elston in the U.S. patent 3,645,992. Commercial examples of homogeneously branched linear ethylene / α-olefin interpolymers include TAFMER R polymers provided by Mitsui Chemical Company and EXAC ™ R polymers supplied by ExxonMobil Chemical Company. The linearly subsidiary ethylene interpolymers used in the present invention are described in U.S. Pat. 5,272,236 and 5,278,272; the complete contents of each of which are incorporated herein by reference. As discussed above, the linear subfunctional epylene interpolymers are those in which the comonomer is randomly distributed within a given interpolymer molecule, and in which, sub-polymerically, all the inferpolymer molecules have the same proportion of ethylene / comonomer within that molecule. iníerpolímero. The substantially linear ethylene interpolymers are prepared using a catalyst of restricted geometry. Examples of restricted geometry catalysts, and such preparations, are described in US Pat. 5,272,236 and 5,278,272.

In addition, the subsfanocially linear epylene interpolymers are homogeneously branched ethylene polymers having long chain branching. The long chain branches have approximately the same comonomer distribution as the polymer backbone and can have approximately the same length as the length of the polymer backbone. As discussed above, "substantially linear" is usually in reference to a polymer that is substituted, on average, with 0.01 branches of long chain for 1 000 total carbons (including both skeletal and branching carbons) up to 3 long chain branches per 1000 total carbons. Commercial examples of substantially linear polymers include ENGAGE R polymers (Dow Chemical Company) and AFFINITY ™ polymers (Dow Chemical Company). The substantially linear ethylene interpolymers form a unique class of homogeneously branched ethylene polymers. They differ substantially from the well-known class of linear, homogeneously branched, linear ethylene interpolymers described by Elston in US Pat. No. 3,645,992 and, furthermore, are not in the same class as linear ethylene polymers polymerized with conventional heterogeneous Ziegler-Natta catalyst. (e.g., ultra low density polyethylene (ULDPE), linear low density polyethylene (LLDPE) or high density polyethylene (HDPE), made, for example, using the technique described by Anderson et al., in US Patent 4,076,698 ); they are not in the same class as highly branched polyethylenes, initiated with free radicals, of alpha pressure, such as, for example, low density polyethylene (LDPE), ethylene-acrylic acid copolymers (EAA) and ethylene / acetate copolymers of vinyl (EVA).

Laminated filler Any inert material with a generally disk-like shape can be used as the laminated filler in the TPO compositions of this invention. Typically and preferably, the laminated filler is an inert mineral powder, for example, talc, kaolin clay or mica, and more preferably is a laminated talc. The common rolled talcs and kaolin clays are identified in Tables 3 and 4, respectively. The particular degree of laminate falck is selected to have sufficient reinforcing force, in order to impart or maintain the desired flexural modulus and HDT of the final composition, without exceeding the density of the polymeric resin that is intended to replace the composition. Normally, the density of a commercial grade resin is approximately 1 .13 g / ml. For compositions made with the propylene homopolymers, high crystallinity and EAO elastomers of this invention, a filler loading of about 30 weight percent is typical, although more or less can be used as desired.

Table 3: Common rolled talcs.

Table 4: Common laminated kaolin clays During the processing of the inventive compositions, it is noted that under a flow stress, the padding formed of plate will generally be aligned parallel to the direction of composition flow. This flow pattern helps to reduce shrinkage of the composition in the direction of flow and makes it possible for the filling to strengthen the resulting polymer product, increasing both the heat deflection temperature and the flexural modulus. The Particular fill effectiveness can be determined by adjusting a line to data taken at various levels of filler addition. The inclination of the line, in units of "percentage increase in property" divided by "percentage by weight of filling addition" is a measure of the particular filling efficiency to increase either the heat deflection temperature or modulus of flexion. The filling reinforcement efficiency in the composition is evaluated by measuring the effect of a 20 percent addition of the filler in the flexural modulus and HDT of the polypropylene and EAO mixture. An efficiency factor of flexural modulus, with units of percent increase in modulus to fill filler percentage, can then be calculated. This factor is relatively linear in a range of filler loading from about 10 to 40 weight percent. A related heat deflection efficiency factor can be calculated similarly for each fill degree by compounding the high crystallinity, isotactic propylene homopolymer, and EAO elastomeric impact modifier with 20 percent by weight reinforcing filler. and without the filling. The heat deflection efficiency factor is less linear than the flexural modulus efficiency factor, and more sensitive for the specific grade of polypropylene and EAO. As a result, the fillers of interest are usually compared to a 20 weight percent filler with the highly crystalline isotactic homopolymer and EAO elastomeric impact modification of this invention. Preferred reinforcement filler grades, eg, talc laminate, of this invention they have a heat deflection efficiency factor greater than, or equal to, about 1.5, more preferably greater than about 1.7, and most preferably greater than 1.09, when formulated at 20 weight percent fillers in the highly crystalline isotactic propylene homopolymer and EAO elaspheres impact modifier. Simultaneously, the preferred reinforcing filler grades of this invention have a flexural modulus efficiency factor greater than about 3, more preferably greater than about 3.5 and most preferably greater than about 4. In one embodiment, the particle size medium is from 0.1 microns to 50 microns, preferably from 0.5 microns to 25 microns, and more preferably from 1 micron to 10 microns. All individual values and subranges from 0.1 miera to 50 micras are included in this and described herein.

