MXPA00011905A - Method of making washable, dryable elastic articles - Google Patents

Abstract

The present invention relates to a method of making improved polyolefinic elastic articles from cured, irradiated or cross-linked amorphous ethylene interpolymers. In particular, the invention relates to a methodof making a shaped article (for example, film or fiber) characterized by improved elevated temperature elasticity as well as washability and dryability. The inventive elastic article comprises a substantially cured, irradiated, cross-linked (or curable, irradiated or cross-linkable) homogeneously branched ethylene interpolymer characterized as having a density less than 0.90 g/cm3 and containing at least one nitrogen-containing stabilizer. The improved elastic article of the present invention is particularly suitable for use in applications where good elasticity must be maintained at elevated temperatures and after laundering such as, for example, elastic waist bands of undergarments and other clothing.

Description

METHOD FOR MAKING LAVATORY, SECABLE ELASTIC ITEMS DESCRIPTION OF THE INVENTION The present invention relates to a method of making improved polyolefin elastic articles from amorphous, irradiated, or crosslinked ethylene interpolymers. In particular, the invention relates to a method for making a shaped article (eg, film or fiber) characterized by improved elasticity at elevated temperature as well as washing ability and drying capacity. The elastic article of the invention comprises a substantially cured, irradiated or interlaced (or irradiatable or crosslinkable curable) ethylene interpolymer homogeneously branched, which has a density less than 0.90 g / cm2 and contains at least one nitrogen-containing stabilizer. The improved elastic article of the present invention is particularly suitable for use in applications where good elasticity must be maintained at high temperatures and after washing, such as, for example, elastic waistbands of underwear and other types of garments. . Materials with excellent stretchability and elasticity are necessary to manufacture a variety of disposable and durable items such as, for example, incontinence pads, disposable diapers, training pants, clothing, underwear, sportswear, automotive shelter, weather insulated , boards and furniture upholstery. Stretching and elasticity are performance attributes which may, for example, function to effect a fit closely conforming to the body of the wearer or the article frame. Although numerous materials are known to exhibit excellent stress-strain properties at room temperature, it is generally desirable for the elastic materials to provide a conformational or secure fit during repeated use, extensions and retractions at elevated temperatures such as at body temperatures or in car interiors during the summer months. The maintenance of hermetic tolerances through temperature cycles are also cases where high temperature elasticity is important. In addition, when an elastic material is used for clothing or articles of clothing, the material must maintain its integrity and elastic function after washing. Disposable elastic articles are typically elastic mixed materials prepared from a combination of film, fibers, polymer sheets and / or absorbent materials, as well as a combination of manufacturing technologies. Although elastic fibers can be prepared through well-known processes such as spinning, meltblowing, melt spinning and continuous filament winding techniques, film and sheet forming processes typically involve known extrusion and coextrusion techniques, for example. example, blown film, cast film, profile extrusion, injection molding, extrusion coating, and extrusion lamination. Conversely, durable resilient articles or profile articles such as, for example, automotive doors and shelter from windows, strands or waistband strips in clothing, and insulation from buildings are generally molded. Such durable articles can be made by well known molding, thermoforming and profile techniques. Typically, a material is characterized as elastic when it has a high percentage of elastic recovery (i.e., a low percentage of permanent fixation) after the application of a diverting force. Ideally, elastic materials are characterized by a combination of three independent temperature properties, that is, a low percentage of permanent fixation, a low tension or load on the deformation, and a low percentage of stress or load relaxation. That is, there must be at low to high service temperatures, (1) a low tension or load requirement to stretch the material, (2) nothing or little tension relaxation or once unloaded, the material is stretched, and (3) complete or high recovery to the original dimensions after discontinue stretching, deviation or tension. Lycra® is a trademark of Dupont Fibers for its elastic spandex fibers. The US International Trade Commission defines spandex fiber as a manufactured fiber wherein the fiber-forming substance is a synthetic long-chain polymer composed of at least 85% segmented polyurethane. The Lycra is known to exhibit temperature-independent, almost ideal, elastic properties, making it very suitable for use in garments, sportswear and swimsuits. However, a major disadvantage of Lycra is that it typically exhibits serviceability, inability to wash from poor to poor at elevated temperatures. Similar to ordinary interlaced polyolefin-based elastic materials, Lycra articles tend to lose their integrity and shape and elastic properties when subjected to elevated service temperatures such as during washing and drying. Another main disadvantage of the Lycra is its cost. That is, the Lycra tends to be extremely cost prohibitive for many applications. Elastic materials such as films, strips, coatings, battens and sheets comprising at least one substantially linear ethylene polymer are described in U.S. Patent No. 5,472,775 to Obijeski et al. However, the patent of E. U. A. No. 5,472,775 does not describe the operation of these materials at elevated temperatures (ie, at temperatures above room temperature), nor their operation after washing. WO 94/25647 describes fibers and elastic fabrics made from substantially linear, homogeneously branched ethylene polymers. The fibers are said to possess at least 50% recovery (ie, less than or equal to 50% permanent fixation) at 100% tension. However, there is no disclosure in WO 94/25647 regarding the elasticity of these fibers at elevated temperatures or the washing effects on these fibers. WO 95/29197 discloses a curable ethylene polymer, substantially grafted with silane, which is useful in wire and cable coatings, climate insulation and fibers. In the examples, samples of the invention include fibers comprising an ethylene polymer substantially grafted with siia having densities of 0.868 g / cm3 and 0.870 g / cm3. Examples of the invention show to exhibit improved elastic recovery at elevated temperatures. However, there is no description in WO 95/29197 regarding the percentage of load relaxation stress or operation at elevated temperatures for these fibers intertwined with silane, nor is there any description with respect to the washing ability. U.S. Patent No. 5,324,576 discloses a band of elastic nonwoven microfibers of ethylene / alpha olefin copolymers intertwined by radiation, preferably having a density of less than 0.9 g / cm 3. In the examples set forth in the patent of US Pat. No. 5,324,576, ethylene polymers having polymer densities greater than or equal to 0.871 g / cm 3 are subjected to electron beam radiation. However, there is no description regarding the elastic performance of these polymers radiated at elevated temperatures, nor is there any description regarding their resistance to washing and drying. U.S. Patent No. 5,525,257 to Kurtz et al., Discloses that low irradiation levels of less than 2 megarrads of linear low density ethylene polymer catalyzed with Ziegler result in improved drawing ability and bubble stability without measurable gelation. . Nevertheless, the '257 patent does not provide any description regarding the elasticity and / or washing capacity at elevated temperatures. U.S. Patent No. 4,957,790 to Warren discloses the use of pro-rad compounds and irradiation to prepare linear heat stretchable low density polyethylene films having an increased orientation speed during manufacture. In the examples presented there, Warren uses ethylene polymers catalyzed with Ziegler having densities greater than or equal to 0.905 g / cm3. Various compounds are described in the art and / or sold commercially as stabilizers and high temperature antioxidants. However, the criteria used to distinguish these compounds as stabilizers and antioxidants typically refer to their ability to resist yellowing, entanglement and / or ill effects of irradiation (e.g., gamma irradiation for stezation purposes). In other cases, different types of stabilizers are made as equations among others or they are said to work in a comparable way. For example, it is known that hindered phenolic stabilizers (e.g., Irganox® 1010 supplied by Ciba-Geigy) can be as effective as the hindered amine stabilizers (e.g., Chimassorb® 944 supplied by Ciba-Geigy), and vice versa. In a product brochure entitled "Chimassorb 944FL: Hindered Amine Light Stabilizer Use and Handiing", printed in 1996, Ciba Geigy states that Chimassorb 9944"provides long-term thermal stability to polyolefins through a radical trapping mechanism similar to that of hindered phenols. " In addition, there is a certain belief that there is no universally effective stabilizer for polymers since the definition for stability inevitably varies with each application. In particular, there is no effective stabilizer for polyolefin elastic materials, with serviceability at high temperatures, washable. In general, it is known that stabilizers inhibit entanglement. Regarding entanglement in general, there are several descriptions regarding radiation resistant compositions (e.g. gamma and electron light beam) comprising amine stabilizers. Such descriptions typically teach relatively high levels of amine stabilizer (eg, greater than or equal to 0.34% by weight) are required when inhibition of entanglement, discoloration and other undesirable irradiation effects is desired. Other examples include stabilized disposable nonwoven fabrics (see, for example, U.S. Patent No. 5,200,443) and stabilized molding materials (e.g., syringes). The fibers resistant to gamma stezation, including amine coatings and the use of phenolic / hybrid amine stabilizers are also well known. See, for example, U.S. Patent No. 5,122,593 to Jennings et al. Stabilized polyethylene compositions with improved oxidation resistance and improved radiation efficiency are also well known. . Iring and others, in "The Effect of the Processing Steps on the Oxidative Stability of Polyethylene Tubing Crossiinked by Irradiation", Die Angew. Makromol, Chemie, Vol. 247, p. 225-238 (1997) teach that amine stabilizers are more effective in inhibiting the effects of electron beam irradiation (ie, they provide better resistance against oxidation) than hindered phenols. WO 92/19993, and U.S. Patent No. 5,283,101 disclose washable retroreflective applications comprised of a multi-component binder composition consisting of an electron beam light curable elastomer, interleaver (s), and an extender agent. optional coupling (s) and colorants, stabilizers, flame retardants and flow modifiers. The applications allegedly of the invention are said to be capable of withstanding ordinary household washing conditions as well as severe industrial washes without the loss of retroreflectivity. Illustrative examples of electron beam curable elastomers of the binder are said to be "chlorosulfonated polyethylenes., ethylene copolymers comprising at least about 70% polyethylene such as ethylene / vinyl acetate, ethylene / acrylate and ethylene / acrylic acid and poly (ethylene-co-propylene-co-diene) polymers ("EPDM") ). "Optional stabilizers are described as" thermal stabilizers and antioxidants such as hindered phenols and "light stabilizers such as hindered amines or ultraviolet stabilizers". Although there is an equation for the convenience or effectiveness of hindered phenols to hindered amines in the descriptions WO 92/19993 and U.S. Patent No. 5,283,101, no stabilizer of any kind is illustrated in the examples provided. In addition, although the application may employ polymers that are described as "highly flexible" before and after curing by electron beam, neither the selected polymers nor the same application are described as "elastic". That is, a material can be highly flexible yet not elastic as the terms "non-elastic" and "elastic" are defined below. However, the converse is not true; Elastic materials are characterized by having a high degree of flexibility (ie, a Young's modulus of less than 68.9 MPa, where a lower modulus represents greater flexibility). Although there is an abundance of technique related to elastic polymer articles, including articles comprising curable, radiated and / or entangled ethylene polymers, and an abundance in the art of stabilized compositions and articles, there is no description of a material polyolefin elastic with effective additive stabilization, wherein the stabilization does not inhibit the desirable effects of irradiation and / or entanglement (designed to impart high temperature elasticity and an increased melting point), and still exhibit the loss of elastic integration (i.e. cleavage or separation) when the material is subjected to washing with detergent and drying at elevated temperatures. In addition, in another product brochure entitled "Stabilization of Adhesives and Their Components", p. 8-9 (1994), Ciba-Geigy, a major stabilizer supplier, states that the cleavage or separation occurring in elastomeric materials (e.g., styrene-isoprene-styrene block copolymers) at elevated temperatures above 70 ° C is not easily controlled through the use of antioxidants. As such, there is a great need for stable, cost-effective elastic articles that have good stability at elevated temperatures as well as good washing capacity and drying capacity. That is, there is a need for elastic articles that retain their shapes under tension at elevated temperatures (eg, greater than or equal to 125 ° C. There is also a need for a method for making elastic articles having good elasticity at elevated temperatures and good washing / drying stability It has been found that these and other objects can be completely satisfied by the present invention.

