ELASTOMERIC TAPES WITH MICROTEXTURED SKIN LAYERS

Abstract: Microtextured elastomeric laminate tape (1) comprising a laminate with at least one elastomeric layer (3) and at least one thin skin layer (2, 4), and an adhesive layer, preferably prepared by coextrusion of the layers followed by stretching the laminate past the elastic limit of the skin layers and then allowing the laminate tape to recover.

Description: E ASTOMERIC TAPES WITH MICROTEXTURED SKIN LAYERS FIELD OF THE INVENTION The invention concerns elastomeric tape and more specifically concerns tape laminates. These tape laminates are particularly useful in garment applications. BACKGROUND Elastomeric tapes are known and used for a variety of purposes. The most common use of elastomeric tapes is as a stretchable backing for a bandage. This is discussed in, e.g., U.S. Pat. No. 3,618,754 (Hoey), which describes a composite structure using a woven layer having elastomeric warp yarns interspersed with flexible warp yarns, the cross or filler yarns are exemplified as cotton. The elastomeric yarns are preferably an elastomeric Spandex™ core with a rayon spun outer covering. This tape is complex and difficult to manufacture. Other constructions for bandage tapes are likewise complex with many designed to provide controlled modulus behavior. Namely, a tape is preferred that has only a limited degree of extensibility and then a high modulus value. Elastomeric tapes have also been proposed for use as electrical insulating tapes based on the electrical properties of rubber as well as their ability to grip a surface, i.e. with their recovery forces when applied under stress. These types of elastic tapes are described, for example, in U.S. Pat. Nos. 3,379,562, 2,559,909 and 3,253,073, which are all described as insulating tapes. U.S. Pat. No. 2,559,990 describes a basic elastic tape of an elastic film forming polymer with a rubber-resin adhesive coating. The elastomer is described as a plasticized vinyl chloride with a blend of plasticizers in permanent equilibrium with a rubber resin adhesive. When this tape is wound into a roll form a liner is used. This liner must be removed when the tape is used to allow it to adhere to itself. Elimination of this removable liner is proposed in U.S. Pat. No. 3,379,562, which places a barrier layer on the tape backside which shatters when stretched. This allegedly exposes the rubber and allows tape to adhere to itself when the tape is stretched. However, fragments of the barrier layer can still interfere with adhesion of the tape to itself. U.S. Pat. No. 3,253,073 describes a tape allegedly designed for high temperature performance. The tape substrate is a laminate of two insulating rubber layers sandwiching a fiber layer. The fibers are brittle and when the tape is stretched sufficiently the fibers break, thereby making the tape elastic in the stretch direction. These fibers are used to improve high temperature performance. A purely elastomeric tape was also disclosed in U.S. Pat. No. 4,024,312 although no specific uses are proposed. The tape comprises a ABA block copolymer based rubber substrate with a rubber resin adhesive on one side and a release coat on the other. The high extensibility allegedly allows the tape to be easily removed when peeled at substantially 0°. This is stated as a desirable quality for ouchless