Preparation of compositions As discussed above, the TPO compositions of this invention contain at least one propylene homopolymer, at least one ethylene / α-olefin ether polymer and at least one laminated filler. Although such compositions can be prepared by one of a variety of different processes, generally these processes fall into one of two categories, i.e., post-reactor mixing, in-reactor mixing or combinations thereof. Illustrative of the foregoing are melt extruders in which two or more solid polymers are fed and physically blended into a substantially homogeneous composition, and multiple solution, paste or gaseous phase reactors, arranged in a parallel arrangement, and in which, the performance of each is mixed with the other to form a substantially homogeneous composition, which is finally recovered in solid form. Illustrative of the above are the multiple reactors connected in series and simple reactors loaded with two or more catalysts. Preferably, the compositions are prepared by post-reactor mixing. Normally, the propylene homopolymer and ethylene / α-olefin interpolymer are mixed with each other, before the addition of the filler, although the filler can be mixed first with one or the other of the polymers before the addition of the other polymer. The filler can be added pure or as a master batch, based on any polymer. All the components of the composition are mixed with each other, until a substantially homogeneous composition is obtained. Standard mixers and extruders can be used for mixing. The compositions of this invention may contain other components as well; for example, pigments, anti-oxidants, processing aids and the like. The TPO compositions of this invention are used in the same manner as conventional polycarbonate bases and polysulfur-based compositions. In particular, the compositions of this invention are well suited for the manufacture of structures used in the preparation of instrument panels of soft touch and similar articles of manufacture.

Composition The preferred inventive composition contains from 60 to 90 percent by weight, preferably from 65 to 85 percent by weight, and more preferably from 70 to 75 percent by weight of the propylene homopolymer, based on the sum of weight of propylene homopolymer and ethylene / α-olefin interpolymer. All individual values and subranges from 60 to 90 weight percent (polypropylene homopolymer) are included herein and described herein. The inventive composition preferably contains from 10 to 40 weight percent, preferably from 15 to 37 weight percent, and more preferably from 20 to 35 weight percent of the ethylene / α-olefin inferpolymer, based on the weight sum of the propylene homopolymer and ethylene / α-olefin interpolymer. All individual values and subranges from 10 to 40 weight percent (eitlene / α-olefin interpolymer) are included herein and described herein. In a modality, the composition contains from 25 to 50 percent by weight, preferably from 30 to 45 percent by weight, and more preferably from 35 to 40 percent by weight of laminated filler, based on the total weight of the composition. All individual values and subranges from 25 to 50 weight percent (rolled filler) are included herein and described herein.

In another embodiment, the composition has a crystallization temperature, Te, greater than, or equal to, 1 10 ° C, preferably greater than, or equal to, 120 ° C, and more preferably greater than, or equal to, 130 ° C, and most preferably greater than or equal to, 140 ° C. In another embodiment, the composition has an HDT, as measured by ASTM D648, which, or equal to, 10 ° C, preferably greater than, or equal to, 120 ° C and more preferably greater than, or equal to, 1 30 ° C, and most preferably greater than, or equal to, 140 ° C. In another embodiment, the composition does not contain another propylene-based polymer, other than the propylene homopolymer component. In another embodiment, the composition contains more than, or equal to, 50 weight percent, preferably more than, or equal to, 60 weight percent, and more preferably more than, or equal to, 70 weight percent of the propylene homopolymer, based on the total weight of the composition.

