MXPA00008883A - STRUCTURES AND FABRICATED ARTICLES HAVING SHAPE MEMORY MADE FROM&agr;-OLEFIN/VINYL OR VINYLIDENE AROMATIC AND/OR HINDERED ALIPHATIC VINYL OR VINYLIDENE INTERPOLYMERS - Google Patents

Abstract

The present invention pertains to structures and fabricated articles having shape/reshape behavior (and processes for their preparation) comprising:(A) from 1 to 100 weight percent (based on the combined weights of Components A and B) of at least one substantially random interpolymer having an I2 of 0.1 to 1,000 g/10 min and an Mw/Mn of from 1.5 to 20, which comprises:(1) from 38 to 65 mol percent of polymer units derived from:(a) at least one vinyl or vinylidene aromatic monomer, or (b) at least one hindered aliphatic or cycloaliphatic vinyl or vinylidene monomer, or (c) a combination of at least one aromatic vinyl or vinylidene monomer and at least one hindered aliphatic or cycloaliphatic vinyl or vinylidene monomer, and (2) from 35 to 62 mol percent of polymer units derived from ethylene and/or at least oneC3-20&agr;-olefin;and (B) from 0 to 99 weight percent (based on the combined weights of Components A and B) of at least one polymer other than that of Component A;and (C) from 0 to 50 percent by weight (based on the combined weights of components A, B, C and D) of at least one tackifier;and (D) from 0 to 80 percent by weight (based on the combined weights of components A, B, C and D) of at least one filler.

Description

STRUCTURES AND MANUFACTURED ARTICLES THAT HAVE MEMORY OF FORM MADE OF INTERPOLIMERQS OF a-QLEFINA / VINYL OR VINYLIDENE WITH VINYL OR VINYLIDENE AROMATIC AND / OR ALIPHATIC IMPEDED This invention relates to fabricated structures and articles prepared from polymers comprising at least one substantially random interpolymer comprising polymer units derived from one or more alpha-olefin monomers with one or more vinyl or aromatic vinylidene monomers and / or vinylidene vinylidene or hindered aliphatic vinylidene or aliphatic cycle, or combined compositions thereof. The structures and articles prepared from these interpolymers can exhibit shape memory properties, because initially they demonstrate high modulus, stiffness and tensile strength, (this is technically designed resin properties), but with the introduction of such an energy source as heat, in an amount sufficient to increase the temperature of the structure of the article above the glass transition temperature (Tg) of the interpolymer, rapidly and impressively decrease the modulus and demonstrate elastomer-like properties. This allows them to be shaped or conform from their original form in a new form or conformation. When the source of enexgia is removed, and the temperature of the structure or articles falls below the glass transition temperature of the interpolymer, the structure or article then retains the new shape and recasts its original, technically designed resin properties. . If the energy source is later reapplied sufficiently to increase the temperature of the structure or article above the glass transition temperature of the interpolymer, the structure or article then reverts back to its shape original or conformation in the absence of any restraining force. Materials that have the ability to reversibly change the shape upon application of an energy source such as heat are known as materials-with "shape memory." Certain metal alloys such as Cu-Al-Ni, Au-Cd, In-Ti, Ni-Ti, can exhibit this property and therefore are often used in applications such as temperature sensors.The uses for these alloys of shape memory metals has however been limited due to temperature ranges - available for these alloys, and the expense of the base metals As an alternative to the metal alloys, several polymers are known that exhibit shape memory behavior The key of this behavior is the morphology of the polymer above and below its glass transition temperature (Tg) and its ability to form a crystalline rubber state partially between the fluid state and the glassy state. Grouper can quite easily be deformed into a new shape, and, when the polymer is cooled below its glass transition temperature, the deformation is fixed and the new shape retained. In this stage the polymer lacks its elasticity of rubber and is rigid. However, the original form can be recovered by simply heating the polymer back to a temperature higher than the glass transition temperature. Thus, it is crucial that the selection of the shape memory polymer used to prepare a manufactured article includes both a knowledge of the final modulus and the stiffness required, as well as a comparison of the glass transition temperature of the polymer with the range of Operating temperature to be used in manufactured articles, and the intended temperature range predicted for this application. For example, the selection of shape memory polymers for use in toy applications will require that the glass transition temperature of the polymer used to make the structure of the manufactured toy or article be in a fairly narrow range slightly above the room temperature, allowing the application to be relatively warm and safe to transform the toy into its moldable state and new configuration. Similarly, simple cooling back to room temperature will result in a new configuration having the original stiffness and the original modulus. The recovery of the original shape or configuration of the toy again will only require the application of a relatively light and safe heating. To date there have been several descriptions of shape memory polymers and articles and applications from them. U.S. Patent No. 5,189,110 discloses a shape memory polymer resin composition which is an ABA block copolymer wherein block A is a vinyl aromatic homopolymer or copolymer (or "a hydrogenated product"). of the same), and block B is a homopolymer or butadiene copolymer and / or a hydrogenated product thereof. U.S. Patent No. 5,098,776 describes a shape memory fibrous sheet comprising a polymer powder of shape memory urethane, styrene / butadiene, crystalline diene, or norbornene U.S. Patent No. 5,093,384 discloses a heat insulator made of a shape memory polymer foam in which the polymer foam is a polyurethane containing approximately equal amounts of NCO and OH groups at the terminals of the molecular chains. US Pat. No. 5,634,913 discloses a softening duct for bringing fluids in and out of the human body having a structure-like needle in which the tip is formed of the shape memory polymer such as a polyurethane. U.S. Patent No. 5,552,197 discloses a dynamic polymer composite comprising a multitude of fibers within a polymer matrix that is made of a shape memory polymer. U.S. Patent No. 5,049,591 discloses a polymer foam with open or closed cell shape memory prepared from urethane, styrene-butadiene, crystalline diene, or norbornene polymers. U.S. Patent No. 5,066,091 discloses an amorphous memory polymer-aligned device wherein the amorphous memory polymer constituent is a covalently crosslinked semicrystalline polymer such as polyethylene or copolymers of ethylvinyl acetate with the polymers of esters of methacrylic acid and aliphatic, or aromatic alcohols, these being particularly preferred. U.S. Patent No. 5,445,140 discloses an endoscopic surgical device in which the hinge member is made of a shape memory polymer that is preferably a polyurethane. U.S. Patent No. 5,192,301 discloses a closed plug device having a flange or elongated end portion made of a shape memory polymer such as a polyborbomer, styrene-butadiene copolymer, polyurethane, or transpolymer. isoprene. Thus, most current shape memory polymers are derived from either urethane polymers or block structure A-B-A styrene / butadiene / styrene. These polymers may additionally require another crosslinking transformation to allow the polymer to exhibit the desired shape memory behavior, thereby further restricting the choice of polymer for a given application. In addition, it is required that many polymers have very high molecular weight to function in these applications (for example 2,000,000 or more) which in turn severely limits their processability and therefore their use in many training processes. Finally, many applications for shape / memory polymers require a frequently narrow operating temperature range and a specific or minimum module, at the same time that current technologies offer only wide temperature operating ranges. It would therefore be desirable to have a memory polymer composition such that it does not require crosslinking, exhibits excellent processability, and which has the ability to accurately refine both its glass transition processes (peak temperature, amplitude and width of the glass). transition) as well as the rigidity and modulus of the material in its final state. There is a wide range of structures and fabricated articles that would benefit from being prepared from polymer compositions that can have both glass transition temperature and module control and preferentially exhibit the shape memory property. These fabricated structures and articles may include, but are not limited to, fibers, foams, films and molded materials. Fibers are often classified in terms of their diameter that can be measured and reported in a variety. of forms. Generally, the diameter of the fiber is measured in denier per filament. Denier is a textile term that is defined as grams of fiber per 9,000 meters of the length of that fiber. Monofilament generally refers to an extruded strand having a denier per filament greater than 15, usually greater than 30. Fine denier fiber generally refers to fiber having a denier of about 15 or less. The microdenier (aka microfibre) generally refers to fiber_ which has a diameter no greater than about 100 microns. The fiber can also be classified by the process by which it is made, such as monofilament, fine filament of continuous winding, fiber of short length or of small cut, glued by spinning, and blown fiber of molten substance. Fiber can also be classified by the number of regions and domains in the fiber. The shape memory fibers of the present invention include the various homochyl fibers made of the substantially random interpolymers or compositions of combinations thereof. Homozygous fibers are those fibers that have a single region (domain) and have no other polymer regions (as do the bicomponent fibers). These homohyl fibers include short fibers, spun fibers or fibers by blowing molten material (using, for example, systems as described in US Pat.

North America number 4,340,563 (Appel et al.), The Patent of the United States of North America number 4,663,220 (Wisneski et al.), The Patent of the United States of America number 4,668,566 (Braun), or the U.S. Patent No. 4,322,027 (Reba), and gel spun fibers (e.g., the system described in U.S. Patent No. 4,413,110 (Kavesh et al.). fibers can be spun fused (that is, they can be extruded into a final fiber diameter directly without further stretching), or they can be spun into a larger diameter and then hot or cold drawn to the desired diameter using fiber stretch techniques The novel shape memory fibers described herein can also be used as bonding fibers, especially when the novel fibers have a lower melting point than the surrounding matrix fibers. , the bond fiber is typically mixed with other fibers on matrix and the entire structure is subjected to heat, where the bond fiber is melted and it joins the surrounding matrix fiber. Typical matrix fibers that benefit from the use of the novel shape memory fibers of the present invention include, but are not limited to, synthetic fibers, such as fibers made of polyethylene terephthalate, polypropylene, nylon, other heterogeneously branched polyethylenes , linear and substantially linear ethylene interpolymers as well as polyethylene polymers. Also included are several natural fibers which include, but are not limited to, those made of silk, wool, and cotton. The diameter of the fiber of the matrix may vary depending on the end-use application.

The shape memory fibers of the present invention also include the various bicomponent composite fibers which may also comprise the substantially random interpolymers and a second polymer component. This second polymer component can be an ethylene or an alpha-olefin homopolymer or interpolymer; an ethylene / propylene rubber (EPM), an ethylene / propylene / diene monomer terpolymer (EPDM), isotactic polypropylene; a styrene / ethylene-butene copolymer, a styrene / ethylene-propylene copolymer, a styrene / ethylene-butene / styrene copolymer (SEBS), a styrene / ethylene-propylene / styrene copolymer (SEPS); polymers of acrylonitrile-butadiene-styrene (ABS), styrene-acrylonitrile (SAN), high impact polystyrene, polyisoprene, polybutadiene, natural rubbers, ethylene / butadiene rubbers, ethylene / propylene diene rubbers (EPDM), rubbers styrene / butadiene, thermoplastic polyurethanes, epoxies, vinyl ester resins, polyurethanes, phenolic resins, homopolymers or copolymers of vinyl chloride or vinylidene chloride, poly (methylmethacrylate), polyester, nylon-6, nylon-6, 6, poly (acetal); poly (amide), poly (arylate), poly (carbonate), poly (butylene) and polybutylene terephthalates, polyethylene; or other compositions thereof. Preferably the second polymer component is an ethylene or an alpha-olefin homopolymer or interpolymer, wherein the alpha-olefin has from 3 to 20 carbon atoms, or polyethylene terephthalate. The bicomponent fibers have the two polymers in a co-continuous phase. Examples of these configurations and shapes of fibers with bicomponents include sheath / core fibers in which the perimeter shape is round, oval, trilobal, triangular, dog bone, or ~ flat or hollow configurations. Other types of bicomponent fibers within the scope of the invention include structures such as cake slices, as well as side-by-side fibers (e.g., fibers having separate regions of polymers, wherein the substantially random interpolymer comprises at least a portion of the surface of the fiber). Xsla bicomponent fibers in the sea are also included "in which a cross-section of the fiber has a main matrix of the first dispersed polymer component through which the domains of the second polymer are. , the matrix of the main polymer looks like a 'sea' in which the domains of the second component of the polymer look like islands. The bicomponent fibers of the present invention can be prepared by co-extruding the substantially random interpolymers into at least a portion of the fiber and a second polymer component into at least one other portion of the fiber. For all configurations in the bicomponent sheath / core fiber (that is, one in which the sheath surrounds the core concentrically), the substantially random interpolymer can be either in the sheath or in the core. Independently different substantially random interpolymers such as sheath and core can also be used in the same fiber, and especially when the sheath component has a melting point lower than the core component. In the case of cake slice configurations, one or more segments may comprise the substantially random interpolymer. In the case of a configuration of Xsla in the sea, "either the islands or the matrix may comprise the substantially random interpolymer." Bicomponent fiber may be formed under conditions of short fiber or continuous filament manufacture, glued by spinning, blown of molten substance The shape of the shape memory fibers of the present invention is not limited, For example, typical fibers have a circular cross-sectional shape, but sometimes the fibers have different shapes, such as a clover shape , or a flat shape (that is, similar to * ribbon). The fiber described herein is not limited by the shape of the fiber. Optionally finisher operations can be performed on the shape memory fiber of the present invention. For example, fibers can be textured by rippling them mechanically or forming them as described in Textile Fibers, Dyes, Finishes, and Processes: A Concise Guide, (Textile Fibers, Dyes, Finishes, and Processes: A Concise Guide), by Howard L. Needles, Noyes Publications, 1986, pages 17-20. The polymer compositions used to make the shape memory X-fibers of the present invention or the fibers themselves can be modified by various cross-linking processes using curing methods at any stage of the fiber preparation including, but not limited to, prior to , during and after stretching either at elevated or ambient temperatures. These crosslinking processes include, but are not limited to, cure systems based on peroxide, silane, sulfur, radiation, or azide. A full description of the various crosslinking technologies is disclosed in copending US Patent Applications Nos. 08 / 921,641 and 08 / 921,642, both filed on August 27,. 1997. Dual healing systems, which use a combination of heat, Thumedad cure, and radiation steps, can be used effectively. Dual cure systems are described and claimed in the United States Patent Application Serial Number 536,022, filed September 29, 1995, in the name of K. L. Alton and S. V. Karande. For example, it may be desirable to employ peroxide crosslinking agents together with silane crosslinking agents, peroxide crosslinking agents together with radiation, crosslinking agents containing sulfur together with silane crosslinking agents, and so on. The polymer compositions can also be modified by various crosslinking processes including, but not limited to the incorporation of a diene component such as a terpolymer in this preparation and subsequent crosslinking by the aforementioned methods and other methods including vulcanization via the vinyl group using sulfur for example as the crosslinking agent. The shape memory fibers of the present invention can be functionalized on the surface by methods including, but not limited to, sulfonation, chlorination using chemical treatments for permanent surfaces or incorporating a temporary coating using the various well-known spin finishing processes. Fabrics made from these novel shape memory fibers include both woven and nonwoven fabrics. Non-woven fabrics can be made variously, including loop-courses (or hydrodynamically entangled) as described in U.S. Patent No. 3,485,706 (Evans) and in U.S. Patent No. 4,939,016 (Rad. anski and collaborators); by loading and thermally bonding homozyme or bicomponent short fibers; by gluing by homoyl or bicomponent fibers in a continuous operation; or by blowing molten substance of homohilo or bicomponent fibers into fabric and subsequently calendering or thermally bonding the resulting network. Other structures made from these fibers are also included within the scope of the invention, including for example, mixtures of these novel shape memory fibers with other fibers (e.g., polyethylene terephthalate) (PET) or cotton or wool or polyester) . Woven fabrics can also be made which comprise the shape memory fibers of the present invention. The different techniques of woven cloth manufacturing are well known to those skilled in the art. technique and its description is not limited to any particular method. Woven fabrics are typically stronger and more heat resistant and are typically used in durable, non-removable applications, for example in polyester woven blends and polyester and cotton blends. The woven fabrics comprising the shape memory fibers of the present invention may be used in applications including but not limited to, upholstery, sporting goods, mats, fabrics, bandages such as, for example, elastic and non-elastic support bands. , ACE® bandages. The novel shape memory fibers and fabrics described herein may also be used in various articles manufactured as described in U.S. Patent No. 2,957,512 (Wade). The union of the fibers with memory of novel form and / or of látela- to the fibers, to fabrics or other articles can be done with gluing by molten substance or with adhesives. Gathered or enjaretados articles can be produced from the new fibers and / or fabrics and other components by folding the. another component (as described in U.S. Patent No. 512) prior to bonding, previously stretching the fiber component with novel fiber memory prior to bonding, or heat shrinking the fiber component with memory in a novel way ^ after the union. The novel shape memory fibers described herein can also be used in loop spinning (or hydrodynamically entangled) processes to make novel structures. For example, U.S. Patent No. 4,801,482 (Goggans), discloses a sheet that can now be made with the novel "memory" fibers / cloth described in the present. Compounds using polyethylene or linear polyethylene copolymer with very high molecular weight also benefit from the novel shape memory fibers described herein. For example, for novel shape memory fibers having a low melting point, such as in the mixture of novel fiber memory fibers and very high molecular weight polyethylene fibers (eg, Spectra® fibers made by Allied Chemical) as described in U.S. Patent No. 4,584,347 (Harpell et al.), Fibers with low melting point are stuck with high molecular weight polyethylene fibers without melting the high molecular weight fibers, this mode preserve the high strength and integrity of the fiber with high molecular weight. Fibers and fabrics may have additional materials that do not materially affect their properties. These useful non-limiting additive materials include pigments, antioxidants, stabilizers, surfactants (e.g., as described in U.S. Patent No. 4,486,552 (Niemann), U.S. Patent No. 4,578,414 (Sawyer et al. ) or U.S. Patent No. 4,835,194 (Bright et al.).

Excellent teachings of processes to make foam structures of etiiénico product and process them are seen in C.P. Park, * Polyolefin Foam, "Chapter 9, Handbook of Polymer Foams and Technology, edited by D. Klempner and KC Frisch, Hanser Publishers, Munich, Vienna, New York, Barcelona (1991) .The foam structures can take any physical configuration known in the art, such as sheet, plank or hemp material Other useful shapes are extendable or foaming particles, moldable foam particles, or beads, and articles formed by expanding and / or coalescing and sticking jesas The foam structures can be made by conventional extrusion foam forming processes.The structure is generally prepared by heating a polymer material to form a plasticized or molten polymer material, incorporating therein a blowing agent to form a gel. foamable and extruding the gel through a matrix to form the foam product, before mixing with the blowing agent, the The polymer material is heated to a temperature at or above its glass transition temperature or melting point. Foam structures can also be formed in the form of a curdled strand by extruding the polymeric ethylene material. through a matrix, of. holes _ multiple. Apparatus and methods for producing curdled foam structures are shown in U.S. Patent Nos. 3,573,152 and 4,824,720. Foam structures can also be formed by accumulating extrusion processes as seen in U.S. Patent No. 4,323,528. Foam structures can also be formed into non-crosslinked foam beads suitable for molding as articles. These processes are well shown in U.S. Patent Nos. 4,379,859 and 4,464,484. In a derivative of this process, the styrene monomer may be impregnated in the suspended granules before impregnation with blowing agent to form an interpolymer grafted with the material of the etiienic product. The process of making polyethylene / polystyrene interpolymer beads is described in U.S. Patent No. 4,168,353. The foam beads can then be molded by any means known in the art, such as loading the foam beads into the mold, compressing the mold to compress the beads and heating the beads such as with steam to effect bonding and welding of the beads. accounts to form the article. Some methods are shown in U.S. Patent Nos. 3,504,068 and 3,953,558. Excellent teachings of the processes. and previous molding methods are seen in C.P. Park, supra, p. 191, pp. 197-198, and pp. 227-229. There are many types of molding operations that can be used to form the fabricated structures and articles of the present invention, including, but not limited to, pouring from solution, thermoforming and various injection molding processes (e.g. those described in Modern Plastics Encyclopedia / 89, Edition of mid-October 1988, Volume 65, Number 11, pp. 264-268, * Introduction to Injection Molding "and on pp. 270-271, * Injection Molding Thermoplastics") , blow molding processes (for example, those described in Modern Plastics Encyclopedia / 89, Edition of mid-October 1988, Volume 65, Number 11, pp. 217-218, "Estrusion-Blow Moldíng"), compression molding profile extrusion, sheet extrusion, film casting, coextrusion and multi-layer extrusion, coinjection molding, lamination, film, spray coating, rotomolding and rotating. However, there remains a requirement for fabricated structures and articles prepared from polymer compositions that exhibit shape memory properties and that have the ability to accurately refine both the glass transition process (location, amplitude and width of the transition) in the vicinity of the temperature: ambient (25 ° C), as the rigidity and the modulus of the material in its final state. It would also be advantageous to prepare these structures and / or articles made from polymer compositions which are easily processable and which exhibit shape memory properties without the requirement of crosslinking. For many applications it would be highly desirable that the glass transition temperature point of the polymer used to prepare the manufactured structure or article be just above room temperature allowing its use in applications requiring stiffness at room temperature but with access to a rubber state that can easily be formed by heating a little just above the glass transition temperature. Also the structure of the manufactured item could be returned to its original conformation by the same degree of mild warming. The present invention relates to fabricated structures and articles prepared from polymer compositions comprising at least one substantially random interpolymer comprising polymer units derived from one or more alpha-olefin monomers with one or more vinyl aromatic monomers or vinylidene and / or hindered or cycloaliphatic aliphatic vinylidene vinylidene monomers or mixtures thereof. Exclusive of these novel materials are the polymer's memory-shape properties, coupled with their ability to precisely refine both glass transition processes (location, amplitude and width of the transition) in the vicinity of the ambient temperature range, as the rigidity and the modulus of the material in its final state. These two factors can be controlled by varying the relative amount of alpha-olefins and vinyl or aromatic vinylidene and / or hindered aliphatic vinyl or vinylidene monomers in the final interpolymer or mixtures thereof. A further increase in the glass transition temperature of the polymer composition used in the present invention can be introduced by varying the type of component mixed with the substantially random interpolymer including the presence of one or more viscosifiers in the final formulation. In a particularly preferred embodiment, the structure is a fiber prepared from substantially random interpolymers or a blend composition of a plurality of which is used to format wrist hair combed at room temperature. the shape memory properties of said fibers allow the wrist hair to be placed or combed in a new conformation by heating above the ambient temperature and the glass transition temperature of the polymer, so that the fibers are its rubber or moldable state, placing the hair in a new conformation or style, and cooling I go back below the ambient temperature and the glass transition temperature of the polymer so that the fibers retain their original rigidity and modulus thus sanding the hair in a new style or configuration. The original style -O- configuration can be recovered simply by heating the hair above the ambient temperature and the glass transition temperature of the polymer. The present invention relates to structures or. manufactured articles having shape memory behavior (and processes for their preparation) comprising: (A) from 1 to 100 weight percent (based on the combined weights of components A and B) of at least one substantially random interpolymer which has an I. of 0.1 to 1,000 grams / 10 minutes and an M "/ Mr, of 1.5 to 20, which _ comprises; (1) from 38 to 65 molar percent units of. polymer derived from: (a) at least one vinyl or vinylidene aromatic monomer, or (b) at least one vinyl monomer or. vinylidene-hindered or cycloaliphatic aliphatic, or (c) a combination of at least one aromatic vinyl or vinylidene monomer and at least one hindered or cycloaliphatic vinylidene or vinylidene monomer, and (2) 35 to 62 mole percent units of polymer derived from ethylene or at least one alphaolefin with from 3 to 20 carbon atoms, or a combination thereof; and (B) from 0 to 99 weight percent (based on the combined weights of components A and B) of at least one polymer other than component A; and (C) from 0 to 50 weight percent (based on the combined weights of components A, B, C and D) of at least one viscosity; and (D) from 0 to 80 weight percent (based on the combined weights of components A, B, C and D) of at least one filler. The structures of the present invention have shape memory properties which may be fibers, foams, molded compositions, or manufactured articles.