COMPENDIUM OF THE INVENTION It has been found that elastic articles comprising curable, irradiated and / or crosslinkable ethylene interpolymers characterized by a polymer density of less than 0.90 g / cm3 at 23 ° C and at least one nitrogen-containing stabilizer exhibits excellent stability at room temperature. and at elevated temperatures as well as excellent washing and drying stability. According to a broad aspect of the invention, there is provided a method for making a curable, irradiated or interlaced shaped article comprising at least one homogenously branched ethylene interpolymer, which comprises ethylene interpoiomerized with at least one other monomer and characterized by having (before being configured, grafted, cured, irradiated or interlaced) a polymer density of less than 0.90 g / cm3 at 23 ° C and at least one nitrogen-containing stabilizer. Another aspect of the invention is a method for making a shaped and cured, irradiated or interlaced article, comprising at least one homogenously branched ethylene interpolymer, which comprises ethylene interpolymerized with at least one monomer and characterized by having (before be configured, grafted, cured, irradiated or interlaced) a polymer density of less than 0.90 g / cm3 at 23 ° C, and at least one nitrogen-containing stabilizer. A third aspect of the invention is a method for making an elastic article comprising the steps of: (a) providing at least one homogenously branched ethylene interpolymer having a density less than 0.90 g / cm3 at 23 ° C, thus having less 0.1% by weight of at least one nitrogen-containing stabilizer therein, (b) making or configuring the article from the interpolymer, and (c) after manufacturing or shaping subjecting the article to heat and / or radiation. ionization, where the article is characterized by having: (i) a percentage of permanent fixation less than or equal to 23 ° C and 200% tension when measured at a thickness of 102 mm using an Instron tensiometer after being configured and cured, irradiated or interlaced, (ii) a percentage of tension relaxation better than or equal to 23 ° C and 200% tension when measured at a thickness of 102 mm using an instron tensometer after being set and cured, irradiated or interlaced, and (iii) a percentage of tension relaxation less than or equal to 55 at 38 ° C and 200% tension when measured at a thickness of 102 mm using an Instron tensometer afterwards. A fourth aspect of the invention is a method for making an elastic article, wherein the steps further comprise incorporating a pro-rad interlacing additive into the interpolymer. A fifth aspect of the invention is a method for making a curable elastic article, comprising the steps of: (a) providing at least one homogenously branched ethylene interpolymer which is characterized as having a density at 23 ° C less than 0.90 g / cm3 and comprising at least 0.1% by weight of at least one nitrogen-containing stabilizer incorporated therein, (b) preparing a melt bath in the stabilized polymer of (a); (c) mixing the melting bath of (b) from 0.5 to 5 phr of a silane interleaver (silane interlayer parts per 100 parts of interpolymer), while the interlayer is at an ambient temperature of between 0 and 30 ° C; and (d) subjecting the molten mixture of (c) to ionization energy or contacting the melting mixture of (c) with at least one free radical initiator to graft at least 50%, based on the total weight of the interlayer and the interpoiimer, from the silane crosslinker to the stabilized interpolymer. Preferably, the article is fabricated using an extrusion technique (ie, the method consists of melting the polymer) such as, for example, a fiber melt spin, blown under fiber melt, blown film, cast film , injection molding, or rotomoulding technique, and allowed to cool or extinguish at room temperature (i.e., allowed to solidify substantially) prior to application or exposures to (additional) heat, ionization radiation and / or humidity .

In a preferred embodiment of the invention, at least the homogeneously branched ethylene interpolymer is a substantially linear ethylene interpolymer. In another preferred embodiment, the ionization radiation is provided by electron beam irradiation. In a third preferred embodiment, at least one nitrogen-containing stabilizer is a hydroquinoline, diphenylamine or substituted piperidine. It has been discovered that there is a subgroup of ethylene polymers, which provide completely unexpected elastic performance results when cured, irradiated and / or interlaced. In particular, it was found that for a broad scale of polymer densities, healing, radiation and / or entanglement can dramatically reduce the percentage of permanent fixation performance (i.e., improve elasticity or elastic recovery) and has no substantial effect on the percentage of environmental stress or load relaxation operation. However, although they tend to adversely affect (i.e., increase) or have no effect on the percentage of stress or load relaxation at elevated temperatures for the polymer having densities equal to or greater than 0.865 g / cm 3, surprisingly the cure, radiation and entanglement reduce (i.e., improve) the percentage of high temperature stress or charge relaxation operation of the ethylene interpolymer having a polymer density of less than 0.865 g / cm3 or a DSC crystallinity at 23 ° C lower that 8.5% ep weight. That is, curing, radiation and / or interlacing is an effective means for providing elastic materials and articles, characterized by having excellent stress relaxation characteristics at elevated temperature. Not only is the response dramatically different from irradiation or entanglement surprisingly by itself, these results are surprising for other reasons as well. For example, these articles are surprisingly and unexpectedly because at a density less than 0.90 g / cm 3, the ethylene interpolymers are already substantially amorphous. That is, a crossing or transition in elastic functioning attributable to curing, irradiation and / or entanglement can ordinarily be expected to be related to the amorphous aspect of the polymer; however, in accordance with the hexane extraction data at 50 ° C, determined in accordance with the Food and Drug Administration (FDA) test method in accordance with 21 37 C. F. R. § 177. 1520 (d) (3) (ii), the ethylene polymers are substantially amorphous at a density of 0.89 g / cm 3 and below. Given such small differences in the amorphous or crystalline aspect, dramatic elastic differences in response to irradiation or entanglement simply can not be ordinarily expected. As another surprise, it has been found that the incorporation of at least one nitrogen-containing stabilizer imparts excellent washing characteristics to the elastic article. This discovery is surprising and unexpected since the stabilizer does not inhibit or interfere with effective healing, radiation effects, entanglement or interlacing effects (and as such allows the substantial melting point to increase, i.e., from minus 75 ° C to more of 125 ° C, still inhibits melting and flow (ie, cleavage or separation) from occurring at substantially elevated temperatures, eg, 133 ° C) in an extended wash / dry test. The operation of washing and drying results from the article of the article of the invention and is also surprising for at least one reason. That is, the effectiveness of at least one nitrogen-containing stabilizer is unexpected since in ordinary stabilization tests (eg, inhibition of yellowing) the nitrogen-containing stabilizers work in a manner comparable to phenolic stabilizers., even more the phenolic stabilizers do not inhibit the fusion or the flow in the washing / drying test. Figure 1 is a graph of the percentage of voltage relaxation at 23 ° C against electron beam radiation megarrads for the examples of the invention 1 and 2 and Comparative Examples 3, 4 and 5. Figure 2 is a graph of the percentage permanent fixation at 23 ° C against electron beam radiation megarrads for the Examples of the invention 1 and 2, and examples, native 3, 4 and 5.

Figure 3 is a plot of voltage relaxation percentage at 38 ° C against electron beam radiation megarrads for Example of the invention 1 and Comparative Example 4. The term "elastic" as used herein refers to to a material that has a permanent fixation less than 60%, especially less than or equal to 25% (that is, especially greater than or equal to 87.5% recovery) at 200% tension (where 200% tension is, for example, stretch an article 2.5 cm to a final dimension of 7.62 cm). The elastic materials are more than simple and highly flexible in addition to having a Young's modulus of less than 68.9 Mpa, and are defined as a low percentage of permanent fixation at 200% tension. Elastic materials are also referred to in the art as "eiastomer" and "elastomeric". The term "non-elastic" as used herein, represents the material or article that is not elastic as defined herein (ie, the material or article has a permanent fixation percentage greater than 25). The elastic materials and articles include, the same ethylene interpolymer cured, radiated and / or interlaced as well as, but not limited to, a fiber, film, strip, tape, ribbon, sheet, coating, and molding composed of the cured ethylene interpolymer, radiated and / or interlaced. The preferred elastic items are fiber and film. The term "radiated" or "irradiated" as used herein, means the ethylene polymer, the configured ethylene interpolymer or the composite article of the ethylene polymer that was subjected to at least 3 megarrads (or the equivalent of those). same) of ionization energy whether or not there is a medibie reduction in the percentage of products extracted from xylene (ie, increase in insoluble gel). That is, substantial entanglement can not result from irradiation. The terms "interlaced" and "substantially interlaced" as used herein, represent the ethylene polymer, the configured ethylene interpolymer or the composite article of the ethylene polymer, and are characterized as having xylene extractable products of less than 85%. % by weight, preferably less than or equal to 75% by weight, most preferably less than or equal to 70% by weight, wherein the xylene extractables are determined in accordance with ASTM D-2765. The terms "cured" and "substantially cured", as used herein, mean that the ethylene interpolymer, the configured ethylene interpolymer or the composite article of the ethylene interpolymer were subjected or exposed to a treatment that induces entanglement. As used herein, terms related to ethylene interpolymers comprise a grafted silane. The terms "curable" and "crosslinkable", as used herein, mean the ethylene interpolymer, the configured ethylene interpolymer or the composite article of the non-interlaced ethylene interpolymer and which has not been subjected or exposed to inducement treatment interlacing although the ethylene interpolymer, ethylene interpolymer configured or the composite article of the ethylene interpolymer comprises additives or functionality that will effect entanglement after the subjection or exposure to said treatment. The term "pro-rad additive" as used herein means a compound that is not activated during the normal manufacture or processing of the homogeneously branched ethylene interpolymer, however, may be activated by the application of temperatures (heat) substantially by above normal manufacturing or processing temperatures and / or through ionization energy to effect some gelification preferably or, preferably, substantial entanglement. The term "homorreliene," as used herein, refers to a fiber having an individual polymer region or domain and having no other region than polymer (such as two-component fibers) .The term "blown under melting" "is used herein in the conventional sense and refers to fibers formed by extruding a molten thermoplastic polymer composition through a plurality of die capillaries., thin, usually circular as strands or fused filaments to convergent high-velocity gas streams (eg, air), which function to attenuate strands or filaments to reduce their diameters.

Then, the filaments or strands are carried by the high velocity gas streams and deposited on a collection surface to form a band of randomly dispersed meltblown fibers with average diameters generally smaller than 10 microns. The term "spinning" is used in the present sense in the conventional sense and refers to fibers formed by extruding a molten thermoplastic polymer composition as filaments through a plurality of fine, usually circular capillaries of a spinner with the diameter of the extruded filaments then being rapidly reduced and then depositing the filaments on a collection surface to form a spun-spun fiber web randomly dispersed with average diameters generally of between 7 and 30 microns. The term "nonwoven" as used herein and in the conventional sense means a web or fabric having a structure of individual fibers or strands that are randomly interspersed, but not in an identifiable manner, as is the case for a web knitted. The elastic fiber of the present invention can be used to prepare non-woven fabrics as well as composition structures comprising elastic non-woven fabric in combination with non-elastic materials. The term "conjugate" refers to fibers that have been formed from at least two polymers extruded from separate extruders, but blown under melt or spun together to form a fiber. Conjugated fibers are sometimes referred to in the art as multi-component or two-component fibers. The polymers are usually different from each other, although the conjugated fibers can be monocomponent fibers. The polymers are arranged in distinct zones substantially and constantly positioned across the cross section of the conjugate fibers and extend continuously along the length of the conjugate fibers. The configuration of the conjugated fibers can be, for example, a sheath / core arrangement (where one polymer is surrounded by another), a collateral arrangement, a cake arrangement or an arrangement of "islands in the sea". Conjugated fibers are described in U.S. Patent No. 5,108,820 to Keneko et al .; U.A. Patent No. 5,336,552 to Strack et al .; and U. U. Patent No. 5,382,400 to Pike et al. The elastic fiber of the present invention may be in a conjugated configuration, for example, as a core, or sheath, or both. At least one homogenously branched ethylene interpolymer can be irradiated, cured and / or interlaced, and has a density at 23 ° C of less than 0.90 g / cm 3, preferably less than or equal to 0.865 g / cm 3, most preferably on the scale of 0.865 g / cm3, as measured in accordance with ASTM D792. At densities greater than 0.90 g / cm 3, the interpolymer is not substantially amorphous or elastic at room temperature. In addition, although at densities equal to or greater than 0.87 g / cm3, the benefits of effective stabilization, physical densities at or below 0.865 g / cm3 are preferred since the desired improvement in high-temperature elastic performance is obtained (especially at a low percentage of tension or load relaxation). Preferably, the homogeneously branched ethylene interpolymer is characterized as having a DSC crystallinity of less than or equal to 8.3% by weight, most preferably less than or equal to 85 by weight and preferably less than or equal to 6%. Preferably, the homogeneously branched ethylene interpolymer is characterized as having a melt index of less than 10 g / 10 minutes, as determined in accordance with ASTM D1238, Condition 190 ° C / 2.16 kilogram (kg). The irradiated, cured and / or interlaced article of the present invention is characterized as having a percentage of permanent fixation better than 60 to 23 ° C, preferably less than or equal to 25 to 23 ° C., preferably less than or equal to 20 and most preferably less than or equal to 15 to 23 ° C and 38 ° C, and a tension of 200% when measured at a thickness of 102 mm using an Instron tensiometer. The irradiated, cured and / or interlaced article of the present invention is characterized by having a tension relaxation percentage of less than or equal to 25 to 23 ° C and 200% of tension and less than or equal to 55, preferably less than or equal to 50, preferably less than or equal to 30% and most preferably less than or equal to 20 to 38 ° C and 200% tension when viewed at a thickness of 102 mm using an Instron tensiometer. The irradiation can be achieved through the use of high energy, ionizing electrons, ultraviolet rays, X-rays, gamma rays, alpha particles, protons and beta particles and combinations thereof. However, electron beam irradiation is preferred. The irradiation is preferably carried out at a dose of up to 70 megarrads, most preferably between 3 to 35 megarrads, and preferably between 4 to 30 megarrads. In addition, the irradiation can be conveniently carried out at room temperature, although higher and lower temperatures can be employed, for example from 0 to 60 ° C. Preferably, the irradiation is carried out from the configuration or manufacture of the article. Also, in a preferred embodiment, the homogeneously branched ethylene interpolymer with a pro-rad additive incorporated therein is irradiated with electron beam radiation of 8 to 20 megarrads. The source of electron beam light irradiation can be any suitable electron beam light source. For example, suitable electron beam light irradiation equipment is available from Energy Services, Inc., Wilmington, Mass, with capacities of at least 100 KeV and at least 5 Kw. The voltage can be adjusted to appropriate levels such as, for example, 100,000, 300,000, 1,000,000 or 2,000,000 or 3,000,000 or higher or lower. Other apparatuses for irradiating polymeric materials are also known in the art. The homogeneously branched ethylene ether can be crosslinked or cured by first grafting a silane onto its polymer base structure and then subjecting or exposing the silane-grafted ethylene interpolymer to water or atmospheric moisture. Preferably, the ethylene polymer with grafted silane is subjected to or exposed to water or atmospheric pressure after a configuration or manufacturing operation. Suitable silanes for the silane interlacing of the ethylene interpolymer include those having the formula: R1 O I II CH2 = C ~ (C ~ (CnH2n) y) xSiR3 wherein R 'is a hydrogen atom or a methyl group; x and y are 0 or 1 always when x is 1, and is 1; n is an integer from 1 to 12, inclusive, preferably from 1 to 4, and each R independently is a hydrolyzable organic group such as an alkoxy group having 1 to 12 carbon atoms (e.g., methoxy, ethoxy, butoxy) , aryloxy group (e.g., phenoxy), an araloxy group (e.g., benzyloxy), aliphatic acyloxy group having from 1 to 12 carbon atoms (e.g., formyloxy, acetyloxy, pronanoyloxy), amino or substituted amino groups (alkylamino, arylamino), or a lower alkyl group having from 1 to 6 carbon atoms inclusive, provided that no more than one of the three R groups is an alkyl.