In another embodiment, the composition contains less than, or equal to, 40 weight percent, preferably less than, or equal to 35 weight percent, and more preferably less than, or equal to, 30 weight percent of the ethylene / α-olefin interpolymer, based on the total weight of the composition. In another embodiment, the composition does not contain copolymers containing only ethylene and propylene monomer units. In another embodiment, the composition does not contain styrene block copolymers. In another embodiment, the composition contains only one interpolymer of ethylene / α-olefin. In another embodiment, the composition does not contain an EPDM polymer. In another embodiment, the composition does not contain an EPR polymer. In another embodiment, the composition does not contain a block copolymer. The composition may further comprise at least one additive of the type conventionally added to polymers or polymer compositions. These additives include, for example, process oils; anfioxidanfes; surface tension modifiers; UV stabilizers; flame retardants, scratch / damage additives, such as polydimethyl siloxane (PDMS) or functionalized polydimethyl siloxane or IRGASURF® SR 100 (available from Ciba Specialty Chemicals) or damage scratch formulations containing erucamide; anti-blocking agents; dispersants; blowing agents; Linear or substantially linear EAOs; LDPE; LLDPE; lubricants; crosslinking agents such as peroxides; antimicrobial agents such as organometallic, isothiazolone, organoazulf and mercaptan; antioxidants such as phenolics, secondary amines, phosphites and thioesters; antistatic agents, such as quaternary ammonium compounds, amines and ethoxylated, propoxylated or glycerol compounds. The functionalized polydimethyl siloxanes include, but are not limited to, hydroxyl-functionalized polydimethyl siloxane, amine-functionalized polydimethyl siloxane, functionalized polydimethyl siloxane with vinyl, polydimethyl siloxane functionalized with aryl, polydimethyl siloxane functionalized with alkyl, polydimethyl siloxane functionalized with carboxyl, polydimethyl siloxane functionalized with mercaptan and derivatives thereof. The inventive compositions may also contain an additional additive. Additional additives include, but are not limited to, hydrolytic stabilizers; lubricants such as fatty acids, fatty alcohols, esters, fatty amides, metal stearates, paraffinic and microcrystalline waxes, silicones and esters of orthophosphoric acid; mold releasing agents, such as fine or powdered particulate solids, soaps, waxes, silicones, polyglycols and complex esters such as trimethylolpropane tristearate or pentaerythritol fefra stearate; pigments, dyes and colorants; plasticizers, such as esters of dibasic acids (or their anhydrides) with monohydric alcohols, such as, o-phthalates, adipates and benzoates; heat stabilizers, such as organotin mercaptans, a phyloglycolophilic acid ester and a barium or cadmium carboxylaph; ultraviolet light stabilizers used as an obstructed amine, an o-hydroxy-phenylbenzotriazole, a 2-hydroxy, 4-alkoxy-benzophenone, a salicylate, a cyanoacrylate, a chelating nickel and a malonate of benzylidene and oxalanilide; and zeolites, molecular sieves, antistatic agents and other known deodorants. A preferred clogged antioxidant is antioxidant Irganox® 1 076, available from Ciba Specialty Chemicals. Expert technicians can easily select any suitable combination of additives and amounts of additive, as well as the method for incorporating the additive (s) into the composition, without undue experimentation. Normally, each of the above additives, if used, does not exceed 45 weight percent, based on the total composition weight, and is advantageously from about 0.001 to about 20 weight percent, preferably from 0.01 to 15 percent by weight and more preferably from 0.1 to 10 percent by weight. In one embodiment of the invention, a composition includes at least one polydimethylsiloxane (PDMS) to improve the scratch / damage resistance of the resulting product. The polydimethylsiloxane is usually present from 0.1 to 10 weight percent, based on the weight of the polymer composition. Suitable polydimethylsiloxanes include those having a viscosity of 25 ° C greater than 100,000 centistokes, and more preferably from 1 × 10 6 to 2.5 × 10 6 centistokes. In a further embodiment, the composition also includes an ethylene homopolymer or ethylene interpolymer grafted with succinic anhydride or maleic anhydride groups, and preferably the grafted ethylene homopolymer or interpolymer comprises less than 20 percent of said composition. Still in a further embodiment, the composition also includes at least one additive, such as a plasticizer, a pigment or dye, a UV stabilizer or a filler. Fillers may include calcined or uncalcined fillings. Suitable fillers include, but are not limited to, calcium carbonate and wollastonite. The components suitable for formulations resistant to scratch damage are described in more detail in USP 5,902,854, the content of which is incorporated herein by reference. Additional scratch damage formulations useful in the compositions of the invention contain IRGASURF® SR 100 with one or more additives as described herein. A particularly suitable formulation contains an aliphatic amide in a polyethylene carrier, such as I RGASURF® SR 100 with one or more fillers, such as wollastonite, and an ethylene homopolymer or interpolymer grafted with maleic anhydride or succinic anhydride groups. Other scratch-resistant polyolefin formulations are described in US publication no. 2006009554 (equivalent to WO 2006/0031 27), which is incorporated herein in its entirety by reference. In a particularly preferred embodiment, the compositions contain a scratch damage concentrate, which in turn, contains from 10 to 30 weight percent of at least one dye and / or UV stabilizer, from 5 to 1 5 weight percent of at least one polydimethylsiloxane, from 30 to 50 weight percent of at least one filler and from 10 to 35 weight percent of at least one homopolymer or ethylene interpolymer grafted with maleic anhydride or succinic anhydride groups. Percentages by weight based on the total weight of the scratch / damage concentrate.