The manufactured articles can be made of structures or directly from substantially random interpolymer compositions or mixed compositions. All references in the present elements or metals belonging to a certain Group refer to the Table Periodic of the Elements published and copyrighted by CRC Press, Inc., 1989. Also any reference to the Group or Groups will be to the Group or Groups as reflected in this Periodic Table of the Elements using the IUPAC system to number the groups. Any numerical value quoted herein includes all values from the lowest value to the highest value in increments of one unit provided such that there is a separation of at least two units between any lower value and any higher value. As an example, if it is said that the amount of a component or a value of a process variable such as, for example, temperature, pressure, time is, for example, from 1 to 90, preferably from 20 to 80, more preferably from 30 to 70, it is intended that values such as 15 to 85, 22 to 68, 43 to 51, 30 to 32, etc. are expressly listed in this specification. For values that are less than one, - a unit is considered to be 0.0001, 0.001, 0.01, or 0.1 as "appropriate." These are only examples of what is specifically intended and all possible combinations of numerical values between the most The term "hydrocarbyl" as used herein means any aliphatic, cycloaliphatic, aromatic, aliphatic, substituted by aryl, cycloaliphatic, substituted by aryl group, shall be considered as expressly stated in this application in a similar manner. , aromatic substituted by aliphatic, or cycloaliphatic substituted by aliphatic. The term "idrocarbyloxy" means a hydrocarbyl group having an oxygen bond between it and the carbon atom to which it is attached The term "interpolymer" is used herein to mean a product in which at least two different monomers are polymerize to make the interpolymer. This includes copolymers, terpolymers, et cetera. The term "deformation" as used in the present is defined as bending, stretching, or compression The term "conformability" as used herein is defined as deformation to a prescribed form. The term "recovery in time" as used herein is defined as returning to the original form in a prescribed amount of time.The amount of deformation or conformation as used herein is defined as work which is equal to force multiplied by distance Energy can come from any source, including heat energy, microwave energy, pressure, compression.

Suitable methods of applying heat energy as used herein include, but are not limited to, hot water, hot air, heat lamps, heating elements. The time element as used herein is both the "short" time that the polymer requires to change the modulus and the "extended time" that the polymer retains its new shape. The term "shape memory behavior" as used herein for fibers is characterized by the capacity of a fiber of a diameter of a fiber of 0.05 millimeters in diameter, after heating it to 37 ° C for 30 seconds to be formed in a new undulating conformation wound tightly around a circular roller with a diameter of 0.8 centimeters and after cooling to 25 ° C to be removed from said roller and still maintain a rolled up conformation for more than 30 seconds The term * memory behavior in a manner "as used herein for molded structures or articles is characterized by the ability of a test specimen with a bending modulus of .ASTM with 1.27 centimeters by 12.7 centimeters by 0.19 centimeters in thickness to show: 1. A percentage decrease eirmi-module (Mdec) greater than 80 percent, as determined by the equation: Mdtíü = M4 - M120) YX x 100 where M120 is the mod measured after holding the specimen at 49 ° C for 60 seconds and M is the module measured after holding the specimen at 1.1 ° C for 60 seconds; and 2. The ability to maintain a new shape for more than 60 seconds at 21.6 ° C and for more than 10 seconds. at 49 ° C where said shape was formed by holding a test specimen with ASTM flexural modulus of 0.127 centimeters by 12.7 centimeters by 0.19 centimeters thick for 60 seconds at 49 ° C (120 ° F), then bending the sample by length 12.7 centimeters, end to end, and holding their ends together with a fastener, place this in cold water at 1.1 ° C for 60 seconds followed by removing the fastener, and count how long it takes to return the sample to its initial configuration at 21.6 ° C as at 49 ° C. The preferred embodiment of the present invention describes fabricated structures and articles that exhibit shape memory properties in the vicinity of room temperature. In this way the tests for shape memory behavior defined herein are carried out at 37 ° C, in the case of fibers, and 49 ° C, in the case of molded articles. However, it is also recognized by those skilled in the art and it is encompassed in the present invention that substantially random interpolymers and mixed compositions can encompass a wide range of glass transition temperatures, anywhere between -50 ° C and + 70. ° C and thus in many cases, have a glass transition temperature much higher or much lower than that of 49 ° CX. In this way for these interpolymers and mixtures it is recommended that the heating step in the aforementioned tests be carried out at a temperature between 5 ° C and 25 ° C above the glass transition temperature of the polymer and the cooling step in the tests is carried out at a temperature between 2 ° C to 10 ° C below the glass transition temperature of the polymer. The term "substantially random" (in the substantially random interpolymer comprising polymer units derived from one or more alpha-olefin monomers with one or more vinyl vinyl or aromatic vinylidene monomers and / or vinylidene or vinylidene-hindered or cycloaliphatic vinylidene monomers ) as used herein means that the distribution of the monomers of said interpolymer can be described by the Bernoulli statistical model or by a Markovian first or second order statistical model, as described by JC Randall in POLYMER SEQUENCE DETERMINATION. -13 NMR Method, Academic Press New York, 1977, pp. 71-78. Preferably, the substantially random interpolymers do not contain more than 15 percent of the amount of vinyl monomer or > total aromatic vinylidene in aromatic vinyl or vinylidene monomer blocks of more than three units. More preferably, the interpolymer is not characterized by a high degree of either isotacticity or syndiotacticity. This means that in the Tcarbon 13 nuclear magnetic resonance spectrum of the substantially random interpolymer the peak areas corresponding to the methylene and methine carbon atoms of the main chain representing either meso diad sequences or racemic diad sequences should not exceed 75. percent of the total peak area of the methylene and methine carbon atoms of the main chain. The term "structure" as used herein is defined as a polymer composition that has undergone a process of molding, film formation, fiber or foam The term "manufactured article" as used herein is defined as a polymer composition in the form of a finished article which can be deformed directly from the polymer composition or formed from an intermediate comprising one of the structures described herein. The Substantially Random Interpolymers The interpolymers used to prepare the structures and articles made of the present invention include interpolymers prepared by the polymerization of one or more alpha-olefins with one or more vinyl aromatic or vinylidene monomers and / or one or more monomers of vinylidene or vinylidene hindered or cycloaliphatic, and optionally other polymerizable monomers. Suitable alpha-olefins include, for example, alpha-olefins containing from 2 to 20, preferably from 2 to. 12, more preferably from 2 to 8 carbon atoms. Particularly suitable are ethylene, propylene, butene-1,4-methyl-1-pentene, hexene-1 or octene-1 or ethylene in combination with one or more of propylene, butene-1,4-methyl-1-pentene, hexene -1 or octeno-1. These alpha-olefins do not contain an aromatic part. Other optional polymerizable ethylenically unsaturated monomers include purified ring olefins such as norbornene and alkyl having from 1 to 10 carbon atoms or norbornenes substituted by alkyl of 1 to 10 carbon atoms or aryl of 6 to 10 carbon atoms, being an exemplary interpolymer ethylene / styrene / norbornene. The aromatic vinyl or vinylidene monomers -conveniences can be used to prepare the interpolymers including, for example, those represented by the following formula: Ar I (CHJr? I R1 - C = C (R2). wherein R 1 is selected from the group of radicals consisting of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl; each R2 independently is selected from the group of radicals consisting of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl; Ar is a phenyl group or a phenyl group substituted with from 1 to 5 substituents selected from the group consisting of halo, alkyl having from 1 to 4 carbon atoms, and haloalkyl having from 1 to 4 carbon atoms; and n has a value from 0 to 4, preferably from zero to 2, more preferably zero. Exemplary vinyl aromatic monomers include styrene, vinyl toluene, alpha-methylstyrene, t-butyl styrene, chlorostyrene, including all isomers of these compounds. Particularly convenient these monomers include styrene and lower alkyl derivatives or substituted by halogen thereof. Preferred monomers include styrene, alphamethyl styrene, the lower alkyl ring or substituted phenyl styrene derivatives, such as, for example, ortho-, meta-, and para-methylstyrene, halogenated ring styrenes, para -vinyl toluene or mixtures thereof. same. A preferred aromatic vinyl monomer is styrene. By the term "vinylidene or hindered aliphatic or cycloaliphatic vinylidene compound" is meant addition-polymerizable vinyl or vinylidene monomers corresponding to the formula: A1 R1 - C = C (R2) wherein Al is a spherically bulky, aliphatic or cycloaliphatic substituent of up to 20 carbon atoms, R 1 is selected from the group of radicals consisting of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl; each R2 is independently selected from the group of radicals which "consists of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl, or alternatively, R1 and A1 together form a ring system. "bulky" is meant that the monomer bearing this substituent is usually incapable of addition polymerization by Ziegler-Natta standard polymerization catalyst at a rate comparable to ethylene polymerizations. The preferred aliphatic or cycloaliphatic vinylidene or vinylidene compounds are monomers in which one of the carbon atoms bearing ethylenic unsaturation is tertiary or quaternary substituted. Examples of these substituents include cyclic aliphatic groups such as cyclohexyl, cyclohexenyl, cyclo-octenyl, or alkyl or aryl ring substituted derivatives thereof, tert-butyl, and norbornyl. Preferred aliphatic or cycloaliphatic vinylidene or vinylidene compounds are the various substituted cyclohexene and cyclohexane isomeric vinyl ring substituted derivatives, and 5-ethylidene-2-norbornene. Especially convenient are 1-, 3-, 4- and 4-vinylcyclohexene. Simple linear unbranched alpha-olefins include, for example, alpha-olefin containing from 3 to 20 carbon atoms such as propylene, butene-1,4-methyl-1-pentene, hexene-1 or octene-1 are not examples of spherically hindered aliphatic or cycloaliphatic vinylidene or vinylidene compounds. The substantially random interpolymers can be modified by typical grafting, hydrogenation, functionalization, or other reactions well known to those skilled in the art. The polymers can easily be sulfonated or chlorinated to provide functionalized derivatives according to established techniques. Although not a requirement for shape memory behavior, substantially random interpolymers can also be modified by various crosslinking processes including, but not limited to, peroxide-, silane-based cure systems., sulfur-, radiation-, or azide. A full description of the various crosslinking technologies is disclosed in copending U.S. Patent Application Nos. 08 / 921,641 and 08 / 921,642 filed on August 27, 1997. Dual cure systems, which use a Heat combination, moisture cure, and radiation steps, can be effectively employed. Dual cure systems are described and claimed in U.S. Patent Application serial number 536, 022, filed September 29, 1995, in the name of K. L. Alton and S. V. Karande. For example, it may be desirable to employ peroxide crosslinking agents together with silane crosslinking agents, peroxide crosslinking agents together with radiation, sulfur-containing crosslinking agents together with silane crosslinking agents, and so on. The substantially random interpolymers can also be modified by various crosslinking processes including, but not limited to, the incorporation of a diene component as a thermonomer in its preparation and subsequent crosslinking by the aforementioned methods and other methods including vulcanization via the vinyl group using sulfur for example as the crosslinking agent. A method for preparing substantially random interpolymers includes polymerizing a mixture of polymerizable monomers in the presence of one or more metallocene or restricted geometry catalysts in combination with several cocatalysts, as described in EP-A-0, 416, 815 by James C. Stevens et al., And U.S. Patent No. 5,703,187 by Francis J. Timmers. The preferred operating conditions for these polymerization reactions are pressures from atmospheric to 3000 atmospheres and temperatures from -30 ° C to 200 ° C. Polymerizations and removal of unreacted monomers at temperatures above the autopolymerization temperature of the respective monomers may result in the formation of some amounts of homopolymer polymerization products resulting from the polymerization of free radicals. Examples of suitable catalysts and methods for preparing substantially random interpolymers are described in U.S. Patent Application Serial No. 702,475, filed May 20, 1991 (EP-A-514, 828).; as well as the Patents of the United States of North-America numbers 5,055,438; 5,057,475; 5,096,867 5,064,802; 5,132,380; 5,189,192; 5,321,106; 5,347, 024 5,350,723; 5,374,696; 5,399,635; 5,470,993; 5,703,187 and 5,721,185. The substantially random aromatic alpha-olefin / vinyl or vinylidene aromatic interpolymers can also be prepared by the methods described in JP 07/278230 using compounds shown. By the general formula wherein Cp1 and Cp2 are cyclopentadienol groups, indenyl groups, fluorenyl groups, or substituents thereof, independently of each other; R1 and R "are hydrogen atoms, halogen atoms, hydrocarbon groups with carbon atom numbers of 1 to 12, alkoxyl groups, or aryloxyl groups, independently of each other; M is a group IV metal, preferably Zr or Hf , more preferably Zr; and R3 is an alkylene group or silanodiyl groups used for crosslinking Cp1 and Cp2 Substantially random interpolymers of alpha-olefin / vinyl or substantially random aromatic vinylidene can also be prepared by the methods described by John G. Bradfute. and collaborators, (WR Grace &Co.) in WO 95/32095, by RB Pannell (Exxon Chemical-Patents, Inc.) in WO 94/00500, and in Plastics Technology, page 25 (September 1992). convenient are substantially random interpolymers comprising at least one alpha-olefin / vinyl aromatic / vinyl aromatic / alpha-olefin tetrad described in United States Patent Application Number 08J 708, 869"presented. on September 4, 1996 and WO 98/09999 both by Francis J. Timmers et al. These interpolymers contain additional signals in their carbon-13 nuclear magnetic resonance spectrum with intensities greater than three times the peak-to-peak noise. These signals appear in the range of chemical change 43.70 - 44.25 ppm and 38.0 - 38.5 ppm. Specifically, higher peaks are observed at 44.1, 43.9, and 38.2 ppm. A proton test nuclear magnetic resonance experiment indicates that the signals in the chemical change region 43.70-44.25 ppm are methine carbon atoms and the signals in the 38.0-38.5 ppm region are methylene carbon atoms. It is believed that these new signals are due to sequences involving two vinyl head-to-tail aromatic monomer insertions preceded and followed by at least one alpha-olefin insert, for example, an ethylene / styrene / styrene / ethylene tetrad where the styrene monomer insertions for said tetrads are present in a 1.2 (head-to-tail) manner only. It is understandable to one skilled in the art that for these tetrads to include an aromatic vinyl monomer other than styrene and alpha-olefin other than ethylene that the ethylene tetrad / vinyl aromatic monomer / aromatic vinyl monomer / ethylene will result in peaks similar to nuclear magnetic resonance of carbon 13 but with changes 41 phenylindenyl) racemic zirconium, di-Cl-4 alkyl (dimethylsilanedi-yl) -bis- (2-methyl-4-phenylindenyl) zirconium racemic, di-Cl-4 alkoxide ( racemic dimethylsilanedi-yl) -bis- (2-methyl-4-phenylindenyl) zirconium, or any combination thereof. It is also possible to use catalysts in restricted geometry based on titanium, dimethyl of [N- (l, l-dimethylethyl) -1, l-dimethyl-l- [(1, 2, 3,4, 5?) -1, 5,6,7-tetrahydro-s-indacene-1-yl] silanaminate (2-) -N-titanium; dimethyl (1-indenyl) (tert-butylamido) dimethylsilane titanium; dimethyl ((3-tert-butyl) (1, 2, 3, 4, 5?) -1-indenyl) (tert-butylamido) dimethylsilane titanium; and dimethyl ((3-iso-propyl) (1, 2, 3, 4, 5?) -1-indenyl) (tert-butyl amido) dimethylsilane titanium, or any combination thereof. Other preparative methods for interpolymers used in the present invention have been described in the literature. Longo and Grassi (Makromol, Chem., Volume 191, pages 2387 to 2396 [1990] and D'Anniello et al.

(Journal of Applied Polymer Science, Volume 58, pages 1701-1706 [1995]) reported the use of a catalytic system based on methylalumoxane (MAO) and cyclopentadienyltitanium trichloride (CpTiCY) to prepare an ethylene-styrene copolymer. Xu and Lin (Polymer Preprints, .Am. Chem. Soc, Div. Polym. Chem.) Volume 35, pages 686, 687 [1994]) have reported copolymerization using a 42-MgCl 2 catalyst / TiCl 4 / NdCl / Al. (iBu) 3 to give random copolymers of styrene and propylene. Lu et al. (Journal of Applied Polymer Science, Volume 53, pages 1453 to 1460 [1994]) have described the copolymerization of ethylene and styrene using TiCl 4 / NdCl 3 / MgCl 2 / Al (Et) 3 catalyst. Sernetz and Mulhaupt, (Macromol. Chem. Phvs., V. 197, pp. 1071-1083, 1997) have described the influence of polymerization conditions on the copolymerization of styrene with ethylene using catalysts Me2Si (Me4Cp) (N-tert-butyl) TiCl2 / methylaluminoxane Ziegler-Natta. Ethylene-styrene copolymers produced by bridged metallocene catalysts have been described by Arai, Toshiaki and Suzuki (Polymer Preprints, Am. Chem. Soc., Div. Polym, Chem.) Volume 38, pages 349, 350 [1997]). The manufacture of alpha-olefin / aromatic vinyl moromer interpolymers such as propylene / styrene and butene / styrene are described in U.S. Patent No. 5,244,996, issued to Mitsui "Petrochemical Industries Ltd or the United States Patent. from North America number 5,652,315 also issued to Mitsui Petrochemical Industries Ltd or as described in DE 197 11 339 Al for Denki agaku Kogyo KK Random copolymers of ethylene and styrene are described in Polymer Preprints Volume 39, number 1, March 199B by Toru. Aria et al may also be employed as blending components for foams of the present invention.