Suitable silanes can be grafted to a suitable ethylene polymer through the use of a suitable amount of organic peroxide, either before or during a configuration or manufacturing operation. However, preferably, the silane is grafted onto the ethylene ether polymer before the configuration or manufacturing operations. In any case, the healing or entanglement reaction is present after the configuration or manufacturing operation through the reaction between the grafted silane groups and water. The water penetrating the bulky polymer either from the atmosphere or from a water bath or "sauna". The phase of the process during which the entanglements are created, is commonly referred to as a "healing phase" and the same process is commonly called "healing." Any silane that is effectively engrafted into and interlaces the ethylene interpolymer can be used in the present invention. Suitable silanes include unsaturated silanes comprising an ethylenically unsaturated hydrocarbyl group, such as a vinyl, allyl, isopropenyl, butenyl, cyclohexenyl, or α- (meth) acryloxy allyl group, and a hydrolyzable group such as, for example, a hydrocarbyloxy group. , hydrocarbonyloxy, or hydrocarbylamino. Examples of hydrolyzable groups include methoxy, ethoxy, formyloxy, acetoxy, propionyloxy, and alkyl or arylamino groups. The preferred silanes are the unsaturated alkoxysilanes, which can be grafted onto the polymer. These silanes and their method of preparation are described more fully in U.S. Patent No. 5,266,627 to Meverden, et al. Vinyl trimethoxy silane, vinyl triethoxy silane, α- (meth) acryloxy propyl trimethoxy silane and mixtures of these silanes are the preferred silane crosslinkers for use in this invention. If a filler is present (eg, calcium carbonate, talc, mica, silica (eg SiO2, clay and aluminum trihydrate), then preferably the interlayer includes vinyl triethoxy silane The amount of silane crosslinker used in the present invention it can vary widely depending on several factors such as the same siiano, processing conditions, grafting efficiency, selection of organic peroxide, the final application and similar factors, however, typically less than 0.5, and preferably less than 0.7 parts per 100 of resin (phr) are used Convenience and economy considerations are usually the two main limitations on the maximum amount of silane interleaver used, and typically the maximum amount of silane interleaver does not exceed 5, preferably does not exceed 2. As used in parts per 100 of resin or phr, "resin" represents the ethylene interpolymer. The silane elastomer is grafted to the ethylene interpolymer from any conventional method, typically in the presence of a free radical initiator, for example, peroxides and azo compounds, or through ionization reaction, etc. A suitable grafting method is described in WO 95/29197. However, for an efficient silane grafting application, organic initiators are preferred, such as any of the peroxide initiators, for example, dicumyl peroxide, di-tert-butyl peroxide, tert-butyl perbenzoate, benzoyl peroxide, eumenohydroperoxide, t-butylperoctoate, methyl ethyl ketone peroxide, , 5-dimethyl-2,5-di (t-butyl peroxy) hexane, lauryl peroxide and tert-butyl peracetate. A suitable azo compound is azobisisobutyl nitrite. The amount of initiator may vary, but typically is present in an amount of at least 0.04, preferably at least 0.06 phr. Typically, the initiator does not exceed 0.15, preferably does not exceed 0.10 phr. The silane interleaver ratio to the initiator can also vary widely, but the typical ratio of interleaver: initiators between 10: 1 to 30: 1, preferably between 18: 1 and 24: 1. Although any conventional method can be used to graft the silane interleaver to the substantially linear ethylene polymer, a preferred method is to mix the two with the initiator in the first stage of a reactor extruder, such as a Buss kneader. Graft application conditions may vary, but melting temperatures are typically between 160 and 260 ° C, preferably 190 and 230 ° C depending on the residence time and the half-life of the initiator. Healing can be promoted with an entanglement catalyst, and any catalyst that provides this function can be used. Suitable catalysts generally include organic bases, carboxylic acids and organometallic compounds and combinations thereof, including organic titanates and complexes and carboxylates of lead, cobalt, iron, nickel, zinc and tin. The representative catalyst includes, for example, but is not limited to, dibutyltin dilaurate, dioctyltin maleate, dibutyltin diacetate, dibutyltin dioctoate, stannous acetate, stannous octoate, lead naphthenate, zinc caprylate, and cobalt naphthenate. Tin carboxylate, especially dibutyl tin dilaurate and dioctyl tin maleate are particularly effective for this invention, the catalyst (or mixture of catalysts) is present in a catalytic amount, typically between 0.015 and 0.035 phr. Representative pro-rad additives include, but are not limited to, azo compounds, organic peroxides and polyfunctional vinyl or allyl compounds such as, for example, triallyl cyanurate, triallyl isocyanurate, pentaerythritol tetramethacrylate, glutaraldehyde, ethylene glycol dimethacrylate , diallyl maleate, dipropargyl maleate, dipropargyl monoalyl cyanurate, dicumyl peroxide, di-tert-butyl peroxide, t-butyl perbenzoate, benzoyl peroxide, eumeno hydroperoxide, t-butyl peroctoate, methyl ethyl peroxide ketone, 2,5-dimethyl-2,5-di (t-butyl peroxy) hexane, lauryl peroxide, tert-butyl peracetate, azobisisobutyryl nitrite and combinations thereof. Preferred pro-rad additives for use in the present invention are compounds having polyfunctional (i.e., at least 2) moieties such as C = C, C = N or C = 0.

At least one pro-rad additive can be introduced to the homogeneously branched ethylene interpolymer by any method known in the art. However, preferably, the pro-rad additive (s) is introduced through a masterbatch concentrate comprising the same base resin or a different one as the ethylene interpolymer. Preferably, the pro-rad additive concentration for the masterbatch is relatively high, eg, 25% by weight (based on the total weight of the concentrate). At least one pro-rad additive is introduced to the homogeneously branched ethylene polymer in any effective amount. Preferably, at least one amount of introduction of the pro-rad additive is from 0.001 to 5% by weight, preferably from 0.005 to 2.5% by weight and most preferably from 0.015 to 1% by weight (based on the total weight of the product). Ethylene ether copolymer). The term "polymer", as used herein, refers to a polymeric compound prepared through the polymerization of monomers, either of the same or different type. As used herein, the generic term "polymer" embraces the terms "homopolymer", "copolymer", "terpolymer", as well as "interpolymer" The term "interpolymer", as used herein, refers to polymers prepared through the polymerization of at least two different types of monomers. As used herein, the generic term "interpolymer" includes in term "copolymer" (which is usually used to refer to polymers prepared from two different monomers), as well as the term "terpolymer" (which usually used to refer to polymers prepared from three different types of monomers). The term "homogeneously branched ethylene polymer" is used herein in the conventional sense and refers to an ethylene interpolymer wherein the comonomer is randomly distributed within a given polymer molecule and wherein substantially all polymer molecules have the same molar ratio of ethylene to comonomer. The term refers to an ethylene interpoiomer that is manufactured using the so-called homogeneous catalyst systems known in the art such as the Ziegler vanadium, hafnium and zirconium catalyst systems and metallocene catalyst systems (eg, a system of constrained geometry catalyst) as described by Elston in the US patent? No. 3,645,992; Stevens et al., In the patent of E. U. A. No. 5,064,802 and EP 0 416 815 A2; Canich in the patent of E. U. A. No. 5,026,798 and patent of E. U. A. No. 5,055,438; Parikh et al. In WO 93/13143; and Kolthammer et al., in WO 94/17112. Homogeneously branched ethylene polymers for use in the present invention can also be described as having less than 15% by weight, preferably less than 10%, preferably less than 5, and most preferably 0% by weight of the polymer with a degree of branching short chain less than or equal to 10 methyls / 1000 carbons. That is, the polymer does not contain any median high density polymer fraction (eg, there is no fraction having a density equal to or greater than 0.94 g / cm 3), as determined, for example, using an elution fractionation technique. of temperature increase (TREF, according to its acronym in English) and infrared or nuclear magnetic resonance 13C (NMR) analysis. Preferably, the homogeneously branched ethylene polymer is characterized by having an essentially individual melting TREF profile / curve and essentially lacking a median high density polymer portion, as determined using an elution fractionation technique of temperature increase ( abbreviated here as "TREF"). The distribution of the composition of an ethylene interpolymer can be easily determined from the TREF as described, for example, by Wild et al., Journal of Polvmer Science, Polv Phvs. Ed .. Vol. 10, p. 441 (1982), or in patent of E. U. A. No. 4,798,081; U.A. Patent No. 5,008,204; or by L. D. Cady, "The Role of Comonomer Type and Distribution in LLDPE Product Performance," SPE Regional Technical Conference, Quaker Square Hilton, Akron, Ohio, October 1-2, p. 107-119 (1985). The distribution of the composition (monomer) of the interpolymer can also be determined using the 13 C NMR analysis according to the techniques described in the patent of E. U. A. No. ,292,845; U.A. Patent No. 4,798,081; U. A. Patent No. 5,089,321 and by J. C. Randall, Rev. Macromol. Chem. Phvs. C29, p. 201-317. In the elution fractionation analysis of analytical temperature increase (as described in U.S. Patent No. 4,798,081 and abbreviated herein as "ATREF"), the film or composition to be analyzed is dissolved in a suitable hot solvent (per example, trichlorobenzene) and allowed to crystallize in a column containing an inert support (stainless steel shot) slowly reducing the temperature. The column is equipped with both a refractive index detector and a differential viscometer (DV) detector. Then, an ATREF-DV chromatogram curve is generated by eluting the crystallized polymer sample from the column by slowly increasing the temperature of the elution solvent (trichlorobenzene). The ATREF curve is also frequently referred to as the short-chain branching distribution curve (SCBD) or composition distribution (CD), since it indicates how the comonomer (for example, octene) is finally distributed through the customized sample. that the elution temperature is reduced, the comonomer content is increased. The refractive index detector provides the short chain distribution information and the differential viscosity detector provides an estimated value of the viscosity average molecular weight. The distribution of composition and other compositional information can also be determined using fractionation of crystallization analysis such as the commercially available CRYSTAF fraction analysis package from PolymerChar, Valencia, Spain. Preferred homogeneously branched ethylene polymers (such as, but not limited to, substantially linear ethylene polymers) have an individual melting peak of between -30 and 150 ° C, as determined using differential scanning calorimetry (DSC), as opposed to the heterogeneously branched ethylene polymers polymerized with traditional Ziegler (for example, LLDPE and ULDPE or VLDPE), which have two or more melting points. The individual melting peak is determined using a differential scanning calorimeter standardized with indium and deionized water. The method involves 5-7 mg of sample sizes, a "first heating" at 180 ° C, which is maintained for 4 minutes, a cooling at 10 ° C / minute at -30 ° C, which is maintained for 3 minutes. minutes, and another heating of 10 ° C / minute at 150 ° C to provide a "second heating" flow curve against temperature, from which the melting point (s) is taken. of polymer is calculated from the area under the curve The homogeneously branched ethylene polymers for use in the invention can be either a substantially linear ethylene polymer or a substantially linear branched ethylene polymer.