Automotive articles Articles can be prepared by a variety of processes. They can be injection molded, blow molded, compression molded, injection molded at low pressure, extruded and then thermoformed by either vacuum casting male or female, or prepared by hybrid process, such as, low pressure molding, wherein a blanket of still molten TPO material is placed against the back of a skin foam composite and pressed under low pressure to form the skin and bond it to the hard TPO substrate. Articles, or components of such articles, that may be made by these processes include, but are not limited to, instrument panel refectors, overcoats, valence panels (closed windshield panel), instrument beam bezels, center console bezels , interior and exterior of glove boxes, columns and posts, pillars A, B and C, all areas and storage covers stocked, and under the chest parts, such as ventilation housings. The inventive compositions are sufficiently fluid at molding temperatures to fill a mold. Overall, the inventive compositions have excellent moldability and alpha rigidity, and can be used to form parts with excellent mechanical strength, impact resistance, ductility and resistance to thermal deformation. Such parts have an excellent appearance and have reduced dimensional changes, at the moment of molding, and reduced coefficients of thermal linear expansion. The compositions are capable of producing injection molded parts having a thickness of wall smaller than that of the parts prepared from conventional PC / ABS resins. In addition, such parts are in the order of seven percent by weight lighter than a polycarbonate / ABS blend. The automotive parts of the invention can be prepared using injection molding tool work designed for conventional PC / ABS resins. In this way, the inventive parts can be prepared using existing automotive equipment.

DEFINITIONS Any numerical range stated herein, includes all values of the inferred value and the upper value, in increments of one unit, provided there is a separation of at least two units between any lower value and any higher value. As an example, if it is stated that a property of composition, physical or otherwise, such as, for example, molecular weight, melt index, etc. , it is from 1 00 to 1, 000, it is intended that all individual values, such as, 100, 101, 1 02, etc., and sub-ranges, such as 100 to 144, 1 55 to 170, 197 to 200, etc. , are expressly listed in this specification. For ranges containing values which are less than one, or containing fractional numbers greater than one (eg, 1 .1, 1 .5, etc.), a unit is considered to be 0.0001, 0.001, 0.01, or 0.1, as appropriate . For ranges containing numbers of simple digits less than ten (for example, 1 to 5), a unit is normally considered 0.1. These are just examples what is specifically intended and all possible combinations of numerical values between the lowest value and the highest value listed, will be considered as expressly declared in this application. Numerical ranges have been declared, as discussed herein, in reference to density, component weight percentage, tan delta, molecular weights and other properties. The term "composition", as used herein, includes a mixture of materials which comprise the composition, as well as reaction products and decomposition products formed from the materials of the composition. The term "polymer", as used herein, refers to a polymeric compound prepared by polymerizing monomers, either the same or of a different type. The term generic polymer thus embraces the term homopolymer, usually used to refer to polymers prepared from a single type of monomer and the term interpolymer as defined hereinafter. As discussed above, the term "interpolymer," as used herein, refers to polymers prepared by the polymerization of at least two different types of monomers. The generic term "interpolymer" thus includes copolymers, usually used to refer to polymers prepared from two different types of monomers and polymers prepared from more than two different types of monomers. The term "ethylene / α-olefin interpolymer", "epylene polymer" or similar terms, as used herein, refers to a polymer formed from predominantly (more than 50 mole percent) monomeric units of ethylene. The mole percentage is based on the total moles of polymerizable monomers. The terms "mixture" or "polymer mixture", as used herein, mean a composition of two or more polymers. Such a mixture can be miscible or not. Such a mixture can be separated in phases or not. Such a mixture may or may not contain one or more domain configurations, as determined from electron transmission spectroscopy.

MEASUREMENTS By the term "Ml" is meant melt index, 12 or l2, in g / 10 min, measured using ASTM D-1238-04, Condition 1 90 ° C / 2.16 gkl for polymers based on polyethylene and 230 ° C /2.16 kg for polypropylene-based polymers. The density is measured in accordance with ASTM D-792-00. The density was measured as a "fast density", meaning that the density was determined after 1 hour of the molding time.

Gel Permeation Chromatography The average molecular weights and molecular weight distributions for epylene based polymers were determined with a gel permeation chromatographic system, consisting of a high temperature chromatograph of Polymer Laboratories model 2000 series. The carousel and column were operated to 140 ° C for polymers based on polyethylene. The columns used were three B columns mixed with 10 micras of Polymer Laboratories. The solvent was 1, 2,4-trichlorobenzene. The samples were prepared at a concentration of 0.1 gram of polymer in 50 milliliters of solvent. The solvent, used as the mobile phase, and to prepare the samples, contained 200 ppm of buffered hydroxyfuene (BHT). The epylene based polymers were prepared by stirring slightly for 2 hours at 160 ° C and polymers based on propylene were dissolved for 2.5 hours. The injection volume was 100 microliters and the flow rate was 1.0 milliliters / minute. The calibration of the GPC column set was performed with narrow molecular weight distribution polystyrene standards, purchased from Polymer Laboratories (UK), with molecular weights ranging from 580 to 8,400,000. The standard polysulfone peak molecular weights were converted to molecular weights of polyethylene using the following equation (as described in Williams and Ward, J. Polym, Sci., Polym, Let., 6, 621 (1968)): Mpolyethylene = A x (Mpolystyrene) where M is the molecular weight, A has a value of 0.4315 and B is equal to 1.0. The polyethylene equivalent molecular weight calculations were performed using the Viscotek TriSEC computer program version 3.0. Molecular weights for polypropylene-based polymers can determined using proportions of Mark-Houwink in accordance with ASTM D6474.9714-1, where, for polystyrene a = 0.702 and log K = -3.9 and for polypropylene, a = 0.725 and log K = -3.721. For samples based on polypropylene, the carousel and column compartments were operated at 160 ° C.