When the substantially random interpolymer is prepared, an amount of vinyl aromatic vinylidene or atactic aromatic vinylidene can be formed due to the homopolymerization of vinyl or aromatic de-vinylidene monomer at elevated temperatures. The presence of aromatic vinyl or vinylidene homopolymers in general is not detrimental to the purposes of the present invention and can be tolerated. The aromatic vinyl or vinylidene homopolymer can be separated from the interpolymer, if desired by extraction techniques such as selective precipitation from the solution with a non-solvent for either the interpolymer or the aromatic vinyl or vinylidene homopolymer. For the purpose of the present invention it is preferred that no more than 20 weight percent, preferably less than 15 weight percent based on the total weight of the vinyl aromatic homopolymer or atactic vinylidene interpolymers be present. Mixture Compositions Comprising Substantially Random Interpolymers The present invention also provides structures and articles made of shape memory polymers prepared from mixtures of substantially random interpolymer of alpha-olefin / vinyl or vinylidene with one or more other components of other - polymers that have a wide range of 44 compositions. When the structure or manufactured article comprises a fiber, it is understood that said fiber can be prepared directly from the mixed polymer composition or it can be prepared by combining preformed fibers from the substantially random interpolymer and from another polymer component. When the fiber has a bicomponent structure, then either the core or the sheath can comprise either the substantially random interpolymer and the other polymer component. The other polymer component of the blend may include, but is not limited to, one or more technically engineered thermoplastics, a homopolymer or alpha-olefin interpolymer, a thermoplastic olefin, a styrenic block copolymer, a styrenic copolymer, an elastomer , a thermosetting polymer, or a vinyl halide polymer. Technically designed thermoplastics The third edition of the Kirk-Ohmer Encyclopedia of Science and Technology defines plastics "technically designed as thermoplastic resins, pure or non-reinforced or filled to maintain dimensional stability and most mechanical properties above 100 ° C and below 0 ° C. The terms technically designed and technically engineered "thermoplastics" can be used interchangeably.Technically designed thermoplastics 45 include acetal and acrylic resins, polyamides (eg, nylon-6, nylon 6, 6), polyimides, polyetherimides, cellulosics, polyesters, poly (arylate), aromatic polyesters, poly (carbonate), poly (butylene) and polybutylene terephthalate and polyethylene, liquid crystal polymers, and selected polyolefins, mixtures, or alloys of the above resins, and some examples of other types of resins (including for example liters) high temperature polyolefins such as polycyclopentanes, their copolymers, and polymethylpentane). A thermoplastic designed technically preferred, when the structure or article manufactured comprises a fiber, are the polyesters. Polyesters can be made by the autoesterification of hydroxycarboxylic acids, or by direct esterification, which involves the reaction of the growth step of a diol with a dicarboxylic acid with resultant elimination of water, producing a polyester with a repeating unit - [- AABB -] -. The reaction can be run batch or in solution using a solvent with high inert boiling point such as xylene or chlorobenzene with azeotropic removal of water. Alternatively, but similarly, the ester forming derivatives of a dicarboxylic acid can be heated with a diol to obtain polyesters in an ester exchange reaction. Suitable acid derivatives for this purpose are alkyl esters, halides, salts or acid anhydrides. The preparation of polyarylates, from bisphenol and an aromatic diacid, can be carried out in an interfacial system which is essentially the same as that used for the preparation of polycarbonate. The polyesters can also be produced by a ring-opening reaction of cyclic esters or lactones with from 4 to 7 carbon atoms, for which the bases of organic tertiary amine, phosphines and alkali and alkaline earth metals, hydrides and alkoxides can be used as initiators. Suitable reagents for making the polyester used in this invention, in addition to hydroxycarboxylic acids, are diols and dicarboxylic acids either or both of which may be aliphatic. or aromatics. A polyester which is a poly (alkylene alkanedicarboxylate), an alkylene poly (arylene dicarboxylate), a poly (arylene alkanedicarboxylate), or a poly (arylene arylenedicarboxylate) is therefore suitable for use herein. The alkyl-alkyl portions of the polymer chain can be substituted with, for example, halogens, alkoxy groups with 1 to 8 carbon atoms or alkyl side chains of 1 to 8 carbon atoms and can contain divalent heteroatomic groups (such as -O-, -Si-, -S- or -S02-) in the paraffinic segment of the chain. The chain may also contain unsaturation and non-aromatic rings with 6 to 10 carbon atoms. The aromatic rings may contain substituents such as halogens, alkoxy with 1 to 8 carbon atoms or alkyl groups with 1 to 8 carbon atoms, and may be attached to the polymer backbone at any position on the ring and directly to the alcohol or acid functionality or intervention atoms. Typical aliphatic diols used in the formation of the ester are primary and secondary glycos with 2 to 10 carbon atoms, such as ethylene-, propylene-, and butylene glycol. The commonly used alkanedicarboxylic acids are oxalic acid, adipic acid and sebacic acid. The diols containing rings can be, for example, a 1,4-cyclohexylene glycol or a 1,4-cyclohexane-dimethylene glycol, resorcinol, hydroquinone, 4,4'-thiodiphenol, bis- (4-hydroxyphenyl) sulfone, dihydroxynaphthalene, a xylylene diol, or may be one of the many bisphenols such as 2,2-bis- (4-hydroxyphenyl) propane. Aromatic diacids include, for example, terephthalic acids, isophthalic acid, naphthalene dicarboxylic acid, diphenylethericarboxylic acid, diphenyldicarboxylic acid, diphenylsulfonodicarboxylic acid, diphenoxyethane-dicarboxylic acid. In addition to polyesters formed of a diol and a diacid only, the term "polyester" as used herein includes copolyesters in pattern or block, for example those formed from two or more different diols and / or two or more diacids different, and / or other divalent heteroatomic groups, Mixtures of these copolyesters, blends of polyesters derived from a diol and a diacid only, and mixtures of members of both of these groups, are also suitable for use in this invention, and all they include in the term * polyester ". For example, the use of cyclohexanedimethanol together with ethylene glycol in the esterification with terephthalic acid forms a clear, amorphous copolyester of particular interest. .-Liquid crystalline polyesters derived from mixtures of 4-hydroxybenzoic acid and 2-hydroxy-6-naphthoic acid are also contemplated.; or mixtures of terephthalic acid, 4-hydroxybenzoic acid and ethylene glycol; or mixtures of terephthalic acid, 4-hydroxybenzoic acid and 4,4'-dihydroxy-phenyl. Aromatic polyesters, those preferred from an aromatic diacid, such as alkylene poly (arylene dicarboxylates), polyethylene terephthalate and polybutylene terephthalate, or mixtures thereof, are particularly useful in this invention. A suitable polyester 49 for use herein may have an intrinsic viscosity of 0.4 to 1.2, although values outside this range are also allowed. Methods and materials useful for the production of polyesters as described above are discussed in greater detail in Whinfield, U.S. Patent 2,465,319, Pengilly, U.S. Patent 3,047,539, Schwarz, U.S. Pat. from North American Issue 3,374,402, Russell, U.S. Patent No. 3,756,986 and East, U.S. Patent Number 4,393,191. A particularly preferred technically designed thermoplastic is the acrylic resins which are derived from the free radical polymerization catalyzed by methyl methacrylate peroxide (MMA). As described by H. Luke in Modern Plastics Encyclopedia, 1989, pages 20-21, MMA is usually copolymerized with other acrylates such as methyl acrylate or ethyl acrylate using four basic polymerization processes, by volume, in suspension, in emulsion and solution. Acrylics can also be modified by various ingredients including butadiene, vinyl acrylate and butyl acrylate. The acrylics known as PMMA have ASTM grades and specifications. Grades 5, 6 and 8 vary mainly in flexure deformation temperature 50 under discharge requirements (DTL). Grade 8 requires a tensile strength of 630 kg / cm2 against 560 kg / cm2 of grades 5 and 6. DTLs range from a minimum requirement of 66 ° C to a maximum of 78 ° C, under a load of 18.5 kg / cm2. Certain grades have a DTL of 90 ° C. The modified impact grades vary from the Izod impact of 0.58 to 1.06 joules / centimeter of transparent materials that are not for exteriors. The modified opaque impact grades can have Izod impact values as high as 2.65 joules / centimeter. Surprisingly we have found that for the shape memory structures of the present invention, the addition of polymethyl methacrylate (PMMA) to the substantially random interpolymer or composition of mixtures, increases the brightness and the modulus and improves the resulting handling characteristics (ie the articles moldings and films have a lower tendency to stick to each other during shipping and storage and the fibers have a lower tendency to stick to each other in processes such as carding and / or combing). Alpha-olefin homopolymers and interpolymers Alpha-olefin homopolymers and interpolymers comprise copolymers of propylene, propylene / alpha-olefin with 4 to 20 carbon atoms, polyethylene, and ethylene / alpha-olefin copolymers with 3 to 20 atoms - of carbon, the 51 interpolymers can be either heterogeneous ethylene / alpha-olefin interpolymers or homogeneous ethylene / alpha-olefin interpolymers, including substantially linear ethylene / alpha-olefin interpolymers. The heterogeneous interpolymers differ from the homogeneous interpolymers because in the latter, substantially all the interpolymer molecules have the same proportion of ethylene / comonomer within the interpolymer, while the heterogeneous interpolymers are those in which the interpolymer molecules do not have the same ethylene / comonomer ratio. The term "broad composition distribution" as used herein describes the distribution of comonomers for heterogeneous interpolymers and means that heterogeneous interpolymers have a "linear fraction" and that heterogeneous interpolymers have multiple melting peaks (ie,, exhibit at least two distinct melting peaks) by DSC. The heterogeneous interpolymers have a degree of branching less than or equal to 2 methyl / 1000 carbon atoms in 10 percent (by weight) or more, preferably more than 15 percent (in weight), and especially more than 20 percent ( in weigh) . The heterogeneous interpolymers also have a branching degree equal to 9 greater than 25 methyls / 1000 carbon atoms in 25 percent or less (by weight), preferably 52 less than 15 percent (by weight), and especially less than 10 percent. percent (in weight). Suitable Ziegler catalysts for the preparation of the heterogeneous component of the current invention. they are typically Ziegler-supported catalysts, which are particularly useful at the high polymerization temperatures of the solution process. Examples of these compositions are those derived from organic magnesium compounds, alkyl halides or aluminum halides or hydrogen chloride, and a transition metal compound. Examples of these catalysts are described in U.S. Patent Nos. 4,314,912 (Lowery, Jr. et al.), 4,547,475 (Glass et al.), And 4,612,300 (W. Coleman, III). Suitable catalyst materials can also be derived from inert oxide supports and transition metal compounds. Examples of these compositions suitable for use in the solution polymerization process are described in U.S. Patent No. 5,420,090 (Spencer et al.). The heterogeneous polymer component can be an alpha-olefin homopolymer preferably polyethylene or polypropylene, or, preferably, an interpolymer of ethylene with at least one of alpha-olefin with from 3 to 20 carbon atoms and / or diolefins with 4 at 18 __ atoms of 53 carbon. Heterogeneous copolymers of ethylene and 1-octene are especially preferred. The relatively recent introduction of metallocene-based catalysts for the polymerization of ethylene / alpha-olefin has resulted in the production of new ethylene interpolymers and new requirements for compositions containing these materials. These polymers are known as homogeneous interpolymers and are characterized by their narrower molecular weight and narrower compositional distributions (defined as the weight percent of the polymer molecules having a comonomer content within 50 percent of the molar comonomer content). average total) in relation to, for example, the heterogeneous polyolefin polymers catalyzed by traditional Ziegler. Generally the blown and emptied film made of these polymers is stronger and has better heat and optical properties than the film made with linear low density polyethylene catalyzed with Ziegler-Natta. It is known that metallocene linear low density polyethylene offers significant advantages over polyethylenes of linear density aaaTbaja produced by Ziegler Natta in cast film or tray wrapping applications, particularly improved in puncture resistance in the tray. These linear low density polyethylenes of 54 metallocene however have significantly worse processability in the extruder than Ziegler Natta products. The substantially linear ethylene / alpha-olefin polymers and the interpolymers of the present invention are defined herein as in U.S. Patent No. 5,272,236 (Lai et al.), And in the U.S. Pat. No. 5,272,872. The substantially linear ethylene / alpha-olefin polymers are also homogeneous metallocene-based polymers, since the comonomer is randomly distributed within a given interpolymer molecule and where substantially all of the interpolymer molecules they have the same proportion of ethylene / comonomer within that interpolymer. Many polymers are unique however due to their excellent processability and unique rheological properties and high melt elasticity and fracture toughness of the melted product. These polymers can be successfully prepared in a continuous polymerization process using the restricted geometry metallocene catalyst systems. "Substantially linear ethylene / alpha-olefin polymers are those in which the chemistry is randomly distributed., Given interpolymer molecule and wherein substantially all of the interpolymer molecules have the same ethylene / comonomer ratio within that interpolymer. The term "substantially linear ethylene / alpha-olefin * interpolymer" means that the core structure of the polymer is substituted with chain branches of length 0.01 / 1000 carbon atoms against chain branches of 3/1000 carbon atoms, more preferably chain lengths of 0.01 / 1000 carbon atoms against chain branches of length of 1/1000 carbon atoms, and especially of chain lengths of 0.05 / 1000 carbon atoms against chain branches of length 1/1000 carbon atoms The long chain branch is defined herein as a chain length of at least one carbon atom more than two carbon atoms less than the total number of carbon atoms in the comonomer, for example, the branch The long chain of a substantially linear ethylene / ethylene octene interpolymer is at least seven (7) carbon atoms in length (that is, 8 carbon atoms minus 2 equals 6 atoms). of carbon plus one is equal to 7 carbon atoms of chain length, long chain). The long chain branch may be as long as about the same length as the length of the polymer core structure. The long chain branching is determined by using nuclear or 13 carbon magnetic resonance spectroscopy and is quantified using Randall's method (Rev. Macrorno 1. Chem. Phys., C29 (2 &3), p. 285-297). The long chain branching will, of course, be distinguished from the short chain branches that result solely from the incorporation of the comonomer, so that for example the short chain branching of a substantially linear ethylene / octene polymer is 6 atoms. of carbon length, while the long chain branching for the same polymer is at least 7 carbon atoms in length. The * rheological processing index "(Pl) is the apparent viscosity (in kpoise) of a polymer measured by a gas extrusion rheometer (GER) .The gas extrusion rheometer is described by M. Shida, RN Shroff and LV Cancio in Polymer Engineering Science, Vol. 17, No. H, pp. 770 (1977), and in "Rheometers for Molten Plastics" by John Dealy, published by Van Nostrand Reinhold Co. (1982) on page 97-99 All experiments of gas extrusion rheometers are performed at a temperature of 190 ° C, at nitrogen pressures between 5250 to 500 psig using a L / D 20: 1 matrix with a diameter of 0.0296 inches with an inlet angle of 180 For the substantially linear ethylene / alpha-olefin polymers described herein, the rheological processing index is the apparent viscosity 57 (in kpoise) of a material measured by gas extrusion rheometer that a shear stress of 2.15 x. 106 dynes / cm2 The interpolymers substantially l novel ethylene / alpha-olefin moieties described herein preferably have a rheological processing index in the range of 0.01 kpoise to 50 kpoise, preferably 15 kpoise or less. The novel substantially linear ethylene / alpha-olefin polymers described herein have a rheological processing index less than or equal to about 70 percent of the rheological processing index of a linear ethylene / alpha-olefin comparative polymer at about the same I2 and Mw / Mn. A graph of shear strength versus apparent shear rate is used to identify the fracture phenomenon of the molten substance. According to Rama urthX in Journal of Rheology, 30 (2), 337-357 ^ 1986, above a critical expense, the irregularities of the extruded product observed can be broadly classified into two main types: surface fracture of the molten substance and large fracture of molten substance. The surface fracture of the molten substance occurs under apparently stable flow conditions and varies in detail from loss of specular brightness to a more severe form of "shark skin". In this description, the surface fracture outbreak of molten substance 58 (OSMF) is initially characterized by loss of gloss of the extrudate in which the surface roughness of the extrudate can only be detected by a 40-fold amplification. The critical shear rate in the melt surface fracture outbreak for substantially linear ethylene / alpha-olefin interpolymers is at least 50 percent greater than the critical shear rate in the surface fracture outbreak. of the molten substance of a linear ethylene / alpha-olefin polymer having approximately the same I¿ and MH / Mn, wherein "about the same" as used herein means that each value is within 10 percent of the comparative value of the comparative linear ethylene polymer. The large fracture of the molten substance presents with conditions of non-stable flow and varies in detail from regular (alternating rough and smooth, helical, etc.) to random distortions. For commercial acceptability, (for example, in blown film products), surface defects should be minimal, if not absent. The critical shear rate of the melt surface fracture (OSMF) outbreak and the large melt fracture (OGMF) outbreak will be used in the present based on the changes in surface roughness and configurations. of the products 59 extruded by means of a gas extrusion rheometer. The substantially linear ethylene / alpha-olefin polymers that are useful for forming, the compositions described herein have homogeneous branching distributions. That is, the polymers are those in which the comonomer is randomly distributed within a given interpolymer molecule where substantially all of the interpolymer molecules have the same ethylene / comonomer ratio within that interpolymer. The homogeneity of the polymers is typically described by the short chain branch distribution index (SCBDI) or the composition distribution branching index (CDBI) and is defined as the weight percentage of the polymer molecules having a content of comonomer within 50 percent of the average total molar comonomer content. The CDBI of a polymer is easily calculated from data obtained from techniques known in the field, such as, for example, rinse temperature elution fractionation (abbreviated herein as "TREF") as described, for example, in Wild et al, Journal of Polymer Science, Poly. Phys. Ed., Vol.20, p.441 (1982), in U.S. Patent No. 4,798,081 (Hazlitt et al.), or as described in Patent of the United States of America number. 60 5.0J8,204 (Stehling). The technique for calculating CDBI is described in U.S. Patent No. 5,322,728 (Davey et al.) And in U.S. Patent No. 5,246,783 (Spenadel et al.), Or in U.S. Pat. North America number 5,089,321 (Chum et al.). The SCBDI or CDBI for the substantially linear olefin interpolymers used in the present invention is preferably greater than 30 percent, especially greater than 50 percent. The substantially linear ethylene / alpha-olefin interpolymers used in this invention essentially lack a "high density" measurable fraction as measured by the TREF technique (ie, the homogeneous ethylene / alpha-olefin interpolymers do not contain a fraction of polymer with a degree of branching less than or equal to 2 methyls / 1000 carbon atoms). Substantially linear ethylene / alpha-olefin polymers also do not contain any fraction. Very short chain branched (that is, they do not contain a polymer fraction with a branching degree equal to or greater than 30 methyl / 1000 carbon atoms). The catalysts used to prepare homogeneous interpolymers for use as the blend components in the present invention are metallocene catalysts. These metallocene catalysts include the. 61 bis (cyclopentadienyl) and mono (cyclopentadienyl) catalyst systems which are restricted geometry catalyst systems (used to prepare the substantially linear ethylene / alpha-olefin polymers). These restricted geometry metal complexes and methods for their preparation are described in U.S. Patent Application Serial No. 545,403, filed July 3, 1990 (EP-A-416,815); U.S. Patent Application Serial Number 547,718, filed July 3, 1990 (EP-A-468,651); U.S. Patent Application Serial No. 702,475, filed May 20, 1991 (EP-A-514, 828); U.S. Patent Application Serial Number 876,268, filed May 1, 1992, (EP-A-520, 732); Patent Application of the United States of America with serial number 8,003, filed on January 21, 1993 (WO93 / 19104); United States Patent Application North America with serial number 08 / 241,523, (WO95 / 00526); as well as in the patents of the United States of North America numbers US-A-5, 055, 438, US-A-5, 057, 475, US-A-5,096,867, US-A-5,064,802, and US-A-5. , 132, 380. In EP-A 418,044, published March 20, 1991 (equivalent to U.S. Patent Application Serial No. 07 / 758,654) and in 62 the States Patent Application. United States of America with serial number 07/758, 660 certain cationic derivatives of the previous catalysts with restricted geometry that are very useful as polymerization catalysts of. olefin are described and claimed. In the U.S. Patent Application Serial No. 720,041, filed on June 24, 1991, certain reaction products of the previous restricted geometry catalysts are described with several borans and a method is taught and claimed. for its preparation. In U.S. Patent No. US-A 5,453,410 combinations of cationic catalysts of restricted geometry with an alumoxane were described as suitable catalysts for olefin polymerization. The homogeneous polymer component can be an alpha-olefin homopolymer preferably polyethylene or polypropylene, or, preferably, an interpolymer of. ethylene with at least one alpha-olefin with "" of 3 to 20 carbon atoms and / or diolefins with 4 to 18 carbon atoms. The homogeneous copolymers of ethylene and 1-octene are especially preferred. Thermoplastic Olefins Thermoplastic olefins (TPO) are generally produced from homo or copolymers, or mixtures of an elastomeric material such as ethylene / propylene rubber 63 (EPM) or ethylene / propylene terylene diene monomer (EPDM) and a more rigid material such as isotactic polypropylene. Other materials or components may be added in the formulation depending on the application, including oil, fillers, and cross-linking agents. Generally, thermoplastic olefins are characterized by a rigidity balance (modulus) and good chemical resistance and impact resistance with low temperature and wide usage temperatures.