The term "linear" as used herein means that the ethylene polymer has no long chain branching. That is, the polymer chains comprising the bulky linear ethylene polymer have an absence of long chain branching, as in the case of linear low density polyethylene polymers or traditional linear high density polyethylene polymers made using polymerization processes from Z? egler (e.g., U.S. Patent No. 4,076,698 (Anderson et al.)), sometimes referred to as heterogeneous polymers. The term "linear" does not refer to branched polyethylene by high volume pressure, ethylene / vinyl acetate copolymers, or ethylene / vinyl alcohol copolymers, which are known to those skilled in the art to have numerous branching long chain. The term "substantially branched linear ethylene polymer" refers to polymers having a narrow short chain branching distribution and absence of long chain branching. Such "uniformly branched" or "linear" homogeneous polymers include those made as described in the patent of E. U. A. No. 3, 645,992 (Lestón) and those made using the so-called individual site catalysts in an intermittent reactor having relatively high ethylene concentrations (as described in U.S. Patent No. 5,026,798 (Canich) or U.S. Patent No. 5,055,438 (Canich) or those made using restricted geometry catalysts in an intermittent reactor also having relatively high olefin concentrations (as described in U.S. Patent No. 5,064,802 (Stevens et al.) Or in European Patent 0416815 A2 (Stevens et al. ).) Typically, homogeneously branched linear ethylene polymers are ethylene / α-olefin interpolymers, wherein the α-olefin is at least one α-olefin of 3 to 20 carbon atoms (eg, propylene, 1-) butene, 1-pentene, 4-methyl-1-pentene, 1-hexene, 1-heptene, and 1-octene) and preferably at least the α-olefin of 3 to 20 carbon atoms is 1-butene, 1- hexene, 1-heptene or 1-octene. Most preferably, the ethylene / α-olefin ether polymer is a copolymer of ethylene and an α-olefin of 3 to 20 carbon atoms, and especially and ethylene / α-olefin copolymer of 4 to 8 carbon atoms, such as a copolymer of ethene / 1-ketene, copolymer of ethylene 1-butene, copolymer of ethylene 1-pentene or copolymer of ethylene 1-hexene. Homogeneously branched linear ethylene polymers suitable for use in the invention are sold under the designation of TAFMER by Mitsui Chemical Corporation and under the designations of EXACT and EXCEED resins by Exxon Chemical Company. The term "substantially linear ethylene polymer" as used herein means that the bulky ethylene polymer is substituted, on average, with 0.01 branches of targa chain / 1000 total carbons to 3 long chain branches / 1000 total carbons (in where, "total carbons" include both chain and branched chain carbons). Preferred polymers are substituted with 0.01 long chain branches / 1000 total carbons to a long chain branch / 1000 total carbons, most preferably 0.05 long chain branches / 1000 total carbons to a branched long chain / 1000 total carbons, and in special of 0.3 long chain branches / 1000 total carbons to a long chain branch / 1000 total carbons. As used herein, the term "base structure" refers to a discrete molecule, and the term "polymer" or "bulky polymer" refers, in the conventional sense, to the polymer as formed in the reactor. For the polymer to be a "substantially linear ethylene polymer", the polymer must have at least enough molecules with long chain branching so that the average long chain branch in the bulky polymer is at least an average of 0.01 / 1000 total carbons to 3 long chain branches / 1000 total carbons. The term "bulky polymer" as used herein, represents the polymer resulting from the polymerization process as a mixture of polymer molecules and, for substantially linear ethylene polymers, including molecules that have an absence of long chain branching as well as molecules that have long chain branching. In this way, a "bulky polymer" includes all the molecules formed during the polymerization. It is understood that, for substantially linear polymers, not all molecules have long chain branching, but a sufficient amount does have it so that the average long chain branching content of bulky polymer positively affects the melting rheology (i.e. , the shear viscosity and melt fracture properties) as described hereinbelow and elsewhere in the literature. The long chain branching (LCB) is defined herein as a chain length of at least one carbon less than the carbon number in the comonomer, while the short chain branching (SCB) is defined herein as a chain length of the same number of carbons in the comonomer residue after it is incorporated into the polymer molecule base structure. For example, a substantially linear ethylene / 1-octene polymer has base structures with long chain branches of at least 7 carbons in length, but also has long chain branches of only 6 carbons in length. The long chain branching can be distinguished from the short chain branching using 13C nuclear magnetic resonance (NMR) spectroscopy to a limited degree, for example, for ethylene homopolymers, can be quantified using a Randall method, (Rev. Macromol Chem. Phvs., C29 12 &3), p. 285-297). However, as a practical matter, 3C nuclear magnetic resonance spectroscopy can not determine the length of a long chain branch in excess of about 6 carbon atoms, and as such, this analytical technique can not distinguish between a branch of 7 carbons and a branch of 70 carbons. The long chain branching may be as long as about the same length as the length of the base structure of the polymer. Although conventional 13C nuclear magnetic resonance spectroscopy can not determine the length of a long chain branch in excess of 6 carbon atoms, there are other known techniques useful for quantifying or determining the presence of long chain branches in ethylene polymers, including ethylene / 1-ketene interpolymers. For example, U.S. Patent No. 4,500,648 teaches that the long chain branching (LCB) frequency can be represented by the equation LCB = b / Mw, where b is the average number in weight of long chain branches per molecule and Mw is the weight average molecular weight. The average molecular weight and the long chain branching characteristics are determined through gel penetration chromatography and intrinsic viscosity methods respectively. Two other useful methods for quantifying or determining the presence of long chain branches in ethylene polymers, including ethylene / 1-ketene interpolymers are gel penetration chromatography coupled with a low angle laser light diffusion detector (GPC-LALLS ) and gei penetration chromatography coupled with a differential viscosimeter detector (GPC-DV). The use of these techniques for detection of long chain branching and the underlying theories have been well documented in the literature. See, for example, Zimm, G. H. and Stockmayer, W. H., J \ _ Chem. Phvs. 17, 1301 (1949) and Rudin, A., Modern Methods of Polvmer Characterization, John Wiley & Sons, New York (1991) p. 103-112. A. Willem deGroot and P. Steve Chum, both of The Dow Chemical Company, at the October 4, 1994 conference of the Federation of Analytical Chemistry and Spectroscopy Society (FACSS) in St. Louis, Missouri, presented data demonstrating that GPC-DV is actually a useful technique to quantify the presence of branching of long chain in substantially linear ethylene polymers. In particular, deGroot and Chum found that the level of long-chain branches in substantially linear ethylene homopolymer samples measured using the Zimm-Stockmayer equation correlated well with the level of long-chain branches measured using 13C NMR. In addition, deGroot and Chum found that the presence of octene does not change the hydrodynamic volume of the polyethylene samples in solution and, as such, one can represent the molecular weight increase attributable to short chain octene branches knowing the mole percentage of octene in the sample. Through the deconvolution of the contribution to the molecular weight increase attributable to short chain branches of 1-octene, deGroot and Chum showed GPC-DV can be used to quantify the level of long chain branches in ethylene / octene polymers substantively linear. DeGroot and Chum also showed that a log plot (l2, melt index) as a record function (weight average molecular weight GPC), as determined through GPC-DV illustrates that aspects of long chain branching (but not the long branching degree) of substantially linear ethylene polymers are comparable with those of low density, highly branched, high pressure polyethylene (LDPE) and are clearly distinct from ethylene polymers produced using Ziegler type catalysts, such as titanium complexes and ordinarily homogeneous catalysts such as hafnium and vanadium complexes. For substantially linear ethylene polymers, the empirical effect of the presence of long chain branching is manifested as improved rheological properties, which are quantified and expressed in terms of gas extrusion rheometry (GER) and / or melt flow, I10 / l2, increments . The substantially linear ethylene polymers used in the present invention are a unique class of compounds further defined in U.S. Patent No. 5,272,236, Application No. 07 / 776,130, filed October 15, 1991.; U.A. Patent No. 5,278,272, Application No. 07 / 939,281, filed on September 2, 1992; and U.S. Patent No. 5,665,800, Application No. 08 / 730,766, filed October 16, 1996. Substantially linear ethylene polymers differ significantly from the class of polymers conventionally known as homogeneously branched linear ethylene polymers described above and, for example, by Leston in US Patent No. 3,645,992. As an important distinction, the substantially linear ethylene polymers do not have a linear polymer base structure in the conventional sense of the term "linear" as is the case for homogeneously branched linear ethylene polymers. The substantially linear ethylene polymers can also differ significantly from the class of polymers conventionally known as linear, polymerized Ziegler, heterogeneously branched, traditional ethylene interpolymers (e.g., ultra low density polyethylene, linear low density polyethylene, or high polyethylene). density made, for example, using the technique described by Anderson et al., in U.S. Patent No. 4,076,698), since the substantially linear ethylene interpolymers are homogeneously branched polymers. In addition, the substantially linear ethylene polymers also differ from the class of heterogeneously branched ethylene polymers, since the substantially linear ethylene polymers are characterized in that they essentially lack a high density polymer or crystalline polymer fraction, as determined using a technique of elution fractionation of temperature increase. The substantially linear, homogeneously branched ethylene polymers for use in the present invention are characterized by having: (a) a melt flow ratio, l? 0 / l2 > _5.63. (b) a molecular weight distribution, Mw / Mn, as determined by gel permeation chromatography and defined by the equation: (Mw / Mn) < (I10 / i2) - 4.63, (c) a gas extrusion rheology so that the critical shear rate at the beginning of the surface melt fracture for the substantially linear etiienic polymer is at least 50% greater than the critical shear rate at the beginning of the melt surface fracture for a linear ethylene polymer, wherein the substantially linear ethylene polymer and the linear ethylene polymer comprise the same comonomer or comonomers, the linear ethylene polymer has an L2 and Mw / Mn within 10% of the substantially linear ethylene polymer and wherein the critical shear rates of the substantially linear ethylene polymer and the linear ethylene polymer are measured at the same melting temperature using a rheometer gas extrusion, (d) an individual differential scanning calorimetry, DSC, melting peak of between -30 ° C and 150 ° C, and (e) a density m greater than or equal to 0.865 g / cm3. The determination of the critical shear rate and the critical shear stress with respect to the melt fracture as well as other rheological properties such as "rheological processing index" (Pl), is performed using a gas extrusion rheometer ( GER). The gas extrusion rheometer is described by M. Shida, R. N. Shroff and L.V. Cancio in Polvmer Engineering Science, Vol. 17, No. 11, p. 770 (1997) and in Rheometers for Molten Plastics by John Dealy, published by Van Nostrand Reinhold Co. (1982) on p. 97-99. The processing index (Pl) is measured at a temperature of 190 ° C, at a nitrogen pressure of 17.2 MPa using a L / D die of 20: 1 with a diameter of 752 micrometers (preferably, a die with a diameter 0.0363 cm for high flow polymers, for example, a melt index of 50 - 100 l2 or greater), having an entry angle of 180 °. The GER processing index is calculated in units of millipoises from the following equation: Pl = 2.15 x 106 dynes / cm2 / (1000 X shear rate). where: 2.15 x 106 dynes / cm2 is the shear stress at 17.2 Mpa, and the shear rate is the shear velocity in the wall as represented by the following equation: 32 Q '/ (60 sec / min) (0.0745) (diameter X 2.54 cm / in) 3, where: Q 'is the extrusion rate (g / min), 0.745 is the melting density of the polymer (gm / cm3), Diameter is the diameter of the capillary hole (centimeters). Pl is the apparent viscosity of a material measured at an apparent shear stress of 2.15 x 108 dynes / cm2. For substantially linear ethylene polymers, the Pl is less than or equal to 70% of that of a conventional linear ethylene polymer having one l2, Mw / Mn and each density of 10% of the substantially linear ethylene polymer. A plot of shear stress versus apparent shear rate was used to identify the melt fracture phenomenon on a nitrogen pressure scale of 36.2 to 3.4 MPa using the die or GER test apparatus previously described. According to Ramamurthy in Journal of Rheology, 30 (2) 337-357, 1986, above a certain critical flow velocity, the irregularities of the extruded product observed can be broadly classified into two main types: surface fracture by melting and fracture of raw fusion. Fracture surface fracture occurs under seemingly stable flow conditions and varies in detail from loss of specular gloss to the more severe form of "shark skin". In this description, the principle of the melt surface fracture is characterized at the beginning of the loss of brightness of the extruded product where the roughness of the surface of the extruded product can only be detected at an amplification of 40 X. The speed of effort Critical cutting at the start of the melt surface fracture for the substantially linear ethylene polymers is at least 50% greater than the critical shear rate at the beginning of the melt surface fracture of a linear ethylene polymer having approximately same l2 and M ^ / Mn. Preferably, the critical shear stress at the beginning of the melt surface fracture for the substantially linear ethylene polymers of the invention is greater than 2.8 x 106 dynes / cm2. Raw fusion fracture occurs at unstable flow conditions and varies with detail from regular distortions (alternation of stiffness and softness, helical, etc.) to random distortions. For commercial acceptability, for example, in blown film products), surface defects can be minimal, if absent. The critical shear rate at the beginning of the melt surface fracture (OSMF) and the shear stress at the beginning of the raw melt fracture (OGMF) will be used here based on the surface roughness changes and configurations of the products extruded by GER.