Differential Scan Calorimetry Differential Scanning Calorimetry (DSC) can be used to measure crispness in polyethylene (PE) based samples and polypropylene (PP) based samples. A sample is pressed into a thin film at a temperature of 190 ° C. Approximately up to eight milligrams of film sample is weighed and placed on a DSC tray. The lid is curled in the tray to assure a wrong atmosphere. The sample tray is placed in a DSC cell and then heated, at a rate of about 1 0 ° C / min, to a temperature of about 180-200 ° C for PE (230 ° C for PP). The sample is kept at this temperature for several minutes. The sample is then cooled at a rate of 1 0 ° C / min to -90 ° C for PE (-90 ° C for PP), and isothermally maintained at that temperature for three to five minutes. The sample is heated again at a speed of 10 ° C / min until full fusion (second heat, around 180 ° C for PE and 230 ° C for PP). Unless stated otherwise, the melting point (s) (Tm) of each polymer sample is determined from the second heat curve obtained from DSC, as described before. The crystallization temperature (Tc) is measured from the first cooling curve. The following examples illustrate, but do not limit, either explicitly or by implication, the present invention. Unless otherwise indicated, all parts and percentages are by weight.

EXPERIMENTAL PHASE Five grades of polypropylene are described in Table 5 below. Profax PD 702 is a conventional propylene homopolymer sold by Basell. JP 707 is a heterophasic propylene propylene copolymer copolymer, prepared, in situ, conventional propylene and ethylene sold by Mitsui Chemicals, I nc. Accpro 9934X, now identified as Innovene H35Z-02, is a nucleated, highly crystalline, 35 MF isotactic propylene homopolymer. D1 18 is a developing, highly nucleated, crystalline propylene homopolymer available from the Dow Chemical Company. This polymer has an Mn of about 41.00 g / mol, an Mw of about 183,000 g / mol and an Mw / Mn of about 4.5.

CDC-1 is a propylene homopolymer version of D1 18 without the nucleant that was broken again with cutting and peroxide at a melt index of 35. CDC-2 is another version of propylene homopolymer D1 18, but this version was prepared with a nucleating agent and then broke again at MFR of 35.

Table 5: Polypropylene properties The nucleation effect can be clearly seen by examining the physical properties of the CDC grades.

Many elastomeric EAO impact modifiers are available for use in the practice of this invention, including ethylene / octene, ethylene / buiene and ethylene / propene copolymers. ENR 7380 is a preferred EAO elasíomer for impact modification due to its low Tg balance, delta as low average at 190 ° C and 0.1 radians per second, and a differential between its melting point and HDT of 10.3 ° C. In the compositions described below, the polypropylene homopolymer and the ethylene / α-olefin were mixed in a twin-screw extruder, without a laminated filler. The polymers were fed at 13608 kg / h (30 Ib / h) of combined feed speed. The screws were rotated at 300 rpm. The temperatures were set at 200 ° C for the barrel zones after the initial feed zone and for the transition and die. The pellets were prepared with a Gala underwater pelletizer. The modification to impact results in a drop of both flexural modulus and HDT of the polypropylene as shown in Tables 6 and 7 below. All formulations were prepared using 70 weight percent of the chosen polypropylene and 30 weight percent of the EAO chosen; each percentage by weight is based on the sum of weight of polypropylene and EAO. The Engage R series 8000 elastomers are copolymers of epylene and 1-butene. EngageM R 8100 has an Mn of approximately 75,000 g / mol, an Mw of approximately 150,000 g / mol and an Mw / Mn of 2.0. EngageM R 81 50 has an Mn of approximately 87,000 g / mol, an Mw of approximately 176,000 g / mol and one Mw / Mn of 2.0. ENRM R 7380 has an Mn of approximately 82,000 g / mol, an Mw of approximately 174,000 g / mol and an Mw / Mn of 2.1. Table 6: Impact modification effect on flexural modulus, 1% secant modulus, MPA The data in Table 6 show that the percentage of loss in modulus of flexion (1% of secant modulus) will not significantly change within this group of elastomers. Similar co-behavior is seen with the percent lost in HDT as shown in Table 7 below (approximately 25 percent of the HDT, with respect to polypropylene and independent of the elastomer). Once again the properties shown are for pure polymer blends of 70 weight percent of the selected polypropylene and 30 weight percent of the selected elastomer.