Due to characteristics like this, thermoplastic olefins are used in many applications, including automobile faci and dashboards, and also potentially in wires and cables. Polypropylene is generally in the isotactic form of polypropylene homopolymer, although other forms of polypropylene can also be used (eg, syndiotactic or atactic). Polypropylene impact copolymers (for example, those where a second polymerization step is employed which reacts ethylene with propylene) and random copolymers (also modified by reactor and usually containing 1.5-7 percent ethylene copolymerized with propylene), however, can also be used in the thermoplastic olefin formulations described herein. Thermoplastic olefins in reactor can also be used as components of mixtures of the present invention. A complete discussion of several polypropylene polymers is contained in Modern Plastics Encyclopedia / 89, Edition of mid-October 1988, Volume 65, Number 11, pp. 86-92 X The molecular weight of the polypropylene for use in the present invention is conveniently indicated using a melt flow measurement in accordance with .ASTM D-1238, Condition 230 ° C / 2.16 kilograms (formerly known as "Condition"). L) "and also known as I2). The expenditure of the molten substance is inversely proportional to the molecular weight of the polymer. In this way, the higher the molecular weight, the lower the cost of the molten substance, although the relationship is not linear. The expenditure of the melt of the polypropylene useful herein is generally 0.1 grams / 10 minutes (g / 10 min) up to 35 g / 10 minutes, preferably 0.5 grams / 10 minutes at 25 grams / 10 minutes, and especially from 1 gram / 10 minutes at 20 grams / 10 minutes. _ Block-shaped styrene copolymers Also included are block copolymers which have unsaturated rubber monomer units including, but not limited to, styrene-butadiene (SB), styrene-isoprene (SI), styrene-butadiene-styrene ( SBS), styrene-isoprene-styrene (SIS), alpha-methylstyrene-butadiene-alpha-methylstyrene and alpha-methylstyrene-isoprene-alpha-ethylstyrene. The peracenic portion of the block copolymer 65 is preferably a polymer or interpolymer of styrene and its analogs and homologs including alpha-methylstyrene and substituted ring styrenes, particularly methylated ring styrenes. The preferred styrenics are styrene and alpha-methylstyrene, and styrene is particularly preferred. Block copolymers with unsaturated rubber monomer units may comprise homopolymers of butadiene or isoprene or may comprise copolymers of one or both of these two dienes with a minor amount of styrenic monomer. Preferred block copolymers with saturated rubber monomer units comprise at least one segment of the styrenic unit and at least one segment of an ethylene-butene or ethylene-propylene copolymer. Preferred examples of these block copolymers with saturated rubber monomer units include styrene / ethylene-butene copolymers, styrene / ethylene-propylene copolymers, styrene / ethylene-butene / styrene copolymers (SEBS), styrene / ethylene-propylene / styrene copolymers (SEPS). Styrenic copolymers In addition to the block copolymers are the polymers of acrylonitrile-butadiene-styrene (ABS), styrene-acrylonitrile, (SAN), and the styrenics modified by rubber that include high impact polystyrene. 66 Elastomers Elastomers include, but are not limited to, rubbers such as polyisoprene, polybutadiene, natural rubbers, ethylene / propylene rubbers, ethylene / propylene diene rubbers (EPDM), styrene / butadiene rubbers, thermoplastic polyurethanes. Thermoset Polymers Thermoset polymers include but are not limited to epoxies, vinyl ester resins, polyurethanes, and phenolics. Vinyl halide polymers Vinyl halide homopolymers and copolymers are a group of resins that are used as a building block of the vinyl structure CH2-CXY, wherein X is selected from the group consisting of F, Cl, Br , and I, while Y is selected from the group consisting of F, Cl, Br, I and H. The vinyl halide polymer component of the blends of the present invention includes but is not limited to halide homopolymers and copolymers. of vinyl with copolymerizable monomers such as alpha-olefins including but not limited to ethylene, propylene, vinyl esters of organic acids containing from 1 to 18 carbon atoms, for example vinyl acetate, vinyl stearate and so on. Vinyl chloride, vinylidene chloride, symmetric dichloroethylene; acrylonitrile, methacrylonitrile; alkyl acrylate esters in which the alkyl group contains from 1 to 8 carbon atoms, for example methyl acrylate and butyl acrylate; the corresponding alkyl methacrylate esters: dialkyl esters of dibasic organic acids in which the alkyl groups contain from 1 to 8 carbon atoms, for example dibutyl fumarate, diethyl maleate and so on. Preferably the vinyl halide polymers are homopolymers or copolymers of vinyl chloride or vinylidene chloride. The Polyvinyl Chloride (PVC) polymers can be further classified into two main types by their degree of rigidity. These are "rigid" PVC and "flexible" PVC. Flexible PVC is distinguished from rigid PVC mainly by the presence and amount of plasticizers in the resin. Flexible PVC typically has improved processability, lower tensile strength and greater elongation of rigid PVC. Of the vinylidene chloride homopolymers and copolymers (PVDC), typically copolymers with vinyl chloride, nitrile acrylates are used commercially and are most preferred. The choice of the comonomer significantly affects the properties of the resulting polymer. Perhaps the most remarkable properties of the different VBAC are their low permeability-68 of gases and liquids, barrier properties; and chemical resistance. Also included are different PVC and PVCD formulations containing minor amounts of other materials present to modify the properties of PVC or PVCD, including but not limited to polystyrene, styrenic co-polymers, polyolefins including homopolymers and copolymers comprising polyethylene, and / or polypropylene, and other ethylene / alpha-olefin copolymers, polyacrylic resins, polymers containing butadiene = such as acrylonitrile-butadiene-styrene terpolymers (ABS), and methacrylate-butadiene-styrene terpolymers (MBS), and resins of chlorinated polyethylene (CPE). Also included in the family of vinyl halide polymers for use as the blend components of the present invention are the chlorinated PVC derivatives typically prepared by post-chlorination of the base resin and known as chlorinated PVC, (CPVC). Although the CPVC is based on PVC and shares some characteristic properties, the CPVC is a unique polymer that has a much higher melting temperature range (410 - 450 ° C) and a higher glass transition temperature (115 - 135). ° C) than PVC. Compositions comprising at least one substantially random interpolymer used to prepare structures and manufactured articles of the present invention in addition to optionally comprising one or more other polymer components optionally may comprise one or more viscosifiers. Viscosants Viscosants can also be added to the polymer compositions used to prepare the fabricated structures and articles of the present invention in order to alter the degree of transition to glass and as well as to extend the range of available application temperature. A suitable viscosity can be selected based on the criteria presented by Hercules in J. Simons, Adhesives Age, "The HMDA Concept: A New Method for Selection of Resins", November 1996. This reference discusses the importance of the polarity and molecular weight of the resin to determine compatibility with the polymer. In the case of substantially random interpolymers of at least one alpha-olefin and a vinyl aromatic monomer, the preferred viscosifiers will have some degree of aromatic character to promote compatibility, particularly in the case of substantially random interpolymers having a high monomer content aromatic vinyl. As an initial indicator, compatible viscosifiers are those that are also known to be compatible with ethylene / vinyl acetate having 28 weight percent vinyl acetate. The viscosifying resins can be obtained by the polymerization of oil and terpene feed stream and from the derivatization of wood, rubber, and rosin oil. Some kinds of viscosizers include wood rosin, liquid resin and liquid resin derivatives, and cyclopentadiene derivatives, such as those described in UK Patent Application GB 2,032,439A. Other classes of viscosifiers include aliphatic resins with 5 carbon atoms, polyterpene resins, hydrogenated reams, mixed aliphatic aromatic resins, rosin esters, natural and synthetic terpenes, terpene-phenolics, and rosin esters. hydrogenated Rosin is a commercially available material that occurs naturally in the oil-rosin of pine trees and is typically derived from the oil-resinous exudate of the living tree, from old stumps and from liquid resin produced as a byproduct of the manufacture of brown paper. After it is obtained, the rosin can be treated by hydrogenation, dehydrogenation, polymerization, esterification, and other after-treatment processes. Rosin is typically classified as gummy rosin, wood rosin, or as resinous rosin, 11 indicating its origin. The materials can be used no. modified, in the form of esters of polyhydric alcohols, and can be polymerized through the inherent unsaturation of the molecules. These materials are commercially available and can be mixed into the compositions using standard mixing techniques. Representative examples of these rosin derivatives include pentaerythritol esters of liquid resin, rubbery rosin, wood rosin, or mixtures thereof. Examples of various classes of viscosizers include, but are not limited to aliphatic resins, polyterpene resins, hydrogenated resins, mixed aliphatic aromatic resins, styrene / alpha-methylene styrene resins, pure monomer hydrocarbon resins, hydrogenated pure hydrocarbon monomer resin, modified styrene copolymers, copolymers of pure aromatic monomer, and hydrogenated aliphatic hydrocarbon resins. Exemplary aliphatic resins include those available under commercial designations. Escorez®, Piccotac®, Mercures®, Wingtack®, Hi-Rez®, Quintone®, Tackirol®, etcetera. Exemplary polyterpene resins include those available under commercial designations. Nirez®, Piccolyte®, Wingtack®, Zonarez®, etcetera. Exemplary hydrogenated resins include those available under the commercial designations Escorez®, Arkon®, Clearon®, 72 et cetera. Exemplary mixed aromatic aliphatic resins include those available under the trade designations Escorez®, Regalite®, Hercures®, 7AR®, Imprez®, Norsolene® M, Marukarez®, Arkon®, M, Quintone®, Wingtack®, et cetera. A preferable class of viscosizers include styrene / alpha-methylene styrene viscosity available from Hercules. Particularly convenient classes of viscosizers include Wingtack® 86 and Hercotac® 1149, Eastman H-130, and styrene / alpha-methyl styrene viscosifiers. Other preferred glidants are Piccotex 75, a pure monomer hydrocarbon resin having a glass transition temperature of 33 ° C., available from Hercules, Regalrez® 1139 which is prepared by the hydrogenation polymerization of pure monomer hydrocarbon, Picotex® 120 which is a modified styrene copolymer, Kristalex® 514Q which is a copolymer of the pure aromatic monomers, Plastolyn® 140 which is a hydrogenated aliphatic hydrocarbon resin, and Endex® 155 which is a copolymer of pure aromatic monomers. Of these, Kristalex® 5140, Plastolyn® 140, and Endex® 155 are preferred, with Endex® 155 being the most preferred. Other additives Additives such as oxidants (for example, hindered phenols such as, for example, Irganox® 1010), phosphites ( for example, Irgafos® 168), ultraviolet stabilizers, bonding additives (eg, poly-isobutyleneol, slip agents 73 (such as erucamide and / or steramide), antiblock additives, colorants, pigments, can also be included in the Interpolymers and / or mixtures used to prepare the structures and articles manufactured of the present invention, to the extent that they do not interfere with the properties of substantially random interpolymers Processing aids, to which reference will be made herein as plasticizers, optionally provide for reducing the viscosity of a composition, and include phthalates, such as dioctyl phthalate and di-isobutyl phthalate, natural oils such as anolina, and paraffin, naphthenic and aromatic oils obtained from the refining of petroleum, and liquid resins from the rosin of petroleum feeds. Exemplary classes of oils useful as processing aids include white mineral oil such as Kaydol® (available from Witco), and Shelflex® 371 naphthenic oil (available from Shell Oil Company). Another convenient oil is Tuflo® oil (available from Lyondell). Also included as a potential component of the polymer compositions used in the present invention are several organic and inorganic fillers, whose identity depends on the type of application in the mixture to be used. Representative examples of these fillers include organic and inorganic fibers such as those made of asbestos, boron, graphite, ceramics, glass metals (such as stainless steel) or polymers (such as aramid fibers) talc, carbon black, carbon fibers, calcium carbonate, aluminum oxide trihydrate, glass fibers, marble powder, cement powder, clay, feldspar, silicon oxide or glass, smoked silicon oxide, aluminum oxide, magnesium oxide, magnesium hydroxide, oxide of antimony, zinc oxide, barium sulfate, aluminum silicate, calcium silicate, titanium dioxide, titanates, aluminum nitride, B203, nickel powder or chalk. Other representative organic or inorganic fillers, fiber or minerals, include carbonates such as barium, calcium or magnesium carbonate; fluorides such as calcium or sodium aluminum fluoride; hydroxides such as aluminum hydroxide; metals such as aluminum, bronze, lead or zinc; oxides such as aluminum oxide, antimony, magnesium or zinc oxide, or silicon or titanium dioxide; silicates such as asbestos, mica, -clay (kaolin or calcined kaolin), calcium silicate, feldspar, glass (ground glass or in hollow glass spheres or microspheres or beads, ceramic fibers or -filaments), nepheline, perlite, pyrophyllite, talc or golastonite; sulfates such as barium or calcium sulfate; metal sulfides; cellulose, in forms such as wood or shell flour; calcium terephthalate; and liquid crystals. Mixtures of more than one of these fillers can also be used. These additives are employed in functionally equivalent amounts known to those skilled in the art. For example, the amount of antioxidant employed is the amount that prevents the polymer or polymer mixture from undergoing oxidation at the temperatures and environment employed during the storage and final use of the polymers. This amount of antioxidants is usually in the range of 0.01 to 10, preferably 0.05 to 5, more preferably 0.1 to 2 weight percent based on the weight of polymer or polymer mixture. Similarly, the amounts of any of the other additives listed are functionally equivalent amounts such that the amount of returning the polymer or the anti-blocking polymer mixture, to produce the desired result, to provide the desired color from the colorant or pigment. These additives can be conveniently employed in the range of 0.05 to 50, preferably 0.1 to 35, more preferably 0.2 to 20 weight percent based on the weight of polymer or polymer blend. When a processing aid is employed, it will be present in the composition of the invention in an amount of at least 5 percent. The processing aid will typically be present in a quantity of not more than 60, preferably not more than 30, and more preferably not more than 20 weight percent. Preparation of the Mixtures Comprising the Substantially Random Interpolymers The mixed polymer compositions used to prepare the manufactured articles of the present invention can be prepared by any convenient method, including dry blending the individual components and subsequently mixing the molten substance or composing the substance cast in Haake's torque torque rheometer, or by dry combination without mixing of the molten substance followed by the manufacture of the part, either directly in the extruder or mill used to make the final item (for example, the automotive part) ), or by mixing the previously melted substance in a separate extruder or mill (e.g., a Banbury mixer), or by solution mixing, or by compression molding, or by calendering. Preparation of structures used to form fabricated articles of the present invention Molded articles The fabricated structures and articles of the present invention can be prepared by many molding operations known to those skilled in the art, including, but not limited to, casting from solution, thermoforming, the various processes of injection molding and blow molding, compression molding, profile extrusion, sheet extrusion, film casting, co-extrusion and multi-layer extrusion, coinjection molding, lamination film , spray coating, rotomolding and rotovating. Foams Also included in the shape memory structures of the present invention are foams comprising substantially random interpolymers either in a crosslinked or non-crosslinked form or mixtures thereof which take a deformed shape and a mold form., said deformed shape being produced when the foam of the polymer is compressed at a temperature higher than the glass transition point (Tg) of the polymer and then kept compressed at a temperature lower than the glass transition temperature until the compression is Fixed, this shape as molded occurs when the compressed polymer foam is heated again to a temperature higher than the glass transition temperature point until it regains its original shape. The foam composition can be used in the form of a single layer or as a layer in a multi-layer structure. Excellent teachings for processes to make ethereal polymer foam structures and process them are seen in C.P. Park, "Polyolefin Foam", Chapter 9, Handbook of Polymer Foams and Technology, edited by D. Klempner and K. C. Frisch, Hanser Publisher, Munich, Vienna, New York, Barcelona (1991). The shape memory foam structures can be made by any conventional extrusion foaming process, including their production in the form of a curdled belt, or by an accumulation extrusion process, or by shaped foam beads suitable for molding into blocks or articles formed by convenient molding methods known in the art. Blowing agents useful for making shape memory foam structures include inorganic agents, organic blowing agents and chemical blowing agents. Convenient inorganic blowing agents include carbon dioxide, nitrogen, argon, water, air, and helium. Organic blowing agents include aliphatic hydrocarbons having from 1 to 6 carbon atoms, aliphatic alcohols having from 1 to 3 carbon atoms, and partially halogenated and fully halogenated aliphatic hydrocarbons having from 1 to 4 carbon atoms. The aliphatic hydrocarbons include methane, ethane, propane, n-butane, isobutane, n-pentane, -isopentane, neopentane. The aliphatic alcohols include methanol, ethanol, n-propanol, and isopropanol. The fully and partially halogenated aliphatic hydrocarbons include fluorocarbons, chlorocarbons, and chlorofluorocarbons. Examples of fluorocarbons include methyl fluoride, perfluoromethane, ethyl fluoride, 1,1-difluoroethane (HFC-152a), 1,1-trifluoroethane (HFC-143a), 1,1,1-tetrafluoroethane ( HFC-134a), pentafluoroethane, difluoromethane, perfluoroethane, 2, 2-difluoropropane, 1,1,1-trifluoropropane, perfluoropropane, dichloropropane, difluoropropane, perfluorobutane, perfluorocyclobutane. The partially halogenated chlorocarbons and the chlorofluorocarbons for use in this invention include methyl chloride, methylene chloride, ethyl chloride, 1,1-trichloroethane, 1,1-dichloro-1-fluoroethane (HCFC-141b), l- chloro-1,1 difluoroethane (HCFC-142b), 1,1-dichloro-2,2,2-trifluoroethane (HCFC-123) and 1-chloro-1,2,2,2-tetrafluoroethane (HCFC-124). Fully halogenated chlorofluorocarbons include trichloromonofluoromethane (CFC-11), dichlorodifluoromethane (CFC-12), trichlorotrifluoroethane (CFC-113), 1,1-trifluoroethane, pentafluoroethane, dichlorotetra-fluoroethane (CFC-114), chlorheptafluoropropane, and dichlorohexafluoropropane. Chemical blowing agents include azodicarbonamide, azodi-isobutyro-nitrile, benzene-sulfonhydrazide, 4,4-oxybenzenesulfonyl-semicarbazide, p-toluenesulfonylsemi-carbazide, barium azodicarboxylate, 80 N, N'-dimethyl-N, N '-dinitrosoterephthalamide , and trihydrazino triazine. Preferred blowing agents include isobutane, HFC-152a, and mixtures of the foregoing. The amount of blowing agents incorporated in the substantially random interpolymer melt to make the foam-forming polymer gel is 0.2 to 5.0, preferably 0.5 to 3.0, and more preferably 1.0 to 2.50 gram moles per kilogram of polymer. . Various additives can be incorporated into the present foam structures such as stability control agents, core forming agents, inorganic fillers, pigments, antioxidants, acid cleaners, ultraviolet absorbers, flame retardants, processing aids, extrusion aids. A stability control agent can be added to the present foam to increase dimensional stability. Preferred agents include amides and esters of fatty acids of 10 to 24 carbon atoms. These agents are seen in U.S. Patent Nos. 3,644,230 and 4,214,054. More preferred agents include stearyl esteramide, glycerol mono-stearate, glycerol monobehenate, and sorbitol monostearate. Typically, these control agents. Stability is employed in an amount ranging from 0.1 to 1.081 parts per 100 parts of the polymer. In addition, a core forming agent can be added in order to control the size of the foam cells. Preferred core forming agents include inorganic substances such as calcium carbonate, talc, clay, titanium oxide, silicon oxide, barium sulfate, diatomaceous earth, mixtures of citric acid and sodium bicarbonate. The amount of core former employed can vary from 0.01 to 5 parts by weight per hundred parts by weight of a polymer resin. Manufactured fibers and / or articles The fiber can be prepared as monofilament, fine filament of continuous rolling, strand or short cut fiber, glued by spinning, and blown fiber of molten substance. The shape memory fibers of the present invention include the various homozygous fibers made from substantially random interpolymers or blended compositions thereof including short fibers, spunbond fibers or meltblown blows. The short fibers can be spun fused or they can be used as binding fibers, especially when the novel fibers have a melting point lower than that of the fibers of the surrounding matrix. The shape memory fibers of the present invention include the various bicomponent fibers that can also be made from novel substantially random interpolymers or blend compositions thereof comprising at least one of the components. Finishing operations can optionally be carried out on the shape memory fibers of the present invention, for example, the fibers can be textured by corrugation or mechanical forming.The polymer compositions that are used to make the fiber with memory of the present invention or the fibers themselves can also be modified by various cross-linking processes using curing methods described herein at any stage of the fiber preparation including, but not limited to, before, during and after stretching them to either elevated or ambient temperatures Polymer compositions can also be modified by various crosslinking processes described herein or functionalize the surface by methods including, but are not limited to sulfonation, chlorination using chemical treatments for permanent surfaces or incorporating a temporary coating using the well-known different spinning finishing processes. Fabrics made from these novel shape memory fibers include, but are not limited to, both woven and non-woven fabrics, but not limited to, upholstery, sports equipment, mats, fabrics, bandages. Properties of Shape Memory Interpolymers and Mixture Compositions in the Fabricated Structures and Articles of the Present Invention The polymer compositions used to prepare the fabricated structures and articles of the present invention comprise from 1 to 100, preferably from 10 to 100, more preferably from 50 to 100, still more preferably from 80 to 100 weight percent, (based on the combined weights of this component and the polymer component other than the substantially random interpolymer) and one or more interpolymers of one or more more alpha-olefins and one or more aromatic vinyl or vinylidene monomers and / or one or more vinylidene or vinylidene monomers aliphatic or cycloaliphatic hindered. The substantially random interpolymer can be. used as a minor component of a multicomponent mixture when used as, for example, a compatibilizer or bonding component, may be present in even more preferably 80 to 100 weight percent amounts, (based on the combined weights of this component and the polymer component other than the substantially random interpolymer). These substantially random interpolymers usually contain from 38 to 65 preferably from 45 to 55, 84 more preferably from 48 to 55 molar percent of at least one aromatic vinyl or vinylidene monomer and / or hindered or cycloaliphatic vinylidene or vinylidene monomer and 35 to 62, preferably 45 to 55, more preferably 45 to 52 mole percent of at least one aliphatic alpha-olefin having from 2 to 20 carbon atoms. The average molecular weight number (Mn) of the substantially random interpolymer used to prepare the shape memory structures and manufactured articles of the present invention is greater than 1,000, preferably from 5,000 to 500,000, more preferably from 10,000 to 300,000. The melt index (I2) of the substantially random interpolymer used to prepare the shape memory structures and manufactured articles of the present invention is from 0.1 to 1,000, preferably from 0.5 to 200, more preferably from 0.5 to 100 grams / 10. minutes The molecular weight distribution (M "/ Mn) of the substantially random interpolymer used to prepare the shape memory structures and manufactured articles of the present invention is from 1.5 to 20, preferably from 1.8 to 10, more preferably from 2 to 5. The density of the substantially random interpolymer used to prepare the shape memory fibers of the present invention is greater than 0.930, preferably from 0.930 to 1.045, more preferably from 0.930 to 1.040, more preferably from 0.930 to 1.030 grams / cm3. The polymer compositions used to prepare the fibers of the present invention may also comprise from 0 to 99, preferably from 0 to 90, more preferably from 0 to 50, still more preferably from 0 to 20 weight percent of at least one polymer other than the substantially random interpolymer (based on the combined weights of this component and the substantially random interpolymer) which may comprise a homogeneous alpha-olefin homopolymer or interpolymer comprising polypropylene, propylene / alpha-olefin copolymers having from 4 to 20 atoms of carbon, polyethylene, and ethylene / alpha-olefin copolymers having from 3 to 20 carbon atoms, the interpolymers can be either heterogeneous ethylene / alpha-olefin interpolymers, preferably a heterogeneous ethylene / alpha-olefin interpolymer with to 8 carbon atoms, more preferably a heterogeneous ethylene / octene-1 interpolymer or homogeneous ethylene / alpha-olefin interpolymers, including the substantially linear interpolymers of ethylene / alpha-olefin, preferably a substantially linear interpolymer of ethylene / alpha-olefin, 86 more preferably a substantially linear interpolymer of ethylene / alpha-olefin with 3 to 8 carbon atoms; or a heterogeneous ethylene / alpha-olefin interpolymer; or a thermoplastic olefin, preferably an ethylene / propylene rubber (EMP) or an ethylene / propylene monomer diene monomer (EPDM) or isotactic polypropylene terpolymer, more preferably isotactic polypropylene; or a styrenic block copolymer, preferably styrene-butadiene (SB), styrene-isoprene (SI), styrene-butadiene-styrene (SBS), styrene-isoprene-styrene (SIS) or styrene-ethylene / butene-block copolymer styrene (SEBS), more preferably "a styrene-butadiene-styrene copolymer (SBS); or styrenic homopolymers or copolymers, preferably polystyrene, high impact polystyrene, polyvinyl chloride, styrene copolymers and at least one of acrylonitrile, methacrylonitrile , maleic anhydride, or alphamethyl styrene, more preferably polystyrene, or elastomers, preferably polyisoprene, polybutadiene, natural rubbers, ethylene / propylene rubbers, ethylene / propylene diene rubber (EPDM), styrene / butadiene rubbers, thermoplastic polyurethanes, more preferably thermoplastic polyurethanes, or thermoset polymers, preferably epoxies, vinyl ester resins, polyurethanes, phenolics, more preferably poly urethanes; or vinyl halide homopolymers and copolymers, preferably homopolymers or copolymers of vinyl chloride or vinylidene chloride or the chlorinated derivatives thereof, more preferably poly (vinyl chloride) and poly (vinylidene chloride); or technically designed thermoplastics, preferably poly (methyl methacrylate) (PMMA), cellulosics, nylons, poly (esters), poly (acetals); poly (amides), poly (arylate), aromatic polyesters, poly (carbonate), poly (butylene) and polybutylene and polyethylene terephthalates, more preferably poly (methyl methacrylate) (PMMA), and poly (esters). The polymer composition used to prepare the homohyl fibers of the present invention can comprise from 0 to 50, preferably from 5 to 50, more preferably from 10 to 40 percent by weight (based on the final weight of the polymer or the mixture of the polymer) of one or more "viscosifiers comprising aliphatic resins, polyterpene resins, hydrogenated resins, mixed aromatic aliphatic resins, styrene / alpha-methylene styrene resins, pure monomer hydrocarbon resin, hydrogenated pure monomer hydrocarbon resin, copolymers of modified styrene, copolymers of pure aromatic monomer, and hydrogenated aliphatic hydrocarbon resins For the bicomponent fibers of the present invention the first component comprises a substantially random interpolymer having the compositions and properties as used to prepare the homozygous fibers of the present invention and present in an amount of from 5 to 95, pre preferably from 25 to 95, more preferably from 50 to 95 weight percent (based on the combined weight of. first and second components of the bicomponent fiber). The second component is present in an amount of from 5 to 95, preferably from 5 to 75, more preferably from 5 to 50 weight percent (based on the combined weight of the first and second components of the bicomponent fiber). The shape memory composition used to prepare the structures and articles manufactured of the present invention having shape memory properties can also comprise from 0 to 80, preferably from 0 to 50, more preferably from 0 to 20 weight percent (based on the final weight of the polymer or polymer mixture) of one or more fillers, comprising talc, carbon black, carbon fibers, calcium carbonate, aluminum oxide trihydrate, glass fibers, marble powder, cement powder, clay, feldspar, silicon oxide or glass, smoked silicon oxide, aluminum oxide, magnesium oxide, magnesium hydroxide, antimony oxide, zinc oxide, barium sulfate, aluminum silicate, calcium silicate , titanium dioxide, titanates, glass microspheres or gis. Of these fillers, talc, calcium bicarbonate, carbon black and titanium dioxide, and mixtures thereof are preferred. The most preferred inorganic fillers are calcium carbonate, carbon black and titanium dioxide or mixtures thereof. The interpolymer or mixture used to prepare the molded structures and the manufactured articles of the present invention having shape memory properties should have a glass transition temperature (Tg) of 40 ° C to 50 ° C, preferably 18 ° C up to 50 ° C glass transition temperature, more preferably 23 ° C to 45 ° C since this range will cover all applications used in the ambient temperature range. The interpolymer of most interest will have a very sharp transition temperature to glass (at any temperature) plus_ will show an impressive change in modulus as the glass transition temperature is reached. The glass transition temperature of the interpolymer or mixture used to prepare the structures. molded and fabricated articles of the present invention having shape memory properties can be controlled by variation in both the monomer composition of the substantially random interpolymer and its overall molecular weight. In this way the increase in the styrene content and the molecular weight of the ethylene / styrene interpolymers can be used to further increase their glass transition temperature (in addition to the aforementioned use of viscosifiers). This invention could be a heat insulator made of foam or molded portion of shape memory polymer having good molding ability and greatly changing the elastic modulus above and below its transition point to glass. Furthermore, this invention could be a fibrous sheet having a shape memory property comprising a sheet made of natural fiber and / or synthetic fiber and a layer formed by applying a shape memory polymer powder.; and a method for imparting shape memory property which comprises applying a shape memory polymer powder to a desired part of a product of a sheet made of natural fiber and / or synthetic fiber by the aid of a resin adhesive . The product of the present invention can be used by the end user for any article that could have a more efficient way to transport it and revert to the original shape, using the process of the present invention. Also included are toys, cushioning devices such as cushions and mattresses that could have the shape of the body, bonding materials for single tubes, internal rolling materials for tubes, household articles such as trays, jugs, lids, and containers, grinders, handles, hooks to withstand merchandise, lining materials, mats. 91 sprinkler, stop clips, instrument materials, medical devices such as stationery and educational materials, artificial flowers, dolls, computer-printed printer roller inner laminates, noise-proof materials, limbs that require restoring deformation after impact absorption such as car bumpers, car seats, armrests and backrests, materials that avoid the gap of water partition members, portable containers which bend when not in use and restore their shape during use , mechanical device such as coupler, etc., various shrinkable tubes with heat, and so on. Other uses include a softening duct to carry fluids in and out of the human body, dynamic polymer composites, a retraction-coated catheter balloon, an endoscopic surgical retractor, a deformable endoscopic surgical retractor, protective equipment, emergency tips, a specimen reduction device, a lock plug of a defect for medical use, make-up material for human use, woven and non-woven fabrics made of polymer with 'shape memory, heat insulators made of foam polymer with memory; shape, amorphous reformed polymer alignment device with an access element, a shape-memory polymer foam 92, multi-cavity fiber restitution polymer formula restorer, formula and polymer restoration fiber optic separator methods The shape memory fibers of the present invention may also have applications such as fibers for mats, elastic fibers, wrist hair, female personal hygiene applications, diapers, sports articles, wrinkle-free and form-fitting articles, conductive fibers , upholstery, and medical applications including, but not limited to, bandages, non-woven sterilizable fibers, woven fabric made with shape memory polymer, shape memory fibrous sheet and method for imparting shape memory property, a product with fibrous sheet. The following examples are illustrative of the invention, but are not to be construed as limiting the scope thereof in any way. EXAMPLES Test Methods a) Flow Measurements and Melt Density The molecular weight of the polymer compositions was determined for use in the present invention which is conveniently indicated using the measurement of. melt index according to ASTM D-1238, Condition 190 ° C / 2.16 kilograms (formally known as ^ Condition (The "and. 33 also known as I;). The melt index is inversely proportional to the molecular weight of the polymer. In this way, the higher the molecular weight, the lower the melting index, although the relationship is not linear. Also useful to indicate the molecular weight of the substantially random interpolymers used in the present invention is the Gottfert melt index (G, cmVlO minutes) which is obtained in a manner similar to the Melt Index (I2) using the .ASTM method. D1238 for automated plastomers, with the fixed melt density at 0.8732, the melt density of polyethylene at 190 ° C. The ratio of the melt density to the styrene content for the ethylene-styrene interpolymers was measured, as a melt of the total styrene content, at 190 ° C for a range of 29.8 percent to 81.8 percent by weight of styrene . The levels of atactic polystyrene in these samples was typically 10 percent Q less. The influence of atactic polystyrene was assumed to be minimal due to low levels. Also, the fusion density of the atactic polystyrene and the melting densities of the samples with high total styrene were very similar. The method used to determine the melt density employed a Gottfert fusion index machine with. a fixed melt density parameter at 0.7632, and the collection of fusion strands as a function of time 94 while the weight of I2 ^ was in force. The weight and time for each melting strand were recorded and normalized to produce the mass in grams per 10 minutes. The calculated melt index value I of the instrument was also recorded. The equation used to calculate the actual fusion density is d = do.7632 x I2 / I2 Gottfert where d0.7b32 = 0.7632 and I2 Gottfert = displayed melting index. An adjustment of linear least squares of melt density calculated against total styrene content leads to an equation with a correlation coefficient da. 0.91 for the following equation: d = 0.00299 x S + 0.723 where S = weight percentage of styrene in the polymer. The ratio of the total styrene to the melt density can be used to determine a current melt index value, using these equations if the styrene content is known. _ So for a polymer that is 73 percent total styrene content with a measured melt flow (the "Gottfert number"), the calculation comes-being: x = 0 00299 * 73 + 0. 723 = 0 9412 where 0. 9412/0. 7632 = IjGü (measured) = 1. 2.3 95 The density of the substantially linear interpolymers used in the present invention is determined in accordance with .ASTM D-792. B) Styrene analysis The styrene content and the atactic polystyrene concentration of the interpolymer were determined using proton nuclear magnetic resonance (lH N.M.R). All samples of nuclear magnetic resonance protons were prepared in 1, 1, 2, 2-tetrachloroethane-d2 (TCE-d2). The resulting solutions were 1.6 - 3.2 percent polymer by weight. The melt index (I2) was used as a guide to determine the concentration of the sample. Thus when the I2 is greater than 2 grams / 10 minutes, 40 milligrams of interpolymer was used; with a melt index between 1.5 and 2 grams / 10 minutes, 30 milligrams of interpolymer was used; and when the melt index was less than 1.5 grams / 10 minutes, 20 milligrams of interpolymer was used. The interpolymers were weighed directly into 5-millimeter sample tubes. An aliquot of 0.75 milliliters of TCE-d¿ was added by syringe and the tube was capped with a tight fitting polyethylene cap. The samples were heated in a water bath at 85 ° C to soften the interpolymer. To provide mixing, the plugged samples were occasionally refluxed using a heat gun.