For the substantially linear ethylene polymers used in the invention, the critical shear stress at the beginning of the raw melt fracture is preferably greater than 4 x 106 dynes / cm2. For the processing index determination and for the determination of GER melt fracture, the substantially linear ethylene polymers are tested without inorganic fillers and have no more than 20 ppm of aluminum catalyst residue. Preferably, however, for the processing index and melt fracture tests, the substantially linear ethylene polymers do not contain antioxidants such as phenols, hindered phenols, phosphites or phosphonites, preferably a combination of a hindered phenol or phenol and a phosphite or a phosphonite.

The molecular weight distributions of ethylene polymers are determined by gel permeation chromatography (GPC) in a Waters 150C high temperature chromatographic unit equipped with a differential refractometer and three columns of mixed porosity. The columns are supplied by Poiymer Laboratories and are commonly packaged with pore sizes of 103, 104, 105 and 106 A. The solvent is 1, 2,3,4-trichlorobenzene of which 0.3% by weight of solutions of the samples are prepared for injection. The flow rate is 1.0 milliliters / minute, the operating temperature of the unit is 140 ° C and the injection size is 100 microliters. The determination of molecular weight with respect to the base structure of the polymer is deduced using narrow molecular weight distribution polyethylene standards (from Polymer Laboratories) together with their elution volumes. Equivalent polyethylene molecular weights are determined using appropriate Marck-Houwink coefficients for polyethylene and polystyrene (as described by Williams and Ward, a Journal of Polvmer Science, Polymer Letters, Vol. 6, page 621, 1968) to derive the following equation: Mpolyethylene - 3 + (M polystyrene In this equation, a = 0.4316 and b = 1.0) The weight average molecular weight, Mw, is calculated in a usual way according to the following formula: Mj = (? w, (M , ')) - Where w, is the fraction by weight of molecules with molecular weight M, eluting from the GPC column in the fraction i = j = 1 when calculating Mw and j = -1 when calculating Mn For at least one homogeneously branched ethylene polymer using the present invention, the Mw / Mn preferably is less than 3.5, preferably less than 3.0, most preferably less than 2.5, and especially in the 1.5 to 2.5 scale, and very especially on the scale of 1.8 to 2.3 The substantially linear ethylene polymers are known to have excellent processability, despite having a relatively narrow molecular weight distribution (ie, the ratio of Mw / Mn is typically less than 3.5). Surprisingly, unlike homogeneous and heterogeneously branched ethylene polymers, the melt flow ratio (10/12) of substantially linear ethylene polymers can vary essentially and independently of the molecular weight distribution, Mw / Mn. Accordingly, when good extrusion processability is desired, the preferred ethylene polymer for use in the present invention is a substantially linear, homogeneously branched ethylene interpolymer. Restricted geometry catalysts suitable for use in the manufacture of substantially linear ethylene polymers include restrained geometry catalysts as described in the U.S. Patent Application No. 07 / 545,403, filed July 3, 1990; application of E. U. A. No. 07 / 758,654, filed on September 12, 1991; U.A. Patent No. 5,532,380 (Application No. 07 / 758,654); U.A. Patent No. 5,064,802 (Application No. 07 / 547,728); U.A. Patent No. 5,470,993 (Application No. 08 / 241,523); U.A. Patent No. 5,453,410 (Application No. 08 / 108,693); U.A. Patent No. 5,374,696 (Application No. 08/08353); U.A. Patent No. 5,532,394 (Application No. 08 / 295,768); U.A. Patent No. 5,494,874 (Application No. 08 / 294,496); and U.A. Patent No. 5,189,192 (Application No. 07 / 647,111). Suitable catalyst complexes can also be prepared in accordance with the teachings of WO 93/08199, and the patents issued therefrom. In addition, the transition metal olefin polymerization catalysts, monocyclopentadienyl, taught in US Patent 5,026,798, are also believed to be suitable for use in the preparation of the polymers of the present invention, provided that the polymerization conditions are substantially uniform to those described in U.S. Patent No. 5,272,236; US Patent No. 5,278,272 and US Patent No. 5,665,800, with special attention to the requirement of continuous polymerization. Such polymerization methods are also described in PCT / US 92/08812 (filed October 15, 1992). The above catalysts can furthermore be described as comprising a metal coordination complex comprising a metal of groups 3-10 of the lanthanide series of the Periodic Table of the Elements and a de-localized β-linked portion substituted with a portion of restriction induction, said complex having a restriction geometry around the metal atom, so that the angle in the metal between the centroid of the substituted pi-attached portion, delocalised and the center of at least one remaining substituent, is lower that the angle in a similar complex containing a similar pi-linked portion lacking said restriction induction substituent, and further providing such complexes comprising more than one delocalised substituted pi-linked portion, only one thereof for each The metal atom of the complex is a pi-linked cyclic, delocalized, substituted portion. The catalyst further comprises an activation co-catalyst.