Table 7: Effect of modification by impact on heat deflection temperature (° C) The importance of laminate fillings is its reinforcing nature. Table 8 below shows the falco addition effect, at a level of 10 weight percent, in the flexural modulus of each of the conventional polypropylene grades. The second part of the table shows how 10 and 20 weight percent of different mill levels increase the modulus of flexion of a polypropylene of random copolymer, modified by impact with various grades of EAO to 30 percent, by weight, in an epoiemro base. In each case, the weight percentage of talc is based on the sum of the weight of polypropylene, EAO and talc. One skilled in the art would know how to formulate the compositions (percentages of polypropylene, EAO and filler components) to compensate for additional additives, such as color concentrates and other additive concentrates. For the study of the effects of individual degrees of falco, two grades of polypropylene (a homopolymer and an impact copolymer) were modified by impact with 8 different grades of EAO and 3 different grades of talc. Polypropylene grades were a 35 MFR homopolymer, Basell Profax PD702, and a 35 MFR impact copolymer, J707PT (heterophasic PER or EPR impact polypropylene, prepared in the reactor and sold by Grand Polymers). The compounds were prepared by feeding the selected polypropylene, the selected elasfomer and the selected falco to a double screw exfruser under conditions used in the previous study. The proportion of polypropylene to elasfomer was set at 70 weight percent polypropylene to 30 weight percent elasperomer; each percentage by weight is based on the sum of weight of polypropylene and EAO. When the compounds were prepared from J707PT, this practice actually resulted in two elastomers that are present in the final compound, the first of the two-phase polypropylene copolymer, the second of the compound formation. The proportion of polypropylene to epylene elaspheres fed to the frother was kept constant at 70 to 30 parts by weight. The polymer feed was adjusted and the talc was increased, so that the falco content hits the target amount. In this manner, a formulation containing a total of 10 percent in such was prepared with 63 weight percent polypropylene, and 27 weight percent elastomer and 10 weight percent talc. Similarly, a 20 weight percent talc formulation contained 56 weight percent of the chosen polypropylene grade, 24 weight percent of the chosen elastomer, and 20 weight percent talcum chosen one.

Table 8: Percentage of increase in 1% secant modulus with the addition of 10 percent and 20 percent talc charges to blends of polypropylene and ethylene non-nucleated alpha-olefins Another way to express this same information that normalizes the response to individual grades of talc at several levels, is to express the same information as the percentage increase in flexural modulus per talc loading percentage. This description is defined as the efficiency factor of non-nucleated flexural modulus, is dimensionless, and is reported in Table 9 below.

Table 9: Non-nucleated flexural modulus efficiency factor A similar study can be made about the effect of reinforcement filler in HDT. Due to the difference between the HDT of the degrees With conventional polypropylene and EAO is relatively small, the impact modification effect is lower than expected for the highly crystalline isotactic homopolymer grades of polypropylene, as reported in Table 10 below.

Table 10: Efficiency factor of non-nucleated HDT As seen in Tables 9 and 10 above, the reinforcement filler it can be compared commercially for its efficiency by increasing HDT (ASTM D648, 0.455 MPa) and 1% secant flexural modulus (ASTM D790). On the basis of these efficiency factors, one can compare filling choices to prepare a TPO composition with properties equivalent to those of conventional resins, such as PC / ABS. Of the grades of talc laminate reported in the tables above, Cimpact 710 offers the best balance of properties. The above reported polypropylene grades were not nucleated. The formation of a composite composition of TPO with talc is known to result in the nucleation of polypropylene due to the large surface area and irregular shape of the falco. Therefore, some of the benefit of adding falco is the nucleation effect of falco. Because most grades of highly crystalline isotactic polypropylene homopolymer, as sold, are nucleated to accentuate their stiffness (flexural modulus) and HDT, the performance of both nucleated and non-nucleated grades was evaluated. The results are reported in Table 1 1 below. For this study, we chose to use a highly crystalline homopolymer polypropylene with an MFR of 35. In the first case, this grade was produced without a nucleating agent and was labeled CDC0501. This material was prepared again, only this time the nucleating agent was added before breaking the polymer again. This nucleated grade was labeled CDC0505. In both cases, the impact modified blends were prepared using 70 weight percent of the highly crystalline polypropylene respective, and 30 weight percent of the ethylene / 1-butene copolymer, ENR 7380, but without talc feed to the extruder. In subsequent runs, each highly crystalline polypropylene was made in a falco filled composite, modified on impact, by feeding the polypropylene, the elastomer and the talcum to the twin screw extruder at the appropriate proportions. Compositions containing 20 percent talc received 56 percent by weight feeds of polypropylene, 24 percent by weight of ENR 7380 and 20 percent by weight of talc. Compositions containing 30 weight percent talc, received feeds of 49 weight percent polypropylene, 21 weight percent ENR 7380 and 30 weight percent falco. Finally, compositions containing 40 weight percent talc, received feedings of 42 weight percent polypropylene, 1 8 weight percent ENR 7380 and 40 weight percent talc. The properties were measured and reported in Table 1 1.