The proton nuclear magnetic resonance spectra were accumulated in a Varian VXR 300 with the sample probe at 80 ° C, and reference was made to the residual protons of TCE-d2 at 5.99 ppm. The delay times were varied between 1 second, and the data was collected in triplicate on each sample. The following instrumental conditions were used for the analysis of the interpolymer samples: Varian VXR-300,: H standard:. Sweep amplitude, 5000 Hertz Acquisition time, 3,002 seconds. Pulse amplitude, 8 μsec Frequency, 300 MHz Delay, 1 second Transients, 16 The total analysis time per sample was approximately 10 minutes. Initially, a 1 H nuclear magnetic resonance spectrum for a polystyrene sample, Styron® 680 (available from The Dow Chemical Company, Midland, MI) was acquired with a delay time of one second. The protons were "labeled": b, branch; a, alpha; or, ortho; m, goal; p, for, as shown in Figure 1. 98 aliphatic 2 to 1 was predicted based on the protons labeled a and b respectively in Figure 1. This ratio was also observed when two aliphatic peaks were integrated separately. For the ethylene / styrene interpolymers, the 1 H nuclear magnetic resonance spectra using a delay time of one second, had the C-7 integrals. Y AC? defined, so that the integration of the peak at 7.1 ppm included all the aromatic protons of the copolymer as well as the protons o and p of aPS. Likewise, the integration of the Cdi aliphatic region in the. The interpolymer spectrum includes aliphatic protons from both aPS and the interpolymer with no clear baseline resolved signal from either of the two polymers. The peak integral at 6.6 ppm C6.6 was resolved for the other aromatic signals and is believed to be due solely to the aPS homopolymer (probably the target protons). (The peak assignment for atactic polystyrene at 6.6 ppm (integral A .b) was made - based on the comparison with the authentic sample of Styron® 680). This is a reasonable assumption since, at very low levels of atactic polystyrene, only a very weak signal was observed here. Therefore, the phenyl protons of the -copolymer should not contribute to this signal. With this assumption, the integral A6.e becomes the basis for quantitatively determining the aPS content. 99 The following equations were then used to determine the degree of styrene incorporation in the ethylene / styrene interpolymer samples: (C Phenyl) = C7. + A7.? - (1.5 x Ab.6) (C Aliphatic) = Ca? - (1.5 x Ab. Sc = (C Phenyl) / 5 ec = (C Aliphatic - (3 x sJ) / 4 E = ec / (ec + sc) Sc = sc / (ec + sc) and the following equations are used to calculate the molar percent of ethylene and styrene in the interpolymers: weight% E = E * 28 (100) f28) + (S-104) Y weight% S Sc 104 100) (E * 28) + (S-) * 104) where: sc and e are proton fractions of styrene and ethylene in the interpolymer, respectively, and Sc and E are molar fractions of styrene monomer and ethylene monomer in the interpolymer, respectively. The weight percentage of aPS in the interpolymers. was then determined by the following equation: (weight% S) * A6.6 / 2 __ 100 -t (weight?, S) * A,., Y2 100 The total styrene content was also determined by infrared Fourier transform spectroscopy (FTIR). The test parts and the characterization data. for the interpolymers and their mixtures were generated according to the following procedures: Compression molding The samples were melted at 190 ° C for 3 minutes and compression molded at 190 ° C under 9,072 kg pressure for another 2 minutes. Subsequently, the molten materials were annealed in a press balanced at room temperature. Injection molding The samples were injection molded in a 150-ton injection molding machine from Mag to 190 ° C melting temperature, one second of injection time, water temperature 21 ° C, and overall cycle time of 60 seconds.The mold was a test mold .ASTM including test specimens of flexural modulus .ASTM with 1.27 centimeters by 12.7 centimeters by 1.9 millimeters of thickness Differential Scanning Calorimetry (DSC) A Dupont DSC-2920 was used to measure the thermal transition temperatures and the heat of the transition of the interpolymers. After removing previous thermal history, the samples were first heated to 200 ° C. The heating and cooling curves were recorded at 10 ° C / minute, the melting (from the second heat) and the crystallization temperatures were recorded from peak temperatures of the endotherm and exotherm, respectively Preparation of ESI interpolymers used in the examples and comparative experiments of the present invention 1) Preparation of ESI # 1-6 The int Erpolymers were prepared in a stirred-batch semicontinuous reactor of 1.514 liters. The reaction mixture consisted of approximately 946 liters of a solvent comprising a mixture of cyclohexane (85 weight percent) and isopentane (15 weight percent), and styrene. Before the addition, the solvent, styrene and ethylene were purified to remove water and oxygen. The inhibitor in styrene was also removed. The inerts were removed by purging the vessel with ethylene. The pressure was controlled to a container to a fixed point with ethylene. Hydrogen was added to control the molecular weight. The container temperature was controlled to the set point by varying the water temperature of the jacket in the container. Before the polymerization, the vessel was heated to a desired execution temperature and the flow of titanium catalyst components was controlled: (Nl, 1-dimethylethyl) dimethyl (1- (1,2,3,4,5 -eta) - 2, 3, 4, 5-tetramethyl-2,4-cyclopentadiene-1-yl) silanaminate)) (2-) N) -dimethyl, CAS # 135072-62-7 and tris (pentafluorophenyl) boron, CAS # 001109-15-5, modified methylaluminoxane type 3A, CAS # 146905-79-5, on a molar ratio basis of 1/3/5 respectively, were combined and added to the vessel. Before starting, the polymerization was allowed to continue with ethylene supplied to the reactor as required to maintain the container pressure. In some cases, hydrogen was added to the reactor gap to maintain a molar ratio to the ethylene concentration. At the end of the run, the catalyst flow was stopped, the ethylene was removed from the reactor, approximately 1000 ppm of Irganox® 1010 was added to the solution and the polymer was isolated in solution. The resulting polymers were isolated from the solution either by being vaporized in a vessel or by the use of a devolatilizing extruder. In the case of steam-split material, additional processing in extruder-like equipment was required to reduce residual moisture and any unreacted styrene. The specific preparation conditions for each interpolymer are summarized in Table 1 and their properties in Table 2. 103 104 105 1) Preparation of ESI # 7 - 25 ESI # 7-25 are substantially random interpolymers of ethylene / styrene prepared using the following catalyst and polymerization methods. Preparation of catalyst A (tell me üTN- (1, 1-dimethylethyl) -1, 1-dimethyl-l- [(1, 2, 3, 4, 5-?) -1, 5, 6, 7-tetrahydro-3-phenyl-s-indacene-1-yl ] silanaptinate (2-) -N] -titanium) 1) Preparation of 3, 5, 6, 7-Tetrahydro-s-Hydrindacen-l (2H) -one Indan (94.00 grams, 0.7954 moles) and 3-chloropropionyl chloride (100.99 grams, 0.7954 moles) were stirred in CH2C12 (300 milliliters) at 0 ° C according to A1C1_, (130 ^ 00 grams, -0.9750 moles) was slowly added under a nitrogen flow. The mixture was allowed to stir at room temperature for 2 hours. Then the volatiles were removed. The mixture was cooled to 0 ° C and concentrated H2SO4 (500 milliliters) was slowly added. The solid that formed had to be broken frequently with a spatula. he lost precocious agitation. The mixture was left under nitrogen overnight at room temperature. The mixture was heated until the temperature readings reached 90 ° C. These conditions were maintained for a period of 2 hours during which time the spatula was used periodically to stir the mixture. After the reaction period, crushed ice was placed in the mixture and moved around, the mixture was transferred to a beaker 106 and washed intermittently with H20 and diethyl ether and then the fractions were filtered and combined. it was washed with H20 (2 x 200 milliliters) The organic layer was then separated and the volatiles were removed The desired product was isolated via recrystallization from hexane at 0 ° C as pale yellow crystals (22.36 grams, yield 16.3 percent) .IK NMR (CDC13): d2.04-2.19 (m, 2 H), 2.65 (t, 3JHH = 5.7 Hz, 2 H) 2.84-3.0 (m, 4 H), 3.03 (t, 3JHH = 5.5 Hz, 2 H), 7.26 (s, 1 H), 7.53 (s, 1 H), 13C NMR (CDC13): d25.71, 26.01, 32.19, 33.24, 36.93, 118. 0, "" 122.16, 135.88, 144.06, 152.89, 154.36, 206.50 GC-MS: Calculated for C12H120 172.09, found 172.05 2) Preparation of 1, 2, 3, 5-Tetrahydro-7-phenyl-s-indacene. 3.5, 6.7-Tetrahydro-s-Hydridandane-1 (2H) -one (12.00 grams 0.06967 moles) was stirred in diethyl ether (200 milliliters) at 0 ° C according to PhMgBr (0.105 moles, 35.00 milliliters of 3.0 M of solution in diethyl ether) was added slowly. This mixture was then allowed to stir overnight at room temperature. After the reaction period the mixture was tempered by placing it on ice. The mixture was acidified (pH = 1) with HCl and stirred vigorously for 2 hours. The organic layer was separated and washed with H20 (2 x 100 milliliters) and then dried over MgSOd. The filtration followed by the removal of the volatiles gave as follows: the isolation of the desired product as a dark oil (14.68 grams, 90.3 percent yield). lE NMR (CDC13): d2.0-2.2 (m, 2 H), 2.8-3.1 (m, 4 H), 6.54 (s, 1 H), 7.2-7.6 (m, 7 H). GC-MS: Calculated for CißHit, 232.13, found 232.05. 3) Preparation of 1, 2, 3, 5-Tetrahydro-7-phenyl-s-indacene, dilithium salt. 1, 2, 3, 5-Tetrahydro-7-phenyl-s-indacene (14.68 grams 0.06291 moles) was stirred in hexane (150 milliliters) as nBuLi (0.080 moles, 40.00 milliliters of 2.0 M solution in cyclohexane) was added slowly. The mixture was allowed to stir overnight. After the reaction period the solid was collected via suction filtration as a yellow solid which was washed with hexane, dried in vacuo, and used without further purification or analysis (12.2075 grams, yield 81.1 percent). 4) Preparation of Chlorodimethyl (1, 5, 6, 7-tetrahydro-3-phenyl-s-indacen-1-yl) silane. 1, 2, 3, 5-Tetrahydro-7-phenyl-s-indacene, dilithium salt (12.2075 grams, 0.05102 moles) in THF (50 milliliters) was added dropwise to a solution of Me2SiCl® (19.5010 grams, 0.1511 moles) in THF (100 milliliters) at 0 ° C. This mixture was allowed to stir at room temperature overnight. After the reaction period the volatiles were removed-and the residue was extracted and filtered using hexane. Removal of hexane resulted in the isolation of the desired product as a yellow oil (15.1492 grams, 91.1 percent yield). XH NMR (CDC13): d? .33 (s, 3 H), 0.38 (s, 3 H), 2.20 (p.3JHH = 7.5 Hz, 2 H), 2.9-3.1 (m, 4 H), 3.84 ( s, 1 H), 6.69 (d, 3 JHH = 2.8 Hz, 1 H), 7.3-7.6 (m, 7 H), 7.68 (d, 3 JHH = 7.4 Hz, 2 H). 13C NMR (CDCI3): d0.24, 0.38, 26.28, 33.05, 33.18, 46.13, 116.42, 119.71, 127.51, 128.33, 128.64, 129.56, 136.51, 141.31, 141.86, 142.17, 142.41, 144.62. GC-MS: Calculated for C20H2? ClSi 324.11, found 324.05.