Suitable cocatalysts for use herein include polymeric or oligomeric aluminoxanes, especially methyalianuminoxane, as well as ion-forming, uncoordinated, compatible, inert compounds. The so-called modified methylaluminoxane (MMAO) is also suitable for use as a cocatalyst. A technique for preparing said modified aiuminoxane is described in the patent of US Pat. No. 5,041,584. Aluminoxanes can also be made as described in the patent of US Pat. No. 5,218,071; U.A. Patent No. 5,086,024; U.A. Patent No. 5,041,585; U.A. Patent No. 5,041,583; U.A. Patent No. 5,015,749; U.A. Patent No. 4,960,878; and U.A. Patent No. 4,544,762. Aluminoxanes, including the modified methylaluminoxane, when used in the polymerization, are preferably used so that the catalyst residue remaining in the polymer (finished) preferably ranges from 0 to 20 ppm of aluminum, especially 0 to 10 ppm of aluminum and most preferably 0 to 5 ppm of aluminum. In order to measure the properties of the bulky polymer (e.g., Pl or melt fracture), aqueous HCl was used to extract the aluminoxane from the polymer. However, the preferred cocatalysts are inert, uncoordinated boron compounds such as those described in EP 520723. Substantially linear ethylene is produced through a continuous controlled polymerization process (as opposed to an intermittent one) using at least one reactor ( for example, as described in WO 93/07187, WO 93/07188, and WO 93/07189), but may also be produced using multiple reactors (e.g., using a multiple reactor configuration as described in the US patent. No. 3,914,342) at a sufficient polymerization temperature and pressure to produce the interpolymers having the desired properties. The multiple reactors can be operated in series or in parallel, with at least one catalyst of restricted geometry employed in at least one of the reactors. Substantially linear ethylene polymers can be prepared through the polymerization of continuous solution, slurry or gas phase in the presence of a constrained geometry catalyst, such as the method described in European Patent No. 416,815-A. Polymerization can generally be performed in any reactor system known in the art, including, but not limited to, a tank reactor (s), a reactor (s), sphere (s), loop reactor (s) of recirculation, or combinations thereof, any reactor or all reactors operated partially or completely in adiabatic, non-adiabatic form or a combination of both. Preferably, a continuous loop reactor solution polymerization process is used to make the substantially linear ethylene polymer used in the present invention. In general, the continuous polymerization required to make substantially linear ethylene polymers can be achieved at conditions well known in the art for Ziegler-Natta or Kaminsky-Sinn type polymerization reactions, ie, at temperatures of 0 to 250 ° C and pressures from atmospheric to 1000 atmospheres (100 MPa). If desired, suspension process, solution, slurry, gas phase or other process conditions may be employed. A support can be used in the polymerization, but preferably the catalysts are used in a homogeneous (ie, soluble) form. Of course, it will be appreciated that the active catalyst system is formed in situ if the catalyst and its cocatalyst components are added directly to the polymerization process and a suitable solvent or diluent, including condensed monomer, is used in said polymerization process. However, it is preferred to form the active catalyst in a separate step from a suitable solvent before adding it to the polymerization mixture. The substantially linear ethylene polymers used in the present invention are ether polymers of at least one α-olefin of 3 to 20 carbon atoms and / or diolefin of 4 to 18 carbon atoms. Copolymers of ethylene and an α-olefin of 3 to 20 carbon atoms are especially preferred. The term "interpolymer" as discussed above, is used herein to mean a copolymer, a terpolymer, or any other multiple monomer polymer, wherein at least one other comonomer is polymerized with ethylene or propylene to make the interpolymer. Suitable unsaturated comonomers useful for polymerization with ethylene include, for example, ethylenically unsaturated monomers, conjugated or non-conjugated dienes, polyols, etc. Examples of such comonomers include α-olefins of 3 to 20 carbon atoms such as propylene, isobutylene, 1-butene, 1-hexene, 1-pentene, 4-methyl-1-pentene, 1-heptene, 1-octene, 1-nonene, and 1-decene. Preferred comonomers include propylene, 1-butene, 1-pentene, 1-hexene, 4-methyl-1-pentene and 1-octene, and 1-octene, with 1-octene being especially preferred. Other suitable monomers include styrene, or styrene substituted by halogen or alkyl, vinylbenzocyclobutane, 1,4-hexadiene, 1,7-octadiene and naphthenics (eg, cyclopentene, cyclohexene and cyclooctene). The homogenously branched ethylene interpolymer can be mixed with other polymers. Polymers suitable for mixing with the ethylene interpolymer are commercially available from a variety of suppliers and include, but are not limited to, an ethylene polymer (e.g., low density polyethylene, ultra low or very low density polyethylene, polyethylene medium density, linear low density polyethylene, high density polyethylene, homogenously branched linear ethylene polymer, substantially linear ethylene polymer, polystyrene, ethylene-styrene ether, ethylene-vinyl acetate interpolymer, ethylene-acid ether acrylic, ethylene-ethyl acetate ether, ethylene-methacrylic acid polymer, and ethylene-methacrylic acid ionomer), polycarbonate, polystyrene, polypropylene (e.g., polypropylene homopolymer, polypropylene copolymer, and polypropylene interpolymer) random block), thermoplastic polyurethane, polyamide, ether polymer polylactic acid, thermoplastic block polymer (for example, styrene-butadiene copolymer, styrene-styrene three-block copolymer, and styrene-ethylene-butylene-styrene tri-block copolymer), polyether block copolymer (e.g. PEBAX), copolyester polymer, polyester / polyether block polymers (eg, HYTREL), ethylene-carbon monoxide interpolymer (eg, ethylene / carbon monoxide (ECO), copolymer, ethylene terpolymer / acrylic acid / carbon monoxide (EAACO), ethylene / methacrylic acid / carbon monoxide terpolymer (EMAACO), ethylene / vinyl acetate / carbon monoxide terpolymer (EVACO) and styrene / carbon monoxide terpolymer (SCO)), terephthalate polyethylene (PET), chlorinated polyethylene, and their mixtures. In a preferred embodiment, the homogenously branched interpolymer of ethylene is mixed with a polypropylene resin, preferably an isotactic polypropylene resin such as Montell Profax 6323 and Amoco 4018. However, polypropylene polymers generally suitable for use in the invention, including random block propylene-ethylene polymers, are available from a number of manufacturers, such as, for example, Montell Poiyolefins, DSM, Amoco, Eastman, Fina and Exxon Chemical Company. At Exxon, suitable polypropylene polymers are supplied under the ESCORENE and ACHIEVE designations. Suitable polylactic acid polymers (PLA) for use in the invention are well known in the literature (for example, see DM Bigg et al., "Effect of Copolymer Ratio on the Cristallinity and Properties of Polylactic Acid Copolymers", ANTEC 196., page 2028-2039; WO 90/01521; EP 0515203A; and EP 0748846A2. Suitable polylactic acid polymers are commercially available from Cargill Dow under the designation EcoPLA. The thermoplastic polyurethanes suitable for use in the present invention are commercially available from The Dow Chemical Company under the designation PELLATHANE. Suitable polyolefin-carbon monoxide interpolymers can be manufactured using well-known high pressure free radical polymerization methods. However, they can also be manufactured using traditional Ziegler-Natta catalysts and even with the use of so-called homogeneous catalyst systems such as those described and presented herein above. Free radical initiated high pressure carbonyl ethylene polymers such as ethylene-acrylic acid interpolymers can be manufactured by any known technique including the methods taught by Thomson and Waples in US Patent No. 3,520,861 and by McKinney and others in U.S. Patent Nos. 4,988,781; 4,599,392; and 5,384,373. Ethylene-vinyl acetate interpolymers suitable for use in the invention are commercially available from various suppliers, including Exxon Chemical Company and Du Pont Chemical Company. Suitable ethylene / alkyl acrylate interpolymers are commercially available from various suppliers. Suitable ethylene / acrylic acid interpolymers are commercially available from The Dow Chemical Company under the designation PRIMACOR. Suitable ethylene / methacrylic acid polymers are commercially available from Du Pont Chemical Company under the designation NUCREL. Chlorinated polyethylene (CPE), or substantially linear, especially chlorinated ethylene polymers can be prepared through the chlorination of polyethylene according to well known techniques. Preferably, the chlorinated polyethylene comprises equal to or greater than 30% by weight of chlorine. Chlorinated polyethylenes suitable for use in the invention are commercially available from The Dow Chemical Company under the designation TYRIN. Suitable nitrogen-containing stabilizers for use in the present invention include, but are not limited to, naphthylamines (e.g., N-phenyl naphthylamines such as Naugard PAN supplied by Uniroyal); diphenylamines and their derivatives, which are also referred to as secondary aromatic amines (for example, 4,4'-bis (oc, oc-dimethylbenzyl) -diphenylamine, which is supplied by Uniroyal Chemical under the designation Naugard® 445); p-phenylenediamines (for example Wingstay® 300 supplied by Goodyear); piperidines and their derivatives (eg, N, N'-bis (2, 2, 6, 6-tetramethyl-4-piperidinyl) -1,6-hexanediamine with 2,4,6-trichloro-1,3,5- triazine and 2,4,4-trimethyl-1,2-pentanamine, which is provided by Ciba Geigy under the designation Chimassorb® 944, as well as other substituted piperidines such as Chimassorb® 119, Tinuvin® 622 and Tinuvin® 770, three also provided by Ciba-Geigy), and quinolines (for example, oxyquinolines and hydroquinolines such as polymeric 2,2,4-trimethyl-1,2-dihydroquinoline, which is provided by Vanderbilt Company under the designation of Agerite® D ). Suitable nitrogen-containing stabilizers also include hybrid stabilizers such as aminophenols (e.g., N, N'-hexamethyleneb-3 (3,5-di-tert-butyl-4-hydroxy-phenyl) -propionamide), acyl Nophenols (which are also referred to as 4-hydroanilides) and the various hybrid stabilizers described in U.S. Patent No. 5,122,593, which consists of an N-substituted 1 - (pierazin-2-one-alkyl) group on a and an acetamide (3, 5-dialkyl-4-hydroxyphenyl) -α, α-disubstituted at the other end. Other suitable nitrogen-containing stabilizers include mono- and dicarboxylic acid carboxylic acid amides and N-monosubstituted derivatives (e.g., N, N-phenyloxamide and 2,2'-oxamidobisetyl 3- (3,5-di-) -propionate. ter-butyl-4-hydroxyphenyl) which is provided by Uniroyal Chemical under the designation Naugard® XL-1); hydrazides of aliphatic and aromatic mono and dicarboxylic acids and their N-acylated derivatives; bis-acylated hydrazine derivatives; melamine; benzotriazoles; hydrazones, acylated derivatives of hydrazino-triazines, polyhydracides; salicylic ethylene oxide; salicyllaloximes; ethylenediaminetetraacetic acid derivatives; and aminotriazoles and their acylated derivatives. Preferred nitrogen-containing stabilizers for use in the present invention are diphenylamines, substituted piperidines and hydroquinolines. In addition, at least one nitrogen-containing stabilizer can be employed alone or in combination with another stabilizer or antioxidant such as, for example, but not limited to, another nitrogen-containing stabilizer as well as a hindered phenol (eg, 2.6 -di-tert-butyl-4-methylphenol which is supplied by Koopers Chemical under the designation of BHT® and tetrakis (methylene 3- (3,5-di-tert-butyl-4-hydroxyphenyl) methanpropionate) , which is supplied by Ciba-Geigy under the designation Irganox® 1010), thioester (for example, duauryl thiodipropionate which is supplied by Evans under the designation Evanstab® 12), phosphite (for example, Irgafos® 168 supplied by Ciba-Gegy Corp. and tris (nonylphenyl) phosphite, which is supplied by Uniroyal Chemical under the designation Naugard® P); diphosphite (for example, distearyl pentaerythritol diphosphite, which is supplied by Borg-Warner under the designation Weston® 618); polyphosphite rich (eg Wytox® 345-S (1) supplied by Olin); phenol and bisphenol phosphites (for example, Wytox® 604 supplied by Olin); and diphosphonium (e.g., 4-4'-biphenylene diphosphite tetrakis (2,4-di-tert-butylphenyl), which is supplied by Sandox under the designation of Sandostab® P-EPQ). At least one nitrogen-containing stabilizer is added to the homogeneously branched ethylene polymer in a melt mixing step, preferably through the use of an additive concentrate, prior to manufacture and the configuration process steps. At least one stabilizer containing nitrogen can be added to the interpolymer at any effective concentration. However, preferably, the concentration of at least one nitrogen-containing stabilizer will be in the range of 0.05 to 0.5% by weight (based on the total weight of the stabilizer and interpolymer), preferably in the range of 0.075 to 0.3%. by weight (based on the total weight of the stabilizer and the ether polymer), and most preferably in the range of 0.1 to 0.25% by weight (based on the total weight of the stabilizer and the interpolymer). Process additives, for example, calcium stearate, water and fluoropolymers, may also be used for purposes such as deactivation of the residual catalyst or improved processability, or both. Dyes, coupling agents and flame retardants may also be included as long as their incorporation does not disrupt the desirable characteristics of the article of the invention, interpolymer or method. The homogenously branched ethylene interpolymer can also be filled or not filled. If it is filled, then the amount of filler present should not exceed an amount that could adversely affect the high temperature elasticity and / or the wash and drying capacity of the article of the invention. Typically, the amount of filler present is between 20 and 80, preferably between 50 and 70% by weight (% / p) based on the total weight of the ether polymer. Representative fillers include kaolin clay, magnesium hydroxide, silica, calcium carbonate. In a preferred embodiment, the filler is covered with a material that will prevent or retard any tendency that the filler might otherwise have to interfere with desirable irradiation and / or interlacing reactions and effects. Stearic acid is an illustrative example of said protective filler cover, although other compounds may be used as protective filler coatings or treatments. The homogenously branched ethylene interpolymer, elastic, improved and the elastic article of the invention have utility in a variety of applications. Suitable applications include, but are not limited to, disposable personal hygiene products (eg, trainers, diapers, absorbent underwear, incontinence products, and feminine hygiene items).; disposable and durable garments (for example, elastic components in industrial clothing, coveralls, head coverings, underwear pants, pants, shirts, gloves and socks); infection control / cleaning of room products (for example, surgical gloves and bandages, masks, head covers, surgical covers and covers, shoe covers, boots, wound dressings, bandages, sterilization wraps, laboratory covers, pants, aprons, shirts and bedding and sheets) and sportswear. Various homologous fibers can be made from the elastic ethylene interpolymer of the present invention, including short fibers, spunbond fibers or blown fibers under fusion (using, for example, systems described in US Patent No. 4,340,563 (Appel. and others), U.S. Patent No. 4,663,220 (Wisneski et al.), U.S. Patent No. 4,668,566 (Braun), or U.S. Patent No. 4,322,027 (Reba)), fibers spun by gei (e.g., the system described in US Pat. U.S. Patent No. 4,414,110 (Kavesh et al))). The short fibers can be spun-fused (i.e., they can be extruded to the final fiber diameter directly without further extraction), or they can be spun by fusion to a larger diameter and subsequently heating or cooling to the desired diameter using techniques of conventional fiber extraction.