Table 1 1: Consequences of impact modification and talc loading for polypropylene of alpha-crystallinity, non-nucleated and nucleophilic isoplast homopolymer * addition of 35% talc The nucleation benefits are clearly visible in the pure propylene homopolymer resulting in an HDT that is 25.9 degrees higher and 1% secant modulus that is almost 5975.5 kg / cm2 (85,000 psi) higher. The benefits decrease after impact modification with 30 weight percent of the total polymer (polypropylene and EAO) addition of ENR 7380 to make a TPO composition. The difference in flexural modulus is less than 2109 kg / cm2 (30,000 psi), and the difference in HDT is less than 1 1 ° C. Once the TPO compositions are filled with falco, the nucleation advantage is lost. This data allows the commercial comparison of a flexural modulus of 9986.60 kg / cm2 (142057 psi) and a HDT of 85.6 ° C to evaluate the reinforcing effects of reinforcement fillers. This is useful because the most common commercial grades of highly crystalline isotactic propylene homopolymer are all nucleated for the impulse in modulus of flexion and HDT. With the correlation developed above, the alternating reinforcement laminates can be classified into a standard formulation based on the highly crystalline, nucleated, isotactic propylene homopolymer, more widely available. The formulation of The polymer is 70 weight percent of the highly crystalline, nucleated, isoplactic propylene homopolymer, up to 30 weight percent EAO elastomeric impact modifier. For the following fill efficiency comparison, Accpro 9934X polypropylene and EAO EN R 7380 were used. The various grades of laminated fillings examined included delaminated kaolin clay and laminated falco derived from Canadian sources, as described in Table 12 to continuation. Table 12: Effect of laminated fillers on modified PP homopolymer with EAO Using 9986.60 kg / cm2 (142057 psi) as the modulus of flexure for the modified impact formulation, unfilled, non-nucleated, and a non-nucleated flexural modulus efficiency factor of 3, a 20 percent by weight charge of Fill should carry the flex module at 15978.55 kg / cm2 (227.291 psi). Similarly, a reinforcing filler that meets the requirement of this invention of an HDT efficiency factor of 1.5, would simultaneously have an HDT of 1 1 1 .3 ° C. JetFil laminated talc grades meet these requirements, but grades of kaolin do not. The formulation can be adjusted by increasing the elastomer content (EAO) as a percentage of total polymer (polypropylene plus elastomer), in order to improve the impact resistance at low temperature. The results of this are shown as Version A. Alternatively, both the elastomer content and the talc content as a percentage of the total compote (polypropylene plus elasfomer plus falco). The results of this change are shown as Version B.

Table 13: Adjust the composition to adjust the properties These formulations were used to evaluate the material for injection molding of large structural automotive structures, such as valence panels, overcoats and retainers. The evaluations consisted of several main parts: confirmation of the material's ability to fill the tools in a manner equivalent to PC / ABS and available commercially available TPO grades used for injection molding; evaluation of the characteristics of material shrinkage both during the molding of the parts and after several weeks at room temperature; and finally injection molding of an instrumental panel retainer, followed by the use of foaming technology in place create an instrumental panel. The instrument panel can then be tested for performance compared to the choice of material currently in use. Version B of Table 13 above was tested for its flow characteristics in large scale injection molding by using a grained panel tool with an opening of 91.44 cm (36 in) in length, 25.4 cm (10 in. in) of width and 2.6 mm of thickness. The tool provided with a central door, giving a maximum polymer flow length of about 50.8 cm (20 in). There was no problem filling this tool, with a very wide processing window ranging from a low speed injection speed of 0.508 cm / s (0.2 in / s) to an injection speed of 5.08 cm / s (2 in / s) ). The injection molding machine had problems maintaining the hydraulic pressure at this point because it was designed to deliver higher flow rates at this pressure. The speed of injection, the time for transfer, and the peak injection pressure are tabulated in Table 14 below.

Table 14: Evaluation of mold filling A commercially available PC / ABS, which is the incumbent material for rigid applications and a commercially available TPO, which is widely used to show parts in instrument panel applications were molded into the same equipment used to evaluate the characteristics of injection molding. of the material of the invention. The conditions for PC / ABS and TPO are summarized below in Table 15.