) Preparation of N- (1,1-Dimethylethyl) -1,1-dimethyl-1- (1, 5, 6, 7-tetrahydro-3-phenyl-s-indacen-1-yl) silanamine. Chlorodimethyl (1, 5, 6, 7-tetrahydro-3-phenyl-s-indacen-1-yl) silane (10.8277 grams, 0.03322 moles) was "stirred in hexane (150 milliliters) according to NEt3 (3.5123 grams, 0.03471 moles' ) and t-butylamine (2.6074 grams, 0.03565 moles) were added.This mixture was allowed to stir for 24 hours.After the reaction period the mixture was filtered and the volatiles were removed resulting in the isolation of the desired product as a thick oil red-yellow (10.6551 grams, 88.7 percent yield). 109 X H NMR (CDCl 3): d? .02 (s, 3 H), 0.04 (s, 3 H), 1.27 (S, 9 H), 2.16 (p, 3 JHH = 7.2 Hz, 2 H), 2.9-3.0 (m, 4 H), 3.68 (s, 1 H), 6.69 (s, 1 H), 7.3-7.5 (m, 4 H), 7.63 (d, YHH = 7.4 Hz, 2 H). 13C NMR (CDCI3): d? .32, -0.09, 26.28, 33.39, 34.11, 46.46, 47.54, 49.81, 115.80 119.30, 126.92, 127.89, 128.46, 132.99, 137.30, 140.20, 140.81, 141.64, 142.08, 144.83. 6) Preparation of N- (1,1-Dimethylethyl) -1,1-dimethyl-1- (1, 5, 6, 7-tetrahydro-3-phenyl-s-indacen-1-yl) silanamine, dilithium salt. N- (1,1-Dimethylethyl) -1,1-dimethyl-1- (1, 5, 6, 7-tetrahydro-3-phenyl-s-indacen-1-yl) silanamine (10.6551 grams, 0.02947 moles) is stirred in hexane (100 milliliters) as NBuLi (0.070 moles, 35.00 milliliters of 2.0 M solution in cyclohexane) was added slowly. This mixture was allowed to stir overnight during this time no salts of the dark red solution were precipitated. After the reaction period the volatiles were removed and the residue was rapidly washed with hexane (2 x 50 milliliters). The red residue was pumped dry and was used without further purification or analysis (9.6517 grams, 87.5 percent yield). 7) Preparation of Dichloro [N- (1,1-dimethylethyl) -1,1-dimethyl-1 - [(1, 2,3,4,5-y) -1,5,6,7-tetrahydro-3 phenyl-s-indacen-1-yl] silanaminate (2-) -N] titanium N- (1,1-Dimethylethyl) -1,1-dimethyl-1- (1, 5, 6, 7- 110 tetrahydro- 3-phenyl-s-indacen-1-yl) silanamine, dilithium salt (4.5355 grams, 0.01214 moles) in THF (50 milliliters) was added dropwise to a slurry of TiCl 3 (THF) 3 (4.5005g, 0.01214 moles) ) in THF (100 mL). This mixture was allowed to stir for 2 hours. Then PbCl2 (1.7136 grams, 0.006162 moles) was added and the mixture was allowed to stir for an additional hour. After the reaction period the volatiles were removed and the residue was extracted and filtered using toluene. Removal of toluene resulted in the isolation of a dark residue. This residue was made slurry in hexane and cooled to 0 ° C. The desired product was isolated via filtration as a reddish brown crystalline solid (2.5280 grams, yield 43.5 percent). aH NMR (CDC13): dO.71 (s, 3 H), 0.97 (s, 3 H), 1.37 (s, 9 H), 2.0-2.2 (m, 2 H), 2.9-3.2 (m, 4 H) ), 6.62 (s, 1 H), 7.35-7.45 (m, 1 H), 7.50 (t, YHH = 7.8 Hz, 2 H), 7.57 (s, 1 H), 7.70 (d, 3 JHH = 7.1 Hz, 2 H), 7.78 (s, 1 H). H NMR (C6D6): d0.44 (s, 3 H), 0.68 (s, 3 H), 1.35 (s, 9 H), 1.6-1.9 (m, 2 H), 2.5-3.9 (m, 4 H) ), 6.65 (s, 1 H), 7.1-7.2 (m, 1 H), 7.24 (t, 3JHH = 7.1 Hz, 2 H), 7.61 (s, 1 H), 7.69 (s, 1 H), 7.77 -7.8 (, 2 H). 13C NMR (CDCI3): di.29, 3.89, 26.47, 32.62"X 32.84, 32.92, 63.16, 98.25, 118.70, 121.75, 125.62, 128.46, 128.55, 128.79, 129.01, 134.11, 134.53, 136.04, 146.15, 148.93. NMR (CbD "): d? .90, 3.57, 26.46, 32.56, 32.78, 62.88," 111 98.14, 119.19, 121.97, 125.84, 127.15, 128.83, 129.03, 129.55, 134.57, 135.04, 136.41, 136.51, 147.24, 148.96 . 8) Preparation of Dimethyl [N- (1,1-dimethylethyl) -1,1-dimethyl-1 - [(1, 2,3,4,5-y) -1,5,6,7-tetrahydro-3-phenyl] -s-indacen-1-yl] silanaminate (2-) -Nichitanium DichlorofN- (1,1-dimethylethyl) -1, 1-dimethyl-1 - [(1, 2,3,4,5-γ) -1.5 , 6,7-tetrahydro-3-phenyl-s-indacen-1-yl] silanaminate (2-) -N] titanium (0.4970 grams, 0.001039 moles) was stirred in diethyl ether (50 milliliters) as MeMgBr was added slowly ( 0.0021 moles, 0.70 milliliters of 3.0 solution M diethyl ether). This mixture was stirred for 1 hour. After the reaction period the volatiles were removed and the residue was extracted and filtered using hexane. Removal of hexane resulted in the isolation of the desired product as a golden yellow solid (0.4546 grams, yield 66.7 percent). : H NMR (C6D6): d0.071 (s, 3 H), 0.49 (s, 3H), 0.70 (s, 3 H), 0.73 (s, 3 H), 1.49 (s, 9 H), 1.7- 1.8 (m, 2 H), 2.5-2.8 (m, 4 H), 6.41 (s, - 1 H), 7.29 (t, JHH = 7.4 Hz, 2 H), 7.48 (s, 1 H), 7.72 fd , 3JHH = 7.4 Hz, 2 H), 7.92 (s, 1 H). 13C NMR (C6D6): d2.19, 4.61, 27.12, 32.86, 33.00, 34.73, "58.68, 58.82, 118.62, 121.98, 24.26, 127.32, 128.63, 128.98, 131.23, 134.39, 136.38, 143.19, 144.85. _ 3_ 112 Preparation of bis (hydrogenated tallow alkyl) cocatalyst methylamine Methylcyclohexane (1200 milliliters) was placed in a 2-liter cylindrical flask.While stirring, 104 grams of bis (hydrogenated tallow alkyl) methylamine milled to a granular form (.ARMEEN® M2HT available from Akzo Chemical), added to the flask and stirred until completely dissolved HCl aqueous (1M, 200 milliliters) was added to the flask, and the mixture was stirred for 30 minutes. a white precipitate. At the end of this time, LiB (CfoF5) 4 * Et20 * 3 LiCl was added to the flask.

(Mw = 887.3, 177.4 grams). The solution began to turn milky white. The flask was equipped with a 16 cm Vigreux column covered with a distillation apparatus and the mixture was heated (140 ° C external wall temperature). A mixture of ether and methylcyclohexane was distilled from the flask. The two-phase solution was now only slightly cloudy. The mixture was allowed to cool to room temperature, and the contents were placed in a 4 liter separatory funnel. The aqueous layer was removed and discarded, and the organic layer was washed twice with H20 and again the aqueous layers were discarded. Saturated methylcyclohexane solutions of H_0 were measured to contain 0.48 weight percent diethyl ether (Et2Q). The solution (600 milliliters) was transferred to a one liter flask, dispersed thoroughly with nitrogen, and transferred to the drying box. The solution was passed through a column (diameter 2.54 centimeters, 15.24 centimeters in height) containing 13X molecular sieves. This reduced the Et20 level from 0.48 weight percent to 0.28 weight percent. The material was then stirred on new 13X screens (20 grams) for four hours. The level of Et0 was measured to be 0.19 weight percent. The mixture was stirred overnight, resulting in another reduction in the Et20 level to approximately 40 ppm. The mixture was filtered using a funnel equipped with a porous glass having a pore size of 10-15 microns to give a clear solution (the molecular sieves were rinsed with additional dry methylcyclohexane). The concentration was measured by gravimetric analysis yielding a value of 16.7 weight percent. Polymerization ESI # 7-25 were prepared in a tank reactor with continuous autoclave agitation, with 22.7 liter oil jacket (CSTR). A stirrer magnetically coupled with Lightning A-320 propellers provided mixing. The reactor ran full liquid at 3,275 kPa. The process flow was in the lower part and outside the upper part. Heat transfer oil was circulated through the jacket of the reactor to remove something from the heat of the reaction. At the outlet of the reactor was a micromotion flow meter that measured the flow and density of the solution. All the lines of the reactor outlet were tracked with a steam of 344.7 kPa and were isolated. The toluene solvent was supplied to the reactor at 207 kPa. The feed to the reactor was measured by a Micro-Motion mass flow meter. A variable speed diaphragm pump controlled the feeding speed. In the discharge of the solvent pump, a side stream was taken to provide wash flows for the catalyst injection line (0.45 kilogram / hour) and the reactor agitator (0.34 kilogram / hour). These flows were measured by differential pressure flow meters and controlled by manual adjustment of the microflow needle valve. The uninhibited styrene monomer was supplied to the reactor at 207 kPa. The feed to the reactor was measured by means of a Micro-Motion mass flow meter. A variable speed diaphragm pump controlled the feeding speed. The styrene stream was mixed with the remaining solvent stream. The ethylene was supplied to the reactor at 4,137 kPa. The ethylene stream was measured by a Micro-Motion mass flow meter just before the Research valve controlling the flow. 115 A Brooks flow meter / controller was used to deliver hydrogen to the ethylene stream at the outlet of the ethylene control valve. The ethylene / hydrogen mixture combines with the solvent / styrene stream at room temperature. The temperature of the sol / conforming monomer entering the reactor was lowered to about 5 ° C by a glycol exchanger at -5 ° C in the jacket. This current entered the bottom of the reactor. The three-component catalyst system and its solvent stream also entered the reactor from below but through a different gate than the monomer stream. The preparation of the catalyst components was carried out in a glovebox under inert atmosphere. The diluted components were placed in nitrogen-filled cylinders and loaded into tanks of catalyst runs in the process area. From these run-off tanks the catalyst was pressurized with piston pumps and the flow was measured with Micro-Motion mass flow meters. These streams were combined with each other and the catalyst stream solvent just before entering through a single injection line in the reactor. The polymerization was stopped with the addition of a catalyst scavenger (water mixed with solvent) in the reactor product line after the micromotion time meter measured the density of the solution. 116 Other polymer additives can be added with the catalyst eliminator. A static mixer in the line provided dispersion of the catalyst scavenger and additives in the reactor effluent stream. This current then entered the heaters after the reactor that provide additional energy for the solvent removal stream. This washing occurred as the effluent left the rear reactor heater and the pressure was lowered from 3,275 kPa to below approximately 250 millimeters of absolute pressure in the reactor pressure control valve. This washed polymer entered a devolatilizer with an oil jacket. Approximately 85 percent of the volatiles were removed from the polymer in the devolatilizer. The volatiles came out through the top of the devolatilizer. The stream was condensed with a glycol jacket exchanger and entered the suction of a vacuum pump and discharged in a glycol jacket solvent and styrene / ethylene separation vessel. The solvent and styrene were removed from the bottom of the container and the ethylene from the top. The ethylene stream was measured with a Micro-Motion mass flow meter and analyzed to determine its composition. The measurement of ventilated ethylene plus a calculation of the gases dissolved in the solvent / styrene stream were used to calculate the conversion of ethylene. The polymer separated in the devolatilizer was pumped out with a gear pump to a vacuum devolatilizing extruder ZSK-30. The dried polymer leaves the extruder as a single strand. This strap cooled and was pulled through a water bath. Excess water was blown from the belt with air and the belt cut into granules with a belt cutter. The different catalysts, cocatalysts and process conditions used to prepare the individual ethylene / styrene interpolymers (ESI # 7-25) are summarized in Table 3 and their properties are summarized in Table 4. 118 LO 120 ittt * N / D = not available Preparation of ESI # 26-31 121 ESI # 26-31 were substantially random ethylene / styrene interpolymers prepared using the following catalyst and polymerization procedures. Preparation of catalyst A; (lH-cyclopenta [l] phenanthrene-2-yl) dimethyl) t-butylamido) -silanetitanium 1,4-diphenylbutadiene 1) Preparation of lithium lH-cyclopenta [l] phenentreno-2-yl To a flask with a round bottom of 250 milliliters containing 1.42 grams (0.00657 moles) of 1H-cyclopenta [l] phenanthrene and 120 milliliters of benzene was added dropwise, 4.2 milliliters of a solution of 1.60 M7 of n-BuLi in mixed hexanes. The solution was allowed to stir overnight. The lithium salt was isolated by filtration, washing it twice with 25 milliliters of benzene and drying it under vacuum. The isolated production was 1,426 grams (97.7 percent). Nuclear magnetic resonance 1E analysis indicated that the predominant isomer was substituted at position 2. 2) Preparation of (lH-cyclopenta [l] phenanthrene-2-yl) dimethylchlorosilane To a 500 milliliter round bottom flask containing 4.16 grams (0.03222 moles) of dimethyldichlorosilane (Me2SiCl) and 250 milliliters of tetrahydrofuran (THF) was added, dropwise to a solution of 1.45 grams (0.0064 mole) of lithium lH-cyclopenta [l] phenanthrene-2-yl in THF. The solution was stirred for approximately 16 hours, after which the solvent was removed under reduced pressure, leaving only an oily solid which was extracted with toluene, filtered through the aid of diatomaceous earth filter (Celite®), it was washed twice with toluene and dried. under reduced pressure. The isolated yield was 1.98 grams (99.5 percent). 3) Preparation of (lH-cyclopenta [l] phenanthrene-2-yl) dimethyl (t-butylamino) silane To a 500 milliliter round bottom flask containing 1.98 grams (0.0064 mole) of 1H-cyclopenta [l] phenanthrene- 2-yl) dimethylchlorosilane and 250 milliliters of hexane were added 2.00 milliliters (0.0160 moles) of t-butylamine. The reaction mixture was allowed to stir for several days, then filtered using a diatomaceous earth filter aid (Celite®), washed twice with hexane. The product was isolated by removing the residual solvent under reduced pressure. The isolated yield was 1.98 grams (88.9 percent). 4) Preparation of (lH-cyclopenta [l] phenanthrene-2-yl) dimethyl (t-butylamino) silane-dilithium To a 250 milliliter round bottom flask containing 1.03 grams (0.0030 moles) of (1H-cyclopenta [l. ] phenanthrene-2-yl) dimethyl (t-butylamino) silane and 120 milliliters of benzene were added dropwise to 3.9 milliliters in a 1.6M solution of n-BuLi in mixed hexanes. The reaction mixture was stirred for approximately 16 hours. The product was isolated by filtration, washed twice with benzene and dried under reduced pressure. The isolated yield was 1.08 grams (100 percent). 5) Preparation of (lH-cyclopenta [l] phenanthrene-2-yl) dimethyl (t-butylamino) silanetitanium dichloride __ To a 250 milliliter round bottom flask containing 1.17 grams (0.0030 moles) of TiCl.j * 3THF and about 120 milliliters of THF was added at a fast drip rate to approximately 50 milliliters of a THF solution of 1.08 grams of (1H-cyclopenta [l] phenanthrene-2-yl) dimethyl (t-butylamino) silane dilithium. The mixture was stirred at about 20 ° C for 1.5 hour at which time 0.55 gram (0.002 mole) of solid PbCl2 was added. After stirring for an additional 1.5 hours the THF was removed in vacuo and the residue was extracted with teoluene, filtered and dried under reduced pressure to give an orange solid. The yield was 1.31 grams (93.5 percent). 6) Preparation of (lH-cyclopenta [l] phenanthrene-2-yl) dimethyl (t-butylamino) silanetitanium 1,4-diphenylbutadiene To an aqueous part of (1H-cyclopenta [l] phenanthrene-2-yl) dimethyl dichloride (t-butylane) silanetitanium (3.48 grams, 0.0075 molesT and 1,551 grams (0.0075 moles) of 1,4-diphenylbutadiene in 124 about 80 milliliters of toluene at 70 ° C were added 9.9 milliliters of a 1.6M solution of n- BüLi (0.0150 moles) The solution immediately darkened The temperature was increased to reflux the mixture and the mixture was kept at that temperature for 2 hours The mixture was cooled to about -20 ° C and the volatiles were removed under reduced pressure The residue was made watery in 60 milliliters of hexanes mixed at about 20 ° C for about 16 hours The mixture was cooled to about -25 ° C for 1 hour The solids were collected on a porous glass by filtration vacuum and dried under pr The dried solid was placed in a glass fiber filter element and the solid was continuously extracted with hexanes using a soxhlet extractor. After 6 hours a crystalline solid was observed in the kettle. The mixture was cooled to about -20 ° C, isolated by filtration from the cold and dry mixture under reduced pressure to give 1.62 grams of dark crystalline solid. The filtrate was discarded. The solids in the extractor were stirred and the extraction continued with an additional amount of mixed hexanes to give an additional 0.46 grams of the desired product as dark crystalline solid. Polymerization ESI # 26-31 were prepared in a continuous operation cycle reactor (139.3 liters). An Ingersoll-Dresser twin screw pump provided mixing. The reactor ran full liquid to 3, 275 kPa with a residence time of approximately 25 minutes. The raw material and the catalyst / cocatalyst were fed into the suction of the twin screw pump through Kenics static mixers and injectors. The pump with twin screws discharged in a line of 5 centimeters in diameter which supplied two muititube heat exchangers type BEM Chemineer-Kenics 10-6-8 in series. The tubes of these exchangers contained twisted ribbons to increase heat transfer. After leaving the last exchanger, the cycle flow returned through the injectors and static mixers to the suction pump. The heat transfer oil was circulated through the jacket of the exchangers to control the temperature probe of the cycle just before the first exchanger. The output current of the cycle reactor was removed between the two exchangers. The flow and density of the solution-the output current was measured by a Micro-Motion. The solvent fed to the reactor was supplied by two different sources. A new toluene stream from a Pulsafeeder 8480-S-E diaphragm pump with velocities measured by a Micro-Motion flow meter was used to provide 126 wash flows for the reactor seals (9.1 kilogram / hour). The recycled solvent was mixed with styrene monomer inhibited on the suction side of five Pulsafeeder 8480-5-E diaphragm pumps in parallel. These five Pulsafeeder pumps supplied solvent and styrene to the reactor at 4,583 kPa. The new styrene flow was measured by a Micro-Motion flow meter, and the total solvent / styrene recycle flow was measured by a separate Micro-Motion flow meter. The ethylene was supplied to the reactor at 4,838 kPa. The ethylene stream was measured by a Micro-Motion mass flow meter. A Brooks flow meter / controller was used to deliver hydrogen to the ethylene stream at the outlet of the ethylene control valve. The ethylene / hydrogen mixture was combined with solvent / styrene stream at room temperature. The temperature of the entire feed stream was brought into the reactor cycle and lowered to 2 ° C by a glycol exchanger at -10 ° C in the jacket. The preparation of the three components of the catalyst was carried out in three separate tanks: new solvent and premix of catalyst concentrate / cocatalyst were added and mixed in their respective run tanks and fed to the reactor via Pulsafeeder 680-S diaphragm pumps -.AEN7 variable speed. As explained earlier, the eX system 127 three-component catalyst entered the reactor cycle through an injector and the static mixer on the suction side of the twin screw pump. The feedstock feed stream was also fed into the reactor cycle through an injector and a static mixer downstream of the catalyst injection point but upstream of the double screw suction pump. The polymerization was stopped with the addition of a catalyst scavenger (water mixed with solvent) in the product line of the reactor after the Micro-Motion flow meter measured the solution density. A static mixer in the line provided dispersion of the catalyst scavenger and additives in the stream of the reactor effluent. This current soon entered the post-reactor heaters that provided additional energy for the immediate removal of the solvent.

This immediate vaporization occurred as the effluent excited the post-reactor heater and the pressure dropped from 3,275 kPa to 450 millimeters of mercury (60 kPa) of absolute pressure in the reactor pressure control valve. This vaporized polymer entered the first of the two devolatilizers with warm oil jacket. The vaporized volatiles from the first devolatilizer were condensed with a glycol jacket exchanger, passed through the suction of a vacuum pump, and 128 were discharged into the solvent and styrene / ethylene separation vessel. The solvent and styrene were removed from the bottom of the container as a recycling solvent while the ethylene was capped at the top. The ethylene stream was cooled with a Micro-Motion mass flow meter. The measurement of the ventilated ethylene plus a calculation of the gases dissolved in the solvent / styrene stream was used to calculate the ethylene conversion. The polymer and the remaining solvent separated in the devolatilizer were pumped with a gear pump to a second devolatilizer. - The pressure in the second devolatilizer was operated at 5 milligrams of mercury (0.7 kPa) of absolute pressure to vaporize the remaining solvent. This solvent was condensed in a glycol heat exchanger, pumped through another vacuum pump, and exported to a waste tank for disposal. The dry polymer (less than 1000 ppm of total volatiles) was pumped with a gear pump to an underwater granulator with a 6-hole die, granulated, dried by cyclone, and collected in boxes of 1000 pounds. The various catalysts, cocatalysts and process conditions used to prepare ESI 26-31 are summarized in Table 5 and their properties are summarized in Table 6. 129 a Catalyst A is (lH-oyolopenta [l] phenanthrene-2-yl) dimethyl (t-butylamido) -silaniotitanium 1,4-diphenylbutadiene. b The cocatalyst B is tetrakis (pentafluorophenyl) borate bis (tallow alkyl hydrogenated) methyl ammonium. c. A commercially modified methylaluminoxane available from Akzo Nobel as MMAO-3A (CAS # 146905-79-51) d. Co-catalyst D is tris (pentafluorophenyl) borane, (CAS # 001109-15-5) 130 Dow Styron® 668 Dow Styron® 66O is a polystyrene which has the trade name and is available from the Dow Chemical Company (Midland, MI). HDPE 42047 HDPE 42047 is a high density polyethylene having a melt index (I2) of 42.0 available from the Dow Chemical Company (Midland, MI). fPVC ~~ Flexible PVC (fPVC) is a flexible molding grade PVC having a Shore A hardness of 90 which has the trade name Polychems ™ CZF-90 and is available from Polytrade Chemicals Co. Ltd (China). Effect of temperature on the elastic modulus of 131 substantially random interpolymers A sample of ESI # 1, 7, 8, and 9 were injection molded and their elastic modulus was determined as a function of temperature using a low Instron tensile tester the ASTM D-638 method at different temperatures. These data are summarized in Table 7. Table 7. Elastic modulus against temperature ESI samples 132 These data demonstrate the rapid change in the module as the temperature increases over the glass transition temperature of the polymer which is characteristic of shape memory polymers. Effect of temperature on the elongation of substantially random interpolymers A sample of ESI 1 having a styrene content of 42 mole percent (73 weight percent) and a melt index (I2) of 1.8 grams / 10 minutes is injected by molding and its porcentage elongation as a function of temperature was determined using an Instron tensile tester under the ASTM D-638 method. These data are summarized in Table 8. Table 8. Alarm against temperature of ESI samples These data show a rapid increase in percentage elongation as the temperature increases above the glass transition temperature which is characteristic of shape memory polymers. Effect of the styrene content on the glass transition temperature of the substantially random ethylene / styrene interpolymers. _ ^ a. The glass transition temperature gives a series 133 of ESI samples that have similar molecular weight (G # about 1.0) and variant styrene content are summarized in Table 9. Table 9. Tg against styrene content of ethylene / styrene interpolymers substantially random * a mixture of 50/50 by weight of the individual interpolymers. These data in Table 9 demonstrate the. increase in the transition temperature to glass according to the styrene content - of substantially random ethylene / styrene interpolymers increase. Effect of molecular weight on the glass transition temperature of the random ethylene / styrene interpolymers The glass transition temperature of a series of substantially linear ethylene / styrene interpolymers having similar styrene content and a molecular weight 134 and the like Molecular weight (as measured by the Gottfert melt index) is shown in Table 10 - Table 10. Tg against Gottfert I2 of substantially random ethylene / styrene interpolymers These data in Table 10 demonstrate the increase in glass transition temperature of the polymer as the molecular weight of substantially random ethylene / styrene interpolymers having the desired shape memory property increases. Effect of added viscosities on the glass transition temperature and modulus of substantially random ethylene / styrene interpolymers The viscosifiers were evaluated in the study, as well as the properties obtained from the commercial literature, are presented in the following Table 11: Table 11. Summary of viscosity properties used in the present invention __ _ ^ _ __ ^ _ __ ___ 135 A series of mixtures of ESI 25 having a styrene content of 42 mole percent (73 weight percent) and a Gottfert melt index of 1.8 gram / cm3 was prepared in a Haake torque rheometer with 10 percent by weight of various viscosities are listed in Table 12. Table 12. Effect of 10 weight percent of various viscosifiers on the Tg of ESI # 25 (42 mole percent styrene, Gottfert = 1.8 bouquet / cm3, T = 23. ° C) 136 The data in Table 12 demonstrate that the glass transition temperature of substantially random ethylene / styrene interpolymers having the desired shape memory property increases with the addition of the disks previously used in the present invention ^ Proof of ownership of shape memory on molded structures. 1. Injection molding the sample and the comparative resins in a 150-ton Mag injection molding machine at 190 ° C melting temperature, injection time 1 second, water temperature 21 ° C, overall cycle time 60 seconds . 2. The mold shall be a test mold .ASTM that includes specimens of ASTM flexure modulus test of 0.5 inches by 5 inches by 75 thousand. 3. Fill a 9 x 12 x 2 inch pan with tap water, place on the hot plate, heat and keep the water at 49 ° C. This is known as hot water temperature. 4. Fill a second 9 x 12 x 2 inch pan with half the water in the tap and half the ice. This will be maintained at 1 ° C and will be known as the cold water temperature. 5. Under ASTM conditions of 22 ° C and 50 percent relative humidity, measure the specimen bending modulus of 137 molded test or injection using an Instron tension meter following ASTM D790. Register as environmental module (AM). 6. Take the same sample and immerse it in ice water for 60 seconds. Remove it and quickly test the flex module. Register as a cold module (CM). 7. Take the same sample and place it in hot water for 60 seconds. Remove it and quickly test the flex module. Register this as a hot module (HM). 8. Take the sample after measuring the module and put it back in hot water for 60 seconds, then remove it and bend the specimen for the length of 5 inches end to end and prick the ends together with a fastener. Place this in the hot water for 60 seconds. 9. Remove the specimen from the water, remove the. bra, and count the sample time to see how much time is required to return to 80 percent of its normal formflat Record as return time at room temperature. 10. Put the sample back in the hot water for 60 seconds, then remove it and bend the specimen for the length of 5 inches end to end and puncture the ends with a fastener. Place this in cold water 138 for 60 seconds. 11. Remove the specimen from the water, remove the fastener, and place the sample in hot water. Count the sample time to see how much time is required to return to 80 percent of your normal, flat way.