The elastic short fibers of the present invention can also be used as binding fibers, especially when the elastic fibers of the invention have a lower melting point than the surrounding matrix fibers. In a bonding fiber application, the bond fiber is typically mixed with other matrix fibers and the entire structure is subjected to heat, when the bonding fiber melts and joins the surrounding matrix fiber. Typical matrix fibers benefit from the use of the elastic fibers of the invention, described herein, include but are not limited to poly (ethylene terephthalate) fibers, cotton fibers, nylon fibers, polypropylene fibers, fibers of heterogeneously branched polyethylene, homogenously branched ethylene polymer fibers, and linear polyethylene homopolymer fibers, and combinations thereof. The diameter of the matrix fiber may vary from the end-use application. It is also possible to make two-component fibers from the elastic interpolymer of the invention described herein. Said two-component fibers have the homogeneously branched, elastic ethylene interpolymer of the present invention and at least a portion of the fiber. For example, in a sheath / core two-component fiber (ie, one of which, the sheath concentrically surrounds the core), the homogenously branched, elastic, stable ethylene interpolymer may also be in the sheath or core. It is also possible to use different homogenously branched, elastic ethylene interpolymers of the present invention independently of the sheath and the core in the same fiber, preferably when both components are elastic and especially when the component has a lower melting point than the component. of core. Other types of two-component fibers are within the scope of the invention as well, and include structures such as collateral conjugated fibers (e.g., fibers having separate polymer regions, wherein the homogeneously branched, elastic ethylene interpolymer of the present invention comprises at least a portion of the surface of the fiber). The shape of the fiber is not limited. For example, a typical fiber has a circular cross-sectional shape, but some fibers have different shapes, such as the shape of three lobes, or a flat shape (ie, "ribbon" type.) The elastic fiber described herein is not limited. By fiber configuration, fiber diameter can be measured and reported in a variety of ways.Fiber diameter is usually measured in deniers per filament.Denier is a textile term, which is defined as grams of fiber. fiber by 9000 meters of that length of fiber Generally, monofilament 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 15 or less Generally, microdenier (aka microfiber) generally refers to fiber having a diameter not greater than 100 microns.The elastic fibers of the invention described herein, and the diameter may be widely varied, with a small impact on the elasticity of the fiber. However, the denier of the fiber can be adjusted to adapt the capacities of the finished article and as such, preferably it can be from 0.5 to 30 denier / filament for meltblowing; from 1 to 30 denier / filament per spin; and from 1 to 20,000 denier / filament for continuous wound filament. Fabrics made from the stable, elastic fibers of the invention described herein include both woven and non-woven fabrics. Non-woven fabrics can be made in a variety of shapes, including lace fabrics (or hydrodynamically entangled fabrics) as described in U.S. Patent No. 3,485,706 (Evans) and U. U. Patent No. 4,939,016 (Radwanski et al.); cardando and thermally joining short fibers; spun spinning continuous fibers in a continuous operation; or blowing under melting the fibers to a fabric and subsequent calendering or thermally bonding the resulting web. These various nonwoven fabric manufacturing techniques are well known to those skilled in the art and the description is not limited to any particular method. Other structures made from fibers are also included within the scope of the invention, including, for example, blends of these stable, novel, stable fibers with other fibers (e.g., polyethylene terephthalate (PET) or cotton). Fabricated articles can be made which utilize the stable, elastic fibers and fabrics of the invention, described herein, and include stable, elastic mixed articles (eg, diapers and underwear) having elastic portions. For example, the elastic portions are typically constructed to a diaper and waistband portions of underwear to prevent the diaper or underwear from falling into the leg band portions to prevent leakage (as shown, for example, in U.S. Patent No. 4,381,781 (Sciaraffa)). In general, the elastic portions promote a better fit and / or fastening systems for a good combination of comfort and reliability. Stable fibers and elastic fabrics of the invention can also produce structures that combine elasticity and breathing capacity. For example, the fibers, fabrics and / or elastic films of the invention can be incorporated into the structures described in the provisional patent application of E. U. A. 60 / 083,784, filed May 1, 1998 in the name of Maugans et al. The fibers and stable elastic fabrics described herein can also be used in various structures as described in the patent of E. U. A. No. 2,957,512 (Wade). For example, the layer 50 of the structure described in the US patent '512 (ie, the elastic component) can be replaced with stable, elastic fibers and fabrics of the invention, especially when making flat, folded, crimped materials, entangled, etc., not elastic to elastic structures. The bonding of suitable fibers and / or elastic fabrics of the invention to fibers, non-elastic fabrics or other structures can be done through fusion bonding or with adhesives. Elastic structures may be produced as a whole or shirred from the fibers and / or stable elastic fabrics of the invention and non-elastic components by folding the non-elastic component (as described in US Patent '512) before joining, pre-stretching of the elastic component before joining, or heat shrinking of the elastic component after joining. The stable elastic fibers of the invention described herein can also be used in a lacing process (or hydrodynamically entangled) to make novel structures. For example, US Patent No. 4,801,482 (Goggans) discloses an elastic sheet 12 (which can now be made with novel elastic fibers / fabrics described herein.) Continuous stable elastic filaments can also be used as described herein in non-woven applications in where elasticity is desired The stable fibers and elastic fabrics of the invention with adjustment in the interpolymer melt index and / or degree of entanglement or grade or radiation also have an adjustable tenacity and retraction force.These capabilities and characteristics allow an extensive design flexibility, for example, to provide a variable reactive force in the garment itself, if necessary, as described, for example, in U.S. Patent 5,196,000 (Clear et al.) U.S. Patent No. 5,037,416 (Alien and others) describes the advantages of a top sheet of shape fixation using elastic slats (see member 19 of the paten E. U. A. '416). The stable elastic fibers of the invention can serve to operate member 19 of the U.A.A. '416 patent., or they can be used in fabric form to provide the desired elasticity. Mixed materials using very high molecular weight linear polyethylene or copolymer polyethylene also benefit from the stable elastic fibers of the invention described herein. For example, the elastic fibers of the invention have a low melting point (the melting point of the polymer essentially and linearly related to the density of the polymer), so that in a mixture of stable elastic fibers of the invention described herein and fibers of very high molecular weight polyethylene (e.g., Spectra ™ fibers made by Allied Chemical) as described in U.S. Patent No. 4,584,347 (Harpell et al), the lower melting elastic fibers bind the polyethylene fibers of high molecular weight without the fusion of high molecular weight fibers, thus preserving the high strength and integrity of the high molecular weight fiber. In the patent of E. U. A. No. 4,981,747 (Morman), the suitable elastic fibers and / or fabrics of the invention can be replaced by the elastic sheet 122, which forms a mixed elastic material including an irreversibly neck material. The stable elastic fibers of the invention can also be an elastic component blown under melting, as described in reference 6 of the drawings of the patent of E. U. A. No. 4,879,170 (Radwanski). The patent of E. U. A. '170 generally describes an elastic co-form material and manufacturing processes. Elastic panels can also be made from the appropriate elastic fibers and fabrics of the invention, and can be used, for example, as members 18, 20, 14, and / or 26 of U.S. Patent No. 4,940,464 (Van Gompel). ). Suitable fibers and elastic fabrics of the invention can also be used as elastic components of mixed side panels (for example, layer 86 of the patent of E. U. A. No. '464). The stable, homogeneously branched ethylene interpolymer can also be configured or manufactured into stable elastic films, covers, sheets, strips, and ribbons, and battens. The elastic film, cover and sheet of the present invention can be manufactured by any method known in the art, including blown bubble processes (e.g., simple bubble as well as biaxial orientation techniques, so that the trapped bubble , double bubble and frame formation), cast extrusion, injection molding processes, thermoforming processes, extrusion coating processes, profile extrusion and sheet extrusion processes. The simple blown bubble film processes are described in, for example, The Encyclopedia of Chemical Technology. Kirk-Othmer, 3rd. Edition, John Wiley &; Sons, New York, 1981, Vol. 16, p. 416-417 and Vol. 18, p. 191-192. The casting extrusion method is described in, for example, Modern Plastics, October 1989, Encyclopedia Issue, Volume 66, number 11, p. 256 to 257. Injection molding, thermoforming, extrusion coating, profile extrusion and sheet extrusion processes are described in, for example, Plastics Materials and Processes, Seymour S. Schwartz and Sidney H. Goodman, Van Nostrand Reinhold Company , New York, 1982, p. 527-563, p. 632-647, and p. 596-602. Suitable elastic strips, tapes and strips of the present invention can be prepared by any known method, including direct extrusion processing or through subsequent extrusion scoring, cutting or stamping techniques. Profile extrusion is an example of a primary extrusion process that is particularly suitable for the preparation of tapes, strips, strips and strips. The stable elastic materials of the present invention can also be made permeable or "breathable" by any method known in the art, including, forming openings, grooving, microperforation, mixing with fibers or foams, and combinations thereof. Examples of such methods include, U.S. Patent No. 3,156,242 by Crowe, Jr., U. A. Patent No. 3,881,489 by Hartwell, U. U. Patent No. 3,989,867 by Sisson and U. U. Patent No. 5,085,654 by Buell. Suitable articles that can be made using the stable elastic articles of the invention include mixed fabric articles (eg, disposable garments and incontinence pads), which are composed of one or more elastic components or portions. The stable elastic articles of the invention described herein can also produce mixed fabric structures, which combine elasticity with breathability using a technique that makes the elastic material permeable or "breathable" as suggested by L? Ppert and others. , in U.S. Patent No. 4,861,652 and indicated above. The stable elastic articles of the invention described herein can also be used in various structures as described in the patent of E. U. A. No. 2,957,512 (Wade). For example, the layer 50 of the structure described in US Pat. No. 512 (ie, the elastic component) can be replaced with novel stable elastic materials, especially when non-elastic, flat, folded and crimped materials are made of elastic structures. or semi-elastic. The bonding of novel suitable elastic materials to non-elastic or less elastic materials can be accomplished by heat bonding or adhesive bonding. Elastic mixed gathered or shirred materials can be produced from the new stable elastic material described herein and non-elastic components by folding the non-elastic component (as described in US Patent '512) before joining, pre-stretching the elastic component before the joining, or shrinking with heat of the elastic component after joining. The recovery after the heat shrink can also be improved by effecting a high degree of orientation in the stable elastic articles of the invention during manufacture. The important orientation can be achieved through the use of various known techniques, such as manufacture of high blown or blown film, casting of cast films and manufacture of "double bubble" or "trapped bubble" film. The stable elastic articles of the invention described herein can also be used to make other novel structures. For example, the patent of E. U. A. No. 4,801,482 (Goggans) describes an elastic sheet (12) which can now be made with the stable elastic articles of the invention described herein. The stable elastic articles of the invention described herein can also be used to make a breathable portion or breathable elastic composite materials. For example, US Patent No. 5,085,654 (Buell) discloses a band (15) for the leg with a breathable portion 45, a breathable upper sheet (26), a breathable backsheet (25), elastic elements (31 and 64) , a breathable element (54), and a breathable sub-element (96) all or any combination of which can now be made with the stable elastic articles of the invention either in permeable or impermeable forms. U.S. Patent No. 5,037,416 (Alien et al.) Discloses the advantages of a shape fixation topsheet using elastic slats (member 12) and an elastic backsheet (member 16). The stable permeable elastic articles of the invention described herein, can serve the function of the member 12 and waterproof elastic materials of this invention can function as the member 16, or the described elastic materials can be used in an elastic mixed fabric form. In the patent of E. U. A. No. 4,981,747 (Morman), the stable elastic articles of the invention described herein can be replaced by elastic sheets 12, 122 and 232 to construct a composite elastic material that includes a reversibly neck-shaped material. Panels, elements or elastic portions can also be made from the stable elastic articles of the invention, and can be used, for example, as members 18, 20, 24, and / or 26 of US Patent No. 4,940,464 (Van Gompel). The stable elastic articles of the invention described herein can also be used, for example, as elastic mixed side panels (e.g., layer) or as elastic battens 42 and / or 44. The following examples are provided to illustrate and further illuminate the present invention, but are intended to limit the invention to the specific embodiments set forth.

EXAMPLES In an evaluation to determine the elastic performance of the various ethylene polymers in response to irradiation or entanglement, 5 different ethylene interpolymers were subjected to varying degrees of electron beam radiation and their elastic properties as cast films of 102. mm were measured at room temperature. Polymer densities and melt indexes of ethylene polymers are shown in Table 1. All polymers were homogenously branched ethylene / 1-octene ether copolymers, commercially available from Dupont Dow Elastomers, Ltd., manufactured using a system of restricted geometry catalyst and containing 2000 rpm of Irganox 1010 thermal stabilizer. However, DDE 8190 was also contained by mixing 4-5% by weight of isotactic polypropylene. The densities for various polymers were determined in accordance with ASTM D-792 and the melt indexes were determined in accordance with ASTM D-1238 Condition 190 ° C / 2.16 kilograms.

TABLE 1 102 mm cast films of each polymer listed in Table 1 were fabricated using conventional cast film extrusion equipment at melting temperatures of 221-260 ° C. After the manufacture of the film, the cast films were irradiated with electron beam light at various doses using equipment similar to that described in the patent of US Pat. No. 5,324,576. Except as otherwise indicated, the elastic properties (strain-strain data) for the various films were determined using an Instron tensiometer set at 25 cm / minute. For the permanent fixation determinations at 23 ° C, the length of the garment was 5.1 cm and the cross head speed was 51 cm / minute. The test consisted of pulling the film sample at a tension of 200% (elongation) and holding it for 30 seconds, then taking the sample at a tension of 0% (elongation) and leaving it at a tension of 0% for 60 seconds, and Then pull the sample to determine the point where the load initially increases above zero. The percentage of permanent fixation was taken as the percentage of deformation at which the load arrives above zero. The test was a cycle test operated in duplicate. To determine the percentage of tension or load relaxation at 23 ° C, the length of the garment was 5.1 cm and the speed was 51 m / minute. These tests consisted of pulling a film sample at a tension of 2005 (elongation) and keeping them there at a tension of 200% for 30 seconds. The voltage initially at a voltage of 200% was taken as the maximum voltage and the voltage after the second holding period of 30 seconds was taken as the minimum voltage. The percentage determinations of tension or load relaxation operated in duplicate and were calculated from the following equation: Maximum voltage - minimum voltage X 100 maximum voltage Table 2 reports the elastic property data (stress-strain) as well as permanent fixation and stress relaxation data for the various film samples. The data in Table 2 were plotted and are shown in Figure 1 and Figure 2. Figure 1 indicates that electron beam light radiation of up to 8-12 megarads has no substantial effect on the percentage of relaxation performance of tension of the various polymers. Conversely, Figure 2 shows that irradiation has a dramatic effect on the percentage of permanent fixation performance of ethylene polymers. However, Figure 2 (as well as Figure 1 and the results shown in WO 95/29197) show no particular distinction between the various polymers since the polymer density dominated the percentage of permanent fixation response and the radiation affected the various polymers in the same way In another evaluation, 102 mm cast films of resin A and resin D were subjected to varying doses of electron beam radiation and evaluated to determine their respective percentage of load stress or load relaxation at 38 ° C. These tests were performed as described above, except that the temperature was 38 ° C instead of 23 ° C, and the samples were maintained at a resistance of 200% for 1 hour instead of 30 seconds. Table 3 shows the results for this evaluation, and Figure 3 graphs the results using the average of the samples in duplicate as well as an average of 4 data points for the resin D at 5-8 megarrads of the beam radiation of electrons TABLE 2 * Example 1 of * Example Example 2 Example Example Invention Comparative Invention 3 * Comparative 4 * Comparative 5 * Resin AAAABBBB cccc DDDDEEEE e-Light beam-megarads 0 3 5 8 0 3 5 8 0 3 5 8 0 5 6 12 0 5 8 12 100% tension load g / inch 232 242 254 259 191 170 211 214 330 315 318 327 131 328 329 397 327 325 303 317 200% load per tension g / inch 269 290 318 354 226 211 235 238 409 384 380 395 387 357 423 379 367 430 382 385% voltage @ 762 651 785 491 1109 896 973 860 667 676 697 410 812 780 883 784 909 869 809 773 rupture Percentage 21 9 10 22 17 11 75 66 41 28 20 23 42 24 35 22 50 24 24 26 Permanent fixation @ 200% voltage stress 19 18 18 19 20 17 19 20 22 20 25 21 23 18 23 19 23 23 22 21 relaxation @ 200% deformation% xylene NA 98.7 9104 68.2 NA 99.6 991 99.6 NA 996 99.8 73.9 NA 99.7 99.3 81.5 NA 99.6 99.4 77.5 extras ^ 1 Jo an example of the innovation; provided only for purposes of illustration.