Table 1 5: Molding conditions The parts that have been produced during these molding evaluations were then compared by percent shrinkage of the tool dimensions. These results are compared in Table 16 below. Because the molding experiment had been done 2 weeks before the PC / ABS and commercial competitive TPO molding verifications, the shrinkage data reported for the material of the invention truly represents the final part size. As demonstrated in this, the TPOs of this invention have the ability to equalize the finished part dimensions of PC / ABS. However, the crystallinity of this material results in a change in thickness, which is reflected in the lighter weight of the formulation panels 3.

Table 16: Molded part dimensions Version A of Table 1 3 above was evaluated by injection molding a retentate in the production tool used to produce the current PC / ABS retainer. The primary change made was to lower the injection temperature. The molding process was summarized as shown in Table 1 7 below. It is noted that a significant amount of crystallization of the version B composition, approximately 90 percent or more, occurs in the tool cavity, prior to the opening of the tool. Shrinkage "out of tool" in the x-y direction is 10 percent or less than the amount of shrinkage in the direction? -and inside the tool cavity. The shrinkage "in the tool" in the z direction is approximately 10 times the shrinkage in the direction? or y. Shrinkage in the z direction is how a lighter inventive part can be produced from a TPO composition as described herein, even when the part is molded in the same tool, such as PC / ABS, and the density of TPO is greater.

Table 17: Production of retainer in a Husky injection molding machine 20 The parts produced conform to the production tools to use foaming technology in place to add a skin of self-formed TPO. The instrumental panel was then evaluated by test as its a commercial instrumental panel. The results of these evaluations are shown in Table 18 below.

Table 18: Evaluating the performance of Form 2 as a retainer Although the invention has been described in some detail through the foregoing specific embodiments, this detail is for the primary purpose of illustration. Many variations and modifications can be made by someone skilled in the art, without departing from the spirit and scope of the invention, as described in the following claims.

Claims (15)

1 . An automotive part, comprising at least one component formed from a polyolefin composition having a heat deflection temperature (HDT, ASTM D648, 0.455 MPa) greater than 1 00 ° C and flexural modulus (ASTM D790, 1% of drying modulus) greater than 1930 MPa, the composition comprising: A) a crystalline isotactic propylene homopolymer having a modulus of flexion (ASTM D790, 1% secant modulus) greater than 1930 MPa and an HDT (ASTM D648, 0.455 MPa) greater than 100 ° C; B) an ethylene / α-olefin interpolymer having a Tg less than -30 ° C, a delta as measured at 0.1 radians / sec at 190 ° C less than 2, an HDT (ASTM D648, 0.455 MPa) which is greater than, or equal to, the peak melting temperature of the ethylene / α-olefin in-polymer, as measured by differential differen- tial calorimetry, and C) a laminated filler, and wherein the weight ratio of homopolymer: interpolymer (A: B) It is between 9: 1 and 6: 4.

2. The automotive part of claim 1, wherein the propylene homopolymer has a flex modulus greater than 2070.

MPa and a HDT greater than 1 10 ° C.

3. The automotive part of claim 1, wherein the propylene homopolymer has a flex modulus greater than 2210 MPa and an HDT greater than 120 ° C.

4. The automotive part of claim 1, wherein the α-olefin

of the ethylene / α-olefin interpolymer is a C3-C20 α-olefin. The automotive part of claim 1, wherein the α-olefin of the ethylene / α-olefin polymer is selected from the group consisting of propylene, 1-butene, 1 -he ene and 1-okene.

6. The automotive part of claim 1, wherein the filler is laminated falco.

The automotive part of claim 6, wherein the composition comprises a sufficient amount of the filler, such that the composition has a flement modulus efficiency factor of 3 or more, and an HDT efficiency factor of 1.5 or more, and where the modulus of flexural efficiency factor is percentage of increase in modulus of flexion per percentage of filler loading, and where the HDT efficiency factor is the percentage of increase in HDT Per percentage of filler loading.

The automotive part of claim 4, wherein the ethylene / α-olefin interpolymer has a Tg less than -40 ° C.

The automotive part of claim 8, wherein the difference between the HDT and the melting point Tm of the ethylene / α-olefin interpolymer is at least 4.

The automotive part of claim 8, wherein the difference between the HDT and the melting point Tm of the ethylene / α-olefin interpolymer is at least 8.

1 1. The automotive part of claim 8, wherein the delta tan, measured at 190 ° C and 0.10 radians / second, of the ethylene interpolymer / a-

Olefin is 2 or less.

12. The automotive part of claim 8, wherein the delta tan, measured at 190 ° C and 0.10 radians / second, of the impact modifier is 1.8 or less. 3.

The automotive part of claim 8, comprising 30 percent by weight of falco based on the total weight of the composition.

14. The automotive part of claim 1, wherein the composition further comprises at least one additive selected from the group consisting of a pigment, an additive resistant to scratch and damage and combinations thereof.

15. The automotive part of claim 1, wherein the part is selected from the group consisting of an instrumental panel, a door panel, a fender, a valence panel, a body side molding, a lower trim molding, a armrest, a visor, a compartment cover and an insulating mat.