Record as return time at hot temperature. In order to exhibit the shape memory behavior the material must: a) Have a module decrease greater than 80 percent; and b The support of the new shape for more than 60 seconds at 22 ° C; and c) Have a return time to 49 ° C greater than 10 seconds. Example 1 An ESI 29 containing 45.4 mole percent styrene (75.5 weight percent) and having a melt index (I2) of 6.8 g / 10 min was subjected to the shape memory test described herein. The results are summarized in Table 13 and demonstrate the decrease of the desired modulus greater than 80 percent and the clamping of the new form by more than 60 seconds at 22 ° C, and for 38 seconds at 49 ° C. Ex emplp 2 - ESI 31 containing 47.1 mole percent styrene (76.7 weight percent) and having a melting index of 139 (I2) of 10.2 g / 10 min was subjected to the shape memory test described in I presented. The results are summarized in Table 13 and demonstrate the decrease of the desired modulus greater than 80 percent and the clamping of the new form by more than 60 seconds at 22 ° C, and for 36 seconds at 49 ° C. Example 3 ESI 27 which contains 37.6 mole percent styrene (69.1 weight percent) and has a melt index (I2) of 3.2 g / 10 min was subjected to the shape memory test described herein. The results are summarized in Table 13 and demonstrate the decrease of the desired modulus greater than 80 percent and the clamping of the new form by more than 60 seconds at 22 ° C, and for 30 seconds at 49 ° C. Comparative experiment 1. ESI 28 containing 17.9 mol percent styrene (44.7 weight percent) and having a melt index (I2) of 0.6 g / 10 min was subjected to the shape memory test described herein. The results are summarized in Table 13 and show that this sample only exhibits a module decrease of 11.09 percent and only sustains the new form for 10 seconds at 22 ° C, and at 49 ° C.

Comparative Experiment 2"_ _ a_ ESI 32 containing 11.3 mole percent styrene (32 weight percent) and having a 140 melt index (I2) of 8.2 g / 10 min was subjected to the shape memory test described herein. The results are summarized in Table 13 and show that this sample only exhibits a module decrease of 39.02 percent and only holds the new form for 10 seconds at 22 ° C, and at 49 ° C. Comparative Experiment 3 A sample of Dow Styron ® 668 was subjected to the shape memory test described herein. The results are summarized in Table 13 and show that this sample only exhibits a module decrease of 8.06 percent and only holds the new shape for 10 seconds at 22 ° C, and at 49 ° C. Comparative Experiment 4 _ A sample of Dow HDPE 40047 was subjected to the shape memory test described herein. The results are summarized in Table 13 and show that this sample only exhibits a module decrease of 59.80 percent and only sustains the new form for 10 seconds at 22 ° C, and at 49 ° C. Comparative experiment 5 .. A flexible PVC sample having an A hardness of 90 was subjected to the shape memory test described herein. The results are summarized in Table 13 and show that this sample only exhibits a module decrease of 91.90 percent and only holds the new form for 10 seconds at 22 ° C, and at 49 ° C. 142 Table 13. Results of the shape test / reform of molded structures a Module decrease = (CM-HM) / CM x 100 * For more than 60 seconds. 143 The data in Table 13 demonstrate that: 1) ESI with 37.6 mole percent (69.1 percent by weight) or more of incorporated styrene shows an impressive change in modulus when tested at 22 ° C, 49 ° C, and 34 F. In contrast, PS and PE no. 2) ESI with 37.6 mole percent (69.1 percent by weight) or more styrene incorporated, as soon as it is brought to 49 ° C, it can easily be given new shape. And the object is then subjected to initially subjected to 34 ° F and then heated, it will take and maintain the new shape for more than 60 seconds at 22 ° C, and for more than 10 seconds at 49 ° C. In contrast, the PS and the PE do not. 3) ESI with less than 37.6 percent polar (69.1 percent by weight) styrene incorporated acts as polyethylene in terms of its return time. 4) Flexible PVC shows sensitivity to module temperature, but no shape / reform behavior. Examples 4-9 The fiber of Example 4 was prepared from ESI 26, the fiber of Examples 5-6 were prepared from ESI 33, the fiber from Example 7 was prepared from ESI 25, the fiber from Example 8 was prepared from ESI 34, and the fiber from Example 9 was prepared from ESI 35 all of which were prepared using the polymerization process used 144 for ESI 7. The process conditions and catalysts used for ESI 33-35 are summarized in Table 14 and have the compositions and properties summarized in the Table. 15. Table 14. Remedy conditions for ESI # 33-35 a Catalyst A is dimethy1 [N- (1,1-dimethylethyl) -1,1-dimethyl- [(1,2,3,4,5-?) -1,5,6,7-tetrahydro- 3-phenyl-s-indacen-1- ilojsilanaminato (2-) -N] -titanium, b Catalyst B is (t-butylamido) dimethyl (tetramethylcyclopentadienyl) silane-titanium (II) 1,3-pentadiene prepared as described in U.S. Patent No. 5,556,928, Example 17, c "Cocatalyst C" is tetrakis (pentafluorophenyl) borate bis (hydrogenated tallow alkyl) methyl ammonium, d Co-catalyst D is tris (pentafluorophenyl) borane, (CAS # 145 001109-15-5), e A commercially modified methylaluminoxane available from Akzo Nobel as MMAO-3A (CAS # 146905-79-5) f The catalyst F is (lH-cyclopenta [l] phenanthrene-2-yl) dimethyl (t-butylamido) -silanetitanium 1,4-diphenylbutadiene. Fiber preparation The polymers were clogged using an extruder 2.54 centimeters in diameter which feeds a gear pump. The gear pump pushes the material through a rotating package containing a sintered flat metal filter of 40 microns (average pore size) and a 34 or 108 hole turner. The orifices have a diameter of 400 or 800 microns having both a length of soil (ie length / diameter or L / D) of 4/1. The gear pump is operated so that approximately 0.39 grams of polymer is extruded through each orifice of the spinner per minute. The melting temperature of the polymer is typically 200-240 ° C, and varies depending on the molecular weight and the styrene content of the interpolymer being spun. Generally at higher molecular weight, the higher the melting temperature. Temperate air (about 25 ° C) is used to help the melted spun fibers cool down. The tempered air is located just below the spinner and blows air through the fiber line as it is extruded. The "velocity of the tempered air 146 is sufficient to be barely felt by the hand in the area of the fiber below the spinner." The fibers are collected on a godet roller located approximately 3 meters below the spinning die and having a diameter The speed of the godet roller is adjustable, but for the experiments shown here, the godet speed varies from 200 to 3,100 revolutions per minute.The fibers were tested on an Instron tensile test device equipped with a small plastic jaw in the crossed head (the jaw weighs approximately 6 grams) and a load cell of 500 grams.The jaws are fixed 2.54 centimeters apart.The speed of the head is fixed at 12.7 centimeters / minute A single fiber is loaded into the Instron jaws for testing.The fiber is stretched at 100 percent tension (That is, another 2.54 centimeters is stretched, and tenacity is recorded.) The fiber is allowed to return to the establishment.

Original Instron (where the jaws are again 2.54 centimeters apart) and the fiber is pulled again. At the point where the fiber begins to provide tensile strength, traction is recorded and the fixed permanent percent is calculated. Thus, a fiber pulled for the second time that does not provide tensile strength (that is, pulls a load) until it has traveled 0.25 to 147 centimeters will have a fixed permanent percent of 10 percent, this is, the percent of tension in which the fiber begins to provide resistance to the stress. The numerical difference between percent permanent fixation and 100 percent is known as percent elastic recovery. In this way, a fiber that has a permanent fixation of 10 percent will have an elastic recovery of 90 percent. After recording the percentage of fixation, permanent, the fiber is pulled at a tension of 100 percent and the tenacity is recorded. The process of pulling the fiber is repeated several times, recording the percentage permanent fixation each time and also recording the 100 percent resistance toughness. Finally, the fiber pulls to its breaking point and the last tenacity and stretch of break is recorded. Forming-Reforming Fiber Test A fiber bundle of .05 millimeters in diameter is wrapped tightly around a 5/16"diameter circular rod, and held tightly by hand for 30 seconds, to bring the fibers to the body temperature (37 ° C) .The heat source (hand) is removed for 10 seconds and then the rod is removed from the coiled fibers.A acceptable fiber that is formed-reformed should maintain at least one loose-wave rosette during more 148 of 30 seconds when tested at room temperature of 25 ° C. If the glass transition temperature of the resin used to produce the fibers is significantly above room temperature, then the fibers will exhibit a very tight crimping that will Hold for more than 30 seconds (see Example 4, Table 15.) If the range of glass transition temperature overlaps the ambient temperature range, then the fiber loop will appear n Loose-wrapped spring (see Example 5, Table 15). The combination of crimped fibers provides mechanical or friction heat to straighten the fibers and the sequence can be repeated numerous times. ~~ The glass transition temperature of the ESI can be increased by the addition of a convenient viscosity as known in Example 6. This improved curl performance, but not as much as that observed in an ESI sample, clean of transition temperature to equivalent glass. It is believed to be due to the fact that clean ESI has a narrower glass transition temperature range than a formulation containing ESI mixed with viscosifying resin. Table 15 illustrates the results of the shape memory test of the fiber when it is carried out using fibers prepared from various ESI interpolymers. Acrylic and polyvinylidene chloride resins are examples of 149 materials currently in commercial use to produce wrist hair fibers that do not pass this shape memory test. Table 15. Results of fiber tests of form / reform * Hercules Endex 155 viscous resin at 20 percent by weight + The glass transition temperature mixture of the 150 mixture in parentheses. Examples 10-16 The fibers of Examples 10-16 were prepared from ESI # 36-37 prepared using the polymerization process used for ESI 7 using the conditions and process catalysts summarized in Table 16. d Co-catalyst D is tris (pentafluorophenyl) borane, (CAS # 001109-15-5), "A commercially available methylaluminoxane available in Akzo Nobel as MMAO-3A (CAS # 146905-79-5) r Catalyst F is (lH-cyclopenta [l] phenanthrene-2-yl) dimethyl (t-butylamido) -silanetitanium 1,4-diphenylbutadiene. The fibers were prepared for Examples 10-16 from formulations as summarized in Table 17. The fibers were produced from these formulations under the following conditions: 0Y 151 Fixed temperature points: 160 ° C / 230 ° C / 250 ° C / 250 ° C / 250 ° C Benchmarks of the 10 rpm and 2 lb / hr of gear pump production Tempering Off ~ / Armed 700 rpm to 0.038 - 0.508 mm. The presence of additives in the formulations caused the maximum lowering speeds that decreased by at least 300 rpm. In other words, making a sample that contains additives to an ally of 700 rpm would require that the base resin could sustain a lowering rate of lOOCTrpm. The glass transition temperature values for the formulations are also summarized in Table 17. Table 17. Fiber test results 152 * Endex® Viscosante 155 Effect of the added viscosifiers and a second mixing component on the glass transition temperature of the substantially random ethylene / ethylene interpolymers having the shape memory property Examples 17-21 Examples 17-21 are fibers prepared as for Example 10 from a mixture of ESI 25 having a styrene content of 42 mole percent (73 weight percent) and a Gottfert melt index of 1.8 gram / cm "'with viscosity Endex® and / or acrylic in relative proportions summarized in Table 18. Table 18. Effect on Endex® 155 and acrylic on Tg in mixtures with ESI # 25 (styrene 42 mole percent, The data in Table 17 and 18 show that the glass transition temperature of the substantially random ethylene / ethylene interpolymers having the desired shape memory property increases with the addition of the viscosity and the second polymer component described and used. in the present invention. Effect of added viscosities and a second mixing component on the modulus of the substantially linear ethylene / styrene interpolymers having the shape memory property Examples 22-29 Examples 22-25 are compression molding plates in Examples 26 -29 are fibers prepared as for Example 10 made from a mixture of ESI 25 having - "a styrene content of 42 mole percent (73 weight percent) and a Gottfert melt index of 1.8, g / cm3 with Endex® and / or acrylic viscosity in the relative proportions summarized in Table 19. The mixtures were prepared as for Example 20. Table 19. Effect on Endex® 155 and the acrylic on the module at 20 ° C and 33 ° C of ESI # 25 (42 mole percent of styrene, 154 The data in Table 19 demonstrate that both the ESI interpolymer and its blend with 10 weight percent acrylic and 20 percent Endex® 155 have an equivalent change in modulus above and below the glass transition temperature. Examples 30-44 A series of bicomponent fibers was prepared from ESI 38 and the following second polymer components: PP1 - a 35 MFR polypropylene available from Montell having the product designation PF 635. PET1 - a polyester available from Wellman which has the product designation Blend 9869, lot number 61418. PEI - a linear low density ethylene / octene copolymer having a melt index, I2 of 17.0 grams / 10 minutes and a density of 0.950 grams / cm'1. S7? N2- a styrene-acrylonitrile copolymer available from Dow Chemical having the product designation TYRIL® 100. The substantially random ethylene / styrene copolymer ESI 38 was prepared using the same catalyst and cocatalyst as the ESI 9 and the same polymerization procedures as the ESI 26-31 using the conditions of process of Table 20. The ESI 38 had a melt index, I_ of 0.94 grams / 10 minutes, a styrene interpolymer content of 77.42 weight percent (48.0 percent 155 molar) and an atactic polystyrene content of 7.48. percent by weight, and contained 0.24 weight percent talcum and 0.20 weight percent siloxane binder. Table 20 A series of bicomponent sheath core fibers were produced by coextruding a substantially random ethylene / styrene interpolymer (ESI-38) as the core and a second polymer as the sheath. The fibers were manufactured using two extruders with a diameter of 3.15 centimeters that fed two gear pumps each pumping at a speed of 6 cmVrev multiplied by the speed of the pump measured in rpm (given in lane 21). The "gear pumps" pushed the material through a rotating package that contained a filter and a multi-hole spinner.The temperature of the spinning head was typically between 275-300 ° C, and varied depending on the melting point and the degradation temperature of the spinning polymer components, generally the higher the polymer weight of the 156 polymers, the higher the melting temperature, tempered air (approximately 10 to 30 ° C) was used to help cool the spun fibers of molten product The tempered air was located just below the spinner and blew air perpendicularly through the length of the fibers as they were extruded.The fibers were collected in a series of godet rollers to produce the yarn. Godete was located approximately 2.5 meters below the rotator matrix and having a diameter of approximately 15.24 centimeters. The godet speeds were adjustable, but for Examples 30-44, godet speeds varied from 100 to 1000 meters / minute. The compositions and manufacturing connections for the fibers of Examples 30-44 are summarized in Table 21. All examples are round shelled core bicomponent fibers with the exception of Example 40 having a delta sheath core configuration. 157 Table 21 158 Approximately 45 meters of the resulting yarn was transferred to a denier wheel that had been weighed to determine the denier number per filament. The resulting yarn was tested on an Instron model 100 tensile testing device equipped with a jaw type 4C (INSTRON # 2714-004, 150 psi max) on the head and 100 lbs of cell load. The speed of the head was set at 130 millimeters / minute. The thread was loaded into Instron jaws for testing. The yarn was thrown until the break and the tenacity and the final breaking stretch were recorded. The results of the test are summarized in Table 22. Table 22. Properties of bicomponent fiber * + Values in parentheses represent the same edits- made after 48 hours. * The data generated from this example had too much variability to determine the value with pressure. These results demonstrated that bicomponent fibers can be prepared with improved toughness (> 0.8 gram / dn) which remains, along with other physical properties, relatively unchanged over time. In this way the choice of the pod component can be used to instill the physical properties of the fiber while the choice of the core component can be used to exert an influence on stretching and other tensile strength characteristics.

Claims (26)