TABLE 3 The data in Table 3 and Figure 3 show, surprisingly, that the irradiation can substantially reduce, ie, improve) the high temperature tension relaxation performance of ethylene interpolymers having densities less than 0.87 g / cm 3 and in In reverse form, they show that the irradiation has no effect or increases the high temperature stress relaxation operation of ethylene interpolymers characterized by higher densities. The data in Table 3 also show that the minimum stress of ethylene interpolymers characterized because they have densities less than 0.87 g / cm3, desirably increases to a higher dose level. The extrapolation of Figure 3 indicates that at an electron beam light radiation dose level of 20 megarrads, said interpolymers will exhibit a tension relaxation percentage at 38 ° C of less than 20. In another investigation, the effectiveness of several stabilizers. In this investigation, stabilizer concentrates of 2% by weight were first prepared by dry mixing and spinning separately a thioester stabilizer (i.e., Evanstab 12), and a diphenylamine stabilizer (Naugard 445), a substituted piperidine stabilizer (ie, Chimassorb 944) and a hydroquinoline stabilizer (ie, Agerite D) with a homogenously branched ethylene interpolymer (ENGAGE 8150 which has a target density of 0.78 g / cm3 and an I2 melt index of 0.5 g / 10 minutes). The dry mixes were then extruded under melting in a Berlyne extruder having an L-D of 30: 1 and equipped with a screw with a diameter of 2.5 cm. The extrusion melting temperature was maintained at 204 ° C, the various melting baths were pelletized and allowed to cool to room temperature. Also, a 10% by weight concentrate of Irganox 1010 (a hindered phenolic stabilizer) was prepared using the same homogeneously branched ethylene interpolymer as above. However, the Irganox 1010 concentrate was prepared with a Haake mixer at a melting temperature of 204 ° C and a mixing residence time of 5 minutes. The Haake fusion mixture was removed from the mixing vessel after the mixing residence time of 5 minutes, allowed to cool to room temperature and then crumbled to small granules. The various stabilizer concentrates were dry mixed by rotation with two different homogenously branched ethylene interpoiomers, one nominally stabilized and the other unstabilized, and both having a peak melting point of less than 70 ° C as determined using differential scanning calorimetry, for several prepared samples. The samples were then spun down under fusion separately to fibers. The fibers were spun under melt separately in a fiber extrusion equipment consisting of an extruder, gear pump and spinner. The extruder was set to provide a melting temperature of 236 ° C. Each polymer melt bath stream was fed to the gear pump, which pressurized the melt bath and passed it through 200 meshes followed by a 34-hole spinner die. The spinner had an L / D of 4: 1, and the holes had a diameter of 800 microns. The resin output of the spinner was controlled at 0.78 g / hole. The fibers were quenched with a high speed air blower at room temperature and collected as free falling fiber samples. The resulting fibers had an average diameter of 800 microns. All the stabilizers allowed the preparation of a fiber with good quality since there is no fiber surface process or defect associated with any stabilizer. The various fiber samples were then irradiated using electron beam radiation to 20 megarads. The irradiated fibers were then evaluated to maintain their ability to withstand ordinary washing and long-term aging. To determine stability or strength, a fiber sample was stretched at a tension of 200% (elongation) 5 times using an Instron tensometer and then placed in a wash solution at 71 ° C. The wash solution consisted of 100 ppm copper chloride and 0.5% by weight of the regular domestic formula of the Tide ™ detergent supplied by Procter and Gamble, and distilled water. The wash solution consisted of 275 milliliters contained in a 500 ml wide-mouthed beaker. The washing temperature of 71 ° C was maintained through the use of a hot plate equipped with a Variac device and thermotherm. Agitation of the wash solution was achieved using a magnetic stirrer, where the hot plate provided the field currents against magnetic to effect rotation of the magnetic stirrer. All the fiber samples were submitted in a washing solution at the same time (jointly) and vigorously stirred for 30 minutes. After exposure for 30 minutes to the wash solution, the fiber samples were carefully removed using tweezers and placed on paper towels to absorb excess wash solution. The washed fibers were then placed separately on a Mylar ™ film (polyester type A film available from The Pilcher Hamilton Company and placed in a circulating air oven.The oven was set at 133 ° C for 10 hours. After aging in the 10-hour oven, the fiber samples were carefully removed (ie, avoiding excessive handling and direct handling) from the oven and examined for visual indications of loss of integrity (eg, melting or fluid capacity). or adhesion to the Mylar film or both Table 4 provides the description of the various samples, provides descriptions of the samples after washing and aging exposures in the furnace and also provides a range ordering the resistance of the various samples to the washing exposure / furnace The results in Table 4 indicate that nitrogen-containing stabilizers such as Naugard 445, Chimassor b 944 and Agerite D are more effective than thioester or phenol stabilizer to stabilize the elastic fibers against loss of integrity due to washing and aging in the furnace. In particular, Table 4 shows that stabilizers such as Agerite D can provide excellent protection, so that there is absolutely no fusion of the fiber or adhesion to the Mylar film. Although the test described above may conveniently and adequately distinguish the merits of the present invention, an improved quantification may be conveniently achieved by measuring the diameter of the fiber (at the widest point) before the exposures and comparing those measurements with the measurements of diameter (at the widest point) taken after the exposures. Any median difference in diameters can be taken as a loss of integrity due to melting and flow. Nevertheless, one skilled in the art will recognize that out-of-flow and swelling indications are indicative of more substantial changes in integrity than melting and adhesion to a Mylar film which generally reflects a substantially less change than the melt bath. Those skilled in the art will also recognize that a melting indication should be made immediately when the sample is removed from the furnace and that various auxiliaries can be used to help determine whether a polymer material is melted or not. Said auxiliaries may include, for example, a pin point probe, a microscope, or Polaríod ™ lenses.

The resin F is an ethylene-octene copolymer having a target density of 0.870 g / cm3 and a melt index of 2 g / 10 minutes. Resin G is an ethylene-octene copolymer having a target density of 0.870 g / cm3 and a melt index of 0.5 g / 10 minutes and containing 800 ppm of Sandostab P-EPQ and 500 ppm Irganox 1076, Ciba-Geigy , trademark of octadecyl 3- (3,5-di-tert-butyl-4-hydroxyphenyl) propionate, which is a hindered phenol stabilizer. * The degree of notation as the adhesion refers to the angle that the Mylar film had to be flexed to adhere to the given sample where 0 ° was the horizontal flat surface and 90 ° was approximately perpendicular to the flat horizontal surface, except for the invention example 13 which moved freely with light film proof handling.

Claims (31)

1. - A method for making an irradiated interlaced article, configured comprising the steps of: (a) providing at least one homogenously branched ethylene interpolymer, which comprises: (i) an ethylene interpolymerized with at least one other monomer and characterized having a polymer density as measured in accordance with ASTM D792 less than 0.90 g / cm3 at 23 ° C, and (ii) at least one nitrogen-containing stabilizer, (b) making or configuring the article from the interpolymer, and (c) after fabrication or configuration, subjecting the article to ionization radiation to intertwine the article by irradiation.

2. A method for making an elastic interlaced article by irradiation, comprising the steps of: (a) providing at least one homogenously branched ethylene ester having a density, as measured in accordance with ASTM D792, of less than or equal to equal to 0.865 g / cm3 at 23 ° C and comprising at least 0.05% by weight of at least one nitrogen-containing stabilizer, (b) making or configuring the article from the interpolymer, and (c) after the manufacture or configuration, subject the article to ionization radiation, where the article is characterized by having: (i) a percentage of permanent fixation less than 60 to 23 ° C and 200% tension when measured at a thickness of 102 mm using an Instron tensiometer after being configured and interlaced by irradiation, (ii) a percentage of stress relaxation better than or equal 25 to 23 ° C and 200% tension when measured at a thickness of 102 mm using an Instron tensiometer after being configured and interlaced by irradiation, and (iii) a percentage of tension relaxation less than or equal to 55 to 38 ° C and 200% tension when measured at a thickness of 102 mm using an Instron tensiometer after being configured and interlaced by irradiation.

3. The methods according to claims 1 and 2, wherein the method further comprises incorporating at least one pro-rad additive in the interpolymer.

4. The method according to claim 1, wherein at least one homogeneously branched ethylene ether is a substantially linear ethylene interpolymer, characterized in that it has: (a) a melt flow ratio, I10 I2 =: 5.63. (b) a molecular weight distribution, Mw / Mn, as determined by gel permeation chromatography and defined by the equation: (lvVMn) < (l10 / l2) - 4.63, "(C) a gas extrusion rheology so that the critical shear rate at the start of the melt surface fracture for the substantially linear ethylene polymer is at least 50% greater than the critical shear rate at the start of the melt surface fracture for a linear ethylene polymer, wherein the substantially linear ethylene polymer and the linear ethylene polymer comprise the same comonomer or comonomers, the linear ethylene polymer has a l2 and Mw / Mn within 10 % of the substantially linear ethylene polymer, and wherein the respective critical shear rates of the substantially linear ethylene polymer and the linear ethylene polymer are measured at the same melting temperature using a gas extrusion rheometer, and (d) an individual differential scanning calorimetry, DSC, melting peak between -30 and 150 ° C.

5. The method according to claim 2, wherein the ionization radiation is provided through electron beam irradiation.

6. - The method according to claim 1, wherein at least one nitrogen-containing stabilizer is selected from the group consisting of hydroquinoline, diphenylamine and substituted piperidine.

7. The method according to claim 2, wherein the article is manufactured using a technique selected from the group consisting of spinning under fiber melting., blown under fiber melting, spinning, lacing, carding, film blowing, cast film, injection molding, stretch extrusion, thermoforming, stamping, forging, blow molding, sheet extrusion, solvent casting, coating of solvent, thermal lamination, calendering, lamination, reaction injection molding, extrusion coating, dispersion coating, and rotomolding.

8. The method according to claim 2, wherein the article is allowed to cool or extinguish at room temperature between 0 and 30 ° C before the application of heating or additional ionization radiation.

9. The method according to claim 1, wherein the homogeneously branched ethylene interpolymer is a homogenously branched linear ethylene polymer.

10. The method according to claim 8, wherein the homogenously branched linear ethylene interpolymer is characterized by having an individual differential scanning calorimetry, DSC, melting peak of between -30 ° and 150 ° C.

11. - The method according to claim 1, wherein the homogenously branched ethylene interpolymer is mixed with another natural synthetic polymer.

12. The method according to claim 11, wherein the synthetic or natural polymer is an olefin polymer.

13. The method according to claim 11, wherein the natural synthetic polymer is a crystalline polyethylene having a density of 23 ° C greater than or equal to 20% by weight as determined using differential scanning calorimetry.

14. The method according to claim 13, wherein the crystalline polyethylene has a density of 23 ° C greater than or equal to 50% by weight as determined using differential scanning calorimetry.

15. The method according to claim 11, wherein the natural synthetic polymer is a polypropylene.

16. The method according to claim 15, wherein the polypropylene is an isotactic polypropylene polymer.

17. The method according to claim 1, wherein the homogeneously branched ethylene interpolymer comprises ethylene interpolymerized with at least α-olefin.

18. The method according to claim 17, wherein the α-olefin is an α-olefin of 3 to 20 carbon atoms.

19. The method according to claim 1, wherein the homogeneously branched ethylene interpolymer comprises ethylene interpolymerized with propylene.

20. - The method according to claim 1, wherein the ethylene interpolymer comprises ethylene ether polymerized with a styrenic compound.

21. The method according to claim 20, wherein the styrenic compound is styrene and the interpolymer is an ethylene-styrene interpolymer.

22. The method according to claim 21, wherein the ethylene-styrene interpolymer comprises from 0.5 to 65 mol% styrene, as determined using nuclear magnetic resonance analysis, wherein: (a) the sample preparation is in 1, 1, 2, 2-tetrachloroethane-d2 (TCE-d2), and (b) the spectra are accumulated in a Varian VXR 300 unit with the sample probe at 80 ° C and referenced to the residual protons of TCE- d2 at 5.99 ppm.

23. The polymer configured in accordance with claim 1 or 2, in the form of a film.

24. The interpolymer configured according to claim 1 or 2, in the form of a fiber.

25. The interpolymer configured according to claim 1 or 2, in the form of a mold.

26. The interpolymer configured according to claim 1 or 2, in the form of a thermoform.

27. The interpolymer configured according to claim 1 or 2, in the form of a woven or non-woven fabric

28. - A personal hygiene article comprising the configured interpolymer of claim 1 or 2. The article according to claim 28, wherein the article is a disposable diaper. 30. The article according to claim 29, wherein the diaper comprises a backsheet or a top sheet composed of the configured interpolymer. 31. An infection control article comprising the configured interpolymer of claim 1 or 2.