161 CLAIMS

1. A structure or manufactured article having shape memory behavior comprising: A) from 1 to 100 weight percent (based on the combined weights of Components A and B) of at least one substantially random interpolymer having an I2 of 0.1 to 1,000 grams / 10 minutes and one M "/ Mn from 1.5 to 20, which comprises; (1) from 38 to 65 mole percent of polymer units derived from: (a) at least one vinyl or vinylidene aromatic monomer, or (b) at least one hindered or cycloaliphatic vinylidene or vinylidene monomer, or (c) ) a combination of at least one aromatic vinyl or vinylidene monomer and at least one hindered or cycloaliphatic vinylidene or vinylidene monomer, and (2) 35 to 62 mole percent of polymer units derived from ethylene or at least one alpha -olefin with from 3 to 20 carbon atoms or a combination thereof; and (B) from 0 to 99 weight percent (based on the combined weights of Components A and B) of at least one polymer other than Component A; and 162 (C) from 0 to 50 weight percent (based on the combined weights of Components A, B, C and D) of at least one viscosity; and (D) from 0 to 80 weight percent (based on the combined weights of Components A, B, C and D) of at least one filler. The structure or manufactured article of claim 1 wherein: (i) Component (A) is present in an amount of 10 to 100 percent by weight (based on the combined weights of Components A and B) and comprises at least one substantially random interpolymer having an I, 0.5 to 200 grams / 10 minutes and an M "/ Mn of from 1.8 to 10; comprising (1) from 45 to 55 mole percent of polymer units derived from: (a) the aromatic vinyl or vinylidene monomer represented by the following formula: Ar R1 C-Ci; wherein R1 is selected from the group of radicals consisting of hydrogen radicals and alkyls containing 3_ carbon atoms or less, and Ar is a phenyl group or a phenyl group substituted with from 1 to 5 substituents selected from group 163 consisting of halo , alkyl with 1 to 4 carbon atoms, and haloalkyl with 1 to 4 carbon atoms; or (b) the aliphatic or cycloaliphatic vinylidene or vinylidene monomer is represented by the following general formula: A1 I R1 - C = C (R2) 2 wherein A1 is a spherically bulky aliphatic or cycloaliphatic substituent of up to 20 carbon atoms, R1 is selected from the group of radicals consisting of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl; each R2 is independently selected from the group of radicals consisting of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl; or alternatively, R1 and A1 together form a ring system; or (c) a combination of at least one aromatic vinyl or vinylidene monomer and at least one hindered or aliphatic vinylidene or cycloaliphatic vinylidene, and (2) 45 to 55 mole percent of polymer units derived from ethylene, or ethylene and at least one of propylene, 4-methyl-1-pentene, butene-1, hexene-1 or octene-1; and 164 ii) Component B is present in an amount of from 0 to 90 weight percent (based on the combined weights of Components A and B) and comprises one or more of 1) a homogeneous interpolymer, 2) a heterogeneous interpolymer; 3) a thermoplastic olefin, 4) a styrenic block copolymer, 5) a styrenic copolymer, 6) an elastomer, 7) a thermoset polymer, 8) a vinyl halide polymer, or 9) a technically designed thermoplastic; and iii) the viscosity, Component C, is present in an amount of 5 to 50 weight percent (based on the combined weights of Components A, B, C, and D) and comprises wood rosin, liquid resin derivatives , cyclopentadiene derivatives, natural and synthetic terpenes, terpene-phenolic, styrene / alpha-methyl styrene resins, and aliphatic-aromatic mixed viscosity resins or any combination thereof; and iv) the filler, Component D, is present in an amount of 0 to 50 percent by weight (based on the combined weights of Components A, B, C, and D) and comprises talc, calcium carbonate, trihydrate aluminum oxide, carbon black, glass fibers, clay, feldspar, silicon oxide 165 or glass, smoked silicon oxide, aluminum oxide, magnesium oxide, magnesium hydroxide, antimony oxide, zinc oxide, sulphate barJLo, aluminum silicate, calcium silicate, titanium dioxide, glass microspheres, chalk or any combination thereof. 3. The manufactured structure or article of claim 1 wherein: (i) Component (A) is present in an amount of 50 to 100 percent by weight (based on the combined weights of Components A and B) and comprises at least one substantially random interpolymer having an I "of 0.5 to 100 grams / 10 minutes and one Mw / Mn of from 2 to 5; comprising (1) from 48 to 55 mole percent of polymer units derived from: a) this vinyl or aromatic vinylidene monomer which comprises styrene, alpha-methyl styrene, * ortho-, meta-, and para-methylstyrene , and the halogenated ring styrenes, or. b) hindered aliphatic vinyl or cycloaliphatic vinyl or vinyl or vinylidene monomer comprising 5-ethylidene-2-norbornene or 1-vinylcyclohexene, 3-vinylcyclo-. hexene, and 4-vinylcyclohexene; or 166 c) a combination of at least one aromatic vinyl or vinylidene monomer and at least one hindered or cycloaliphatic vinylidene or vinylidene monomer, and (2) 45 to 52 mole percent of polymer units derived from ethylene, or ethylene and at least one of propylene, 4-methyl-1-pentene, butene-1, hexene-1 or octene-1; or ii) Component B is present in an amount of from 0 to 50 weight percent (based on the combined weights of Components A and B) and comprises one or more than 1) a substantially linear ethylene / alpha-olefin interpolymer; 2) a heterogeneous ethylene / alpha-olefin interpolymer with 3 to 8 carbon atoms; 3) an ethylene / propylene rubber (EPM), ethylene / propylene monomer diene terpolymer (EPDM), isotactic polypropylene; 4) a styrene / styrene-butene copolymer, a styrene / ethylene-propylene copolymer, a styrene / ethylene-butene / styrene copolymer (SEBS), a styrene / ethylene-propylene / styrene copolymer (SEPS), 5) polymers of acrylonitrile-butadiene-styrene (ABS), styrene-acrylonitrile (SAN), high impact polystyrene, 6) polyisoprene, polybutadiene, natural rubbers, ethylene / propylene rubbers, ethylene / propylene diene rubbers 167 (EPDM ), styrene / butadiene rubber, thermoplastic polyurethanes, 7) epoxies, vinyl ester resins, polyurethanes, phenolic resins, 8) homopolymers or copolymers of vinyl chloride or vinylidene chloride, 9) poly (methylmethacrylate), polyester, nylon- 6, nylon-6,6, poly (acetal); poly (amide), poly (arylate), poly (carbonate), poly (butylene) and polybutylene terephthalates, polyethylene, and iii) the viscosity, Component C, is present in an amount of 10 to 40 weight percent (based on in the combined weights of Components A, B, C, and D) and comprises styrene / alpha-methyl styrene resins, and aliphatic-aromatic mixed viscosity resins or any combination thereof; and iv) the filler, Component D, is present in an amount of 0 to 20 weight percent (based on the combined weights of Components A, B, C, and D) and comprises talc, calcium carbonate, oxide trihydrate of aluminum, barium sulfate, titanium dioxide, or any combination thereof. 4. The manufactured structure or article of claim 3 wherein the Al Component is styrene, Component A2 is ethylene, Component B is 168 poly (methyl methacrylate), and Component C is a styrene / alpha-methyl styrene resin. 5. The manufactured structure or article of claim 3 wherein the Al component is styrene; and Component A2 is ethylene and at least one of propylene, 4-methyl-1-pentene, butene-1, hexene-1 or octene-1; Component B is poly (methyl methacrylate), and Component C is a styrene / alpha-methyl styrene resin. 6. The manufactured article of claim 4 in the form of wrist hair. 7. The manufactured article of claim 5 in the form of wrist hair. 8. The manufactured article of claim 4 in the form of a toy. 9. The manufactured article of claim 5 in the form of a toy. 10. A process for shaping and reshaping a structure or article made from a polymer having an original module, wherein the process comprises: I) one or more applications of a source of energy to said polymer which causes its module to decrease below its original module, II) to shape or conform said structure or article. manufactured in a prescribed position, III) remove the source of energy that caused it to assume the prescribed position in order to regain its original module; and wherein the polymer comprises: A) from 1 to 100 weight percent (based on the combined weights of Components A and B) of at least one substantially random interpolymer having an I2 of 0.1 to 1,000 grams / 10 minutes and a MYMr, from 1-5 to 20, which comprises; (1) from 38 to 65 mole percent of polymer units derived from: (a) at least one vinyl or vinylidene aromatic monomer, or (b) at least one hindered or cycloaliphatic aliphatic vinylidene vinylidene monomer, or (c) a combination of at least one aromatic vinyl or vinylidene monomer and at least one hindered or cycloaliphatic vinylidene or vinylidene monomer, and ( 2) from 35 to 62 mole percent of polymer units derived from ethylene or at least one alphaolefin with from 3 to 20 carbon atoms or a combination thereof; Y 170 (B) from 0 to 99 weight percent (based on the combined weights of Components A and B) of at least one polymer other than Component A; and (C) from 0 to 50 weight percent (based on the combined weights of Components A, B, C and D) of at least one viscosity; and (D) from 0 to 80 weight percent (based on the combined weights of Components A, B, C and D) of at least one filler. The process of claim 10 wherein: (i) Component (A) is present in an amount of 10 to 100 percent by weight (based on the combined weights of Components A and B) and comprises at least one substantially random interpolymer having an I. of 0.5 to 200 grams / 10 minutes and a MYMn of from 1.8 to 10; comprising (1) from 45 to 55 mole percent of polymer units derived from: (a) the aromatic vinyl or vinylidene monomer represented by the following formula: Ar R - C == CH1 171 wherein R1 is selected from the group of radicals consisting of hydrogens and alkyls containing 3 carbon atoms or less, and Ar is a phenyl group or a femlo group substituted with from 1 to 5 substituents selected from the group consisting of halo, alkyl having from 1 to 4 carbon atoms, and haloalkyl having from 1 to 4 carbon atoms; or (b) the aliphatic or cycloaliphatic vinylidene or vinylidene monomer is represented by the following general formula: A1 R * c = c (Ry .. wherein A1 is a spherically bulky aliphatic or cycloaliphatic substituent of up to 20 carbon atoms, R * is selected from the group of radicals consisting of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl; each R "is independently selected from the group of radicals consisting of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl, or alternatively, R1 and A1 together form a ring system, or (c) a combination of at least one aromatic vinyl or vinylidene monomer and at least one hindered or cycloaliphatic vinylidene or vinylidene monomer, and 172 (2) 45 to 55 mole percent of polymer units derived from ethylene, or ethylene and at least one of propylene, 4-methyl-1-pentene, butene-1, hexene-1 or octene-1, and ii) Component B is present in an amount of from 0 to 90 weight percent (based on the combined weights) of Components A and B) and comprises one or more than 1) a homogeneous interpolymer, 2) a heterogeneous interpolymer, 3) a thermoplastic olefin, 4) a styrenic block copolymer, 5) a styrenic copolymer, 6) an elastomer, 7) a polymer t ermoestable, 8) a vinyl halide polymer, or 9) a technically designed thermoplastic; and iii) the viscosity, Component C, is present in an amount of 5 to 50 weight percent (based on the combined weights of Components A, B, C, and D) and comprises wood rosin, liquid resin derivatives , cyclopentadiene derivatives, natural and synthetic terpenes, terpene-phenolics, styrene / alpha-methyl styrene resins, and aliphatic-aromatic mixed viscosity resins or any combination thereof; and iv) the filler, Component D, is present in an amount of 0 to 50 percent by weight (based on the combined weights of Components A, B, C, and D) and comprises talc, calcium carbonate, trihydrate aluminum oxide, carbon black, glass fibers, clay, feldspar, silicon oxide or glass, smoked silicon oxide, aluminum oxide, magnesium oxide, magnesium hydroxide, antimony oxide, zinc oxide, barium sulfate , aluminum silicate, calcium silicate, titanium dioxide, glass microspheres, chalk or any combination thereof. The process of claim 10 wherein: (i) Component (A) is present in an amount of 50 to 100 percent by weight (based on the combined weights of Components A and B) and comprises at least one substantially random interpolymer that has an I_; from 0.5 to 100 grams / 10 minutes and one Mw / Mr? from 2 to 5; comprising (1) from 48 to 55 mole percent of polymer units derived from: a) this vinyl or aromatic vinylidene monomer which comprises styrene, alpha-methyl styrene, ortho-, meta-, and para-methylstyrene, and halogenated ring styrenes, or b) hindered aliphatic vinyl or cycloaliphatic vinyl or vinyl vinylidene monomer comprising 5-ethylidene-2-norbornene or 1-vinylcyclohexene, 3-vinylcyclohexene, and 4-vinylcyclohexene; or 174 c) a combination of at least one aromatic vinylidene or vinylidene monomer and at least one hindered or cycloaliphatic vinylidene or vinylidene monomer, and (2) from 45 to 52 mole percent of polymer units derived from ethylene, or ethylene and at least one of propylene, 4-methyl-1-pentene, butene-1, hexene-1 or octene-1, or ii) Component B is present in an amount of from 0 to 50 weight percent ( based on the combined weights of Components A and B) and comprises one or more than 1) a substantially linear ethylene / alpha-olefin interpolymer, 2) a heterogeneous ethylene / alpha-olefin interpolymer with 3 to 8 carbon atoms, 3) a ethylene / propylene rubber (EPM), ethylene / propylene diene monomer terpolymer (EPDM), isotactic polypropylene, 4) a styrene / styrene-butene copolymer, a styrene / ethylene-propylene copolymer, a styrene / ethylene-copolymer butene / styrene (SEBS), a styrene / ethylene copolymer leno-propylene / styrene (SEPS), 5) polymers of acrylonitrile-butadiene-styrene (.ABS), styrene-acrylonitrile (SAN), high-impact polystyrene, 6) poly-isoprene, polybutadiene, natural rubbers, ethylene rubbers / propylene, ethylene / propylene diene rubber (EPDM), styrene / butadiene rubber, thermoplastic polyurethanes, 7) epoxies, vinyl ester resins, polyurethanes, phenolic resins, 8) vinyl chloride or chloride homopolymers or copolymers vinylidene, 9) poly (methyl methacrylate), polyester, nylon-6, nylon-6, 6, poly (acetal); poly (amide), poly (arylate), poly (carbonate), poly (butylene) and polybutylene terephthalates, polyethylene, and iii) the viscosity, Component C, is present in an amount of 10 to 40a percent by weight (based on in the combined weights of Components A, B, C, and D) and comprises styrene / alpha-methyl styrene resins, and aliphatic-aromatic mixed viscosity resins or any combination thereof; and iv) the filler, Component D, is present in an amount of 0 to 20 weight percent (based on the combined weights of Components A, B, C, and D) and comprises talc, calcium carbonate, trihydrate aluminum oxide, barium sulfate, titanium dioxide, or any combination thereof. The manufactured structure or article of claim 12 wherein the Al Component is styrene, Component A2 is ethylene, Component B is 176 poly (methyl methacrylate), and Component C is a styrene / alpha-methyl styrene resin. The manufactured structure or article of claim 12 wherein the Al component is styrene; and Component A2 is ethylene and at least one of propylene, 4-methyl-1-pentene, butene-1, hexene-1 or octene-1; Component B is poly (methyl methacrylate), and Component C is a styrene / alpha-methyl styrene resin. 15. A bicomponent fiber having shape memory behavior comprising: (I) a first component comprising from 5 to 95 weight percent (based on the combined weights of Components I and II) of (A) of 1 to 100 weight percent (based on the combined weights of Components A and B) of at least one substantially random interpolymer having an I2 of 0.1 to 1,000 grams / 10 minutes and one Mw / Mn of from 1.5 to 20, which comprises; (1) from 38 to 65 mole percent of polymer units derived from: (a) at least one aromatic vinyl or vinylidene monomer, or (b) at least one hindered or cycloaliphatic vinylidene or vinylidene monomer, or 177 ( c) a combination of at least one aromatic vinyl or vinylidene monomer and at least one hindered or cycloaliphatic vinylidene or vinylidene monomer, and ~ (2) from 35 to 62 mole percent of polymer units derived from ethylene or at least an alpha-olefin with 3 'to 20 carbon atoms or a combination thereof; and (B) from 0 to 99 weight percent (based on the combined weights of Components A and B) of at least one polymer other than Component A; and (C) from 0 to 50 weight percent (based on the combined weights of Components A, B, C and D) of at least one viscosity; and (D) from 0 to 80 weight percent (based on the combined weights of Components A, B, C and D) of at least one filler. II) a second component, present in an amount of from 5 to 95 weight percent (based on the combined weights of Components I and II) which comprises one or more of: A) a homopolymer or interpolymer of ethylene or alpha-olefin;178 B) an ethylene / propylene rubber (EPM), ethylene / propylene monomer diene terpolymer (EPDM), isotactic polypropylene; C) a styrene / styrene-butene copolymer, a styrene / ethylene-propylene copolymer, a styrene / ethylene-butene / styrene copolymer (SEBS), a styrene / ethylene-propylene / styrene copolymer (SEPS), D) polymers of acrylonitrile-butadiene-styrene (.ABS), styrene-acrylonitrile (SAN), high impact polystyrene, E) polyisoprene, polybutadiene, natural rubbers, ethylene / propylene rubbers, ethylene / propylene diene rubbers (EPDM), styrene / butadiene rubber, thermoplastic polyurethanes, F) epoxies, vinyl ester resins, polyurethanes, phenolic resins, G) homopolymers or copolymers of vinyl chloride or vinylidene chloride, H) poly (methyl methacrylate), polyester, nylon-6, nylon-6,6, poly (acetal); poly (amide), poly (arylate), poly (carbonate), poly (butylene) and polybutylene terephthalates, polyethylene. 16. The bicomponent fiber of claim 15 is of the sheath / core type, pie slice type, side by side or "islands on the sea" type; and where: 179 (i) the first Component I comprises from 25 to 95 weight percent (based on the combined weights of Components I and II); (ii) Component (A) is present in an amount of 10 to 100 weight percent (based on the combined weights of Components A and B) and comprises at least one substantially random interpolymer having an I2 of 0.5 to 200 grams / 10 minutes and one M "/ Mn from 1.8 to 10; comprising (1) from 45 to 55 mole percent of polymer units derived from: (a) the aromatic vinyl or vinylidene monomer represented by the following formula: Ar R1 C == CH, wherein R1 is selected from the group of radicals consisting of hydrogen radicals and alkyls containing 3 carbon atoms or less, and Ar is a phenyl group or a phenyl group substituted with from 1 to 5 substituents selected from the group consisting of halo, alkyl having from 1 to 4 carbon atoms, and haloalkyl having from 1 to 4 carbon atoms; or (b) the aliphatic or cycloaliphatic vinylidene or vinylidene monomer is represented by the following general formula: A1 R1 C == C (R2) 2 wherein A1 is a spherically bulky aliphatic or cycloaliphatic substituent of up to 20 carbon atoms, R1 is selected from the group of radicals consisting of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl; each R2 is independently selected from the group of radicals consisting of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl; or alternatively, R1 and A1 together form a ring system; or (c) a combination of at least one aromatic vinyl or vinylidene monomer and at least one hindered or aliphatic vinylidene or cycloaliphatic vinylidene monomer, and (2) from 45 to 55 mole percent of polymer units derived from ethylene, or ethylene and at least one of propylene, 4-methyl-1-pentene, butene-1, hexene-1 or octene-1; and iii) Component B is present in an amount of from 0 to 90 weight percent (based on the combined weights of Components A and B) and comprises one or more than 1) a homogeneous interpolymer, -2) an interpolymer heterogeneous; 3) a thermoplastic olefin, 1S1 4) a styrenic block copolymer, 5) a styrenic copolymer, 6) an elastomer, 7) a thermoset polymer, 8) a vinyl halide polymer, or 9) a technically designed thermoplastic; and iv) the viscosity, Component C, is present in an amount of 5 to 50 weight percent (based on the combined weights of Components A, B, C, and D) and comprises wood rosin, liquid resin derivatives , cyclopentadiene derivatives, natural and synthetic terpenes, terpene-phenolic, styrene / alpha-methyl styrene resins, and aliphatic-aromatic mixed viscosity resins or any combination thereof; and v) the filler, Component D, is present in an amount of 0 to 50 percent by weight (based on the combined weights of Components A, B, C, and D) and comprises talc, calcium carbonate, oxide trihydrate Aluminum, carbon black, glass fibers, clay, feldspar, silicon oxide. or glass, smoked silicon oxide, aluminum oxide, magnesium oxide, magnesium hydroxide, antimony oxide, zinc oxide, barium sulfate, aluminum silicate, broth silicate, titanium dioxide, glass microspheres, chalk or any combination thereof; and 182 (vi) the second component II, is present in an amount of from 5 to 75 weight percent (based on the combined weights of Components I and II) which comprises one or more of: A) a homopolymer or ethylene or alpha-olefin interpolymer; B) an ethylene / propylene rubber (EPM), ethylene / propylene monomer diene terpolymer (EPDM), isotactic polypropylene; C) a styrene / styrene-butene copolymer, a styrene / ethylene-propylene copolymer, a styrene / ethylene-butene / styrene copolymer (SEBS), a styrene / ethylene-propylene / styrene copolymer (SEPS), D) polymers of acrylonitrile-butadiene-styrene (ABS), styrene-acrylonitrile (SAN), high-impact polystyrene, E) epoxies, vinyl ester resins, polyurethanes, phenolic resins, F) poly (methyl methacrylate), polyester, nylon-6 , nylon-6, 6, poly (acetal); poly (amide), poly (arylate), poly (carbonate), poly (butylene) and polybutylene terephthalates, polyethylene. 17. The bicomponent fiber of claim 16 wherein: 183 (i) the first Component I comprises 50 to 95 weight percent (based on the combined weights of Components I and II); (ii) Component (A) is present in an amount of 50 to 100 percent by weight (based on the combined weights of Components A and B) and comprises at least one substantially random interpolymer having an I., of 0.5 at 100 grams / 10 minutes and one Mw / Mn from 2 to 5; comprising _ (I) from 48 to 55 mole percent of polymer units derived from: a) this vinyl or -vinylidene aromatic monomer which comprises styrene, alpha-methyl styrene, ortho-, meta-, and para-methylstyrene , and halogenated ring styrene, or b) hindered aliphatic vinyl or cycloaliphatic vinyl or vinyl or vinylidene monomer comprising 5-ethylidene-2-norbornene or 1-vinylcyclohexene, 3-v.inylcyclo-. hexene, and 4-vinylcyclohexene; or c) a combination of at least one aromatic vinyl or vinylidene monomer and at least one hindered or cycloaliphatic vinylidene or vinylidene monomer, and (2) 45 to 52 mole percent of polymer units derived from ethylene, or ethylene and at least one of propylene, 4-methyl-1-pentene, butene-1, hexene-1 or octene-1; or 184 iii) Component B is present in an amount of from 0 to 50 weight percent (based on the combined weights of Components A and B) and comprises one or more than 1) a substantially linear ethylene / alpha-olefin interpolymer; 2) a heterogeneous ethylene / alpha-olefin interpolymer with 3 to 8 carbon atoms; 3) an ethylene / propylene rubber (EPM), ethylene / propylene monomer diene terpolymer (EPDM), isotactic polypropylene; 4) a styrene / styrene-butene copolymer, a styrene / ethylene-propylene copolymer, a styrene / ethylene-butene / styrene copolymer (SEBS), a styrene / ethylene-propylene / styrene copolymer (SEPS), 5) polymers of acrylonitrile-butadiene-styrene (ABS), styrene-acrylonitrile (SAN), high impact polystyrene, 6) polyisoprene, polybutadiene, natural rubbers, ethylene / propylene rubbers, ethylene / propylene diene rubbers (EPDM) , styrene / butadiene rubber, thermoplastic polyurethanes, 7) epoxies, vinyl ester resins, polyurethanes, phenolic resins, 8) vinyl chloride-or vinylidene chloride homopolymers or copolymers, 185 9) poly (methylmethacrylate), polyester, nylon-6, nylon-6, 6, poly (acetal); poly (amide), poly (arylate), poly (carbonate), poly (butylene) and polybutylene terephthalates, polyethylene, and iv) the viscosity, Component C, is present in an amount of 10 to 40 weight percent (based on in the combined weights of Components A, B, C, and D) and comprises styrene / alpha-methyl styrene resins, and aliphatic-aromatic mixed viscosifying resins or any combination thereof; and v) the filler, Component D, is present in an amount of 0 to 20 weight percent (based on the combined weights of Components A, B, C, and D) and comprises talc, calcium carbonate, oxide trihydrate of aluminum, barium sulfate, titanium dioxide, or any combination thereof. (vi) the second component, II, is present in an amount of from 5 to 50 weight percent (based on the combined weights of Components I and II) which comprises one or more of: A) a homopolymer or interpolymer of ethylene or alpha-olefin; B) a styrene / styrene-butene copolymer, a styrene / ethylene-propylene copolymer, a styrene / ethylene-butene / styrene copolymer (SEBS), a styrene / ethylene-propylene / styrene copolymer (SEPS), or a high impact polystyrene, C) poly (methyl methacrylate), polyester, nylon-6, nylon-6,6, poly (acetal); poly (amide), poly (arylate), poly (carbonate), poly (butylene) and polybutylene terephthalates, polyethylene. 18. The bicomponent fiber of claim 17 wherein the fiber is of the core / sheath type and wherein the Component I is the core and the Component II is the sheath and wherein the Al Component is styrene; and Component A2 is ethylene; Component B is not present and Component II is polypropylene, polyethylene, and a copolymer of ethylene / octene, polyethylene terephthalate, polystyrene, nylon-6, nylon-6, 6, or combinations thereof. 19. The bicomponent fiber of claim 17 wherein the fiber is of the core / sheath type and wherein the Component I is the core and the Component II is the sheath and wherein the Al Component is styrene; and Component A2 is ethylene and at least one of propylene, 4-methyl-1-pentene, butene-1, hexene-1 or octene-1; Component B is not present and Component II is polypropylene, polyethylene, and a copolymer of ethylene / octene, polyethylene terephthalate, polystyrene, nylon-6, nylon-6, 6, or combinations thereof. 187 20. A fabric comprising the fiber of claim 15. The fabric of claim 20 comprising a woven fabric. 2

2. The fabric of claim 20, comprising a non-woven fabric. 2

3. A fabricated article prepared from the fiber of claim 15, comprising rugs, doll's hair, a wig, a tampon, a diaper, athletic items, wrinkle-free clothing that conforms to the shape, upholstery, bandages, and sterilizable non-woven articles with gamma rays. 2

4. A plurality of the fibers of claim 15 in the form of doll's hair. 2

5. A plurality of the fibers of claim 18 in the form of doll's hair. 2

6. A plurality of fibers of claim 19 in the form of wrist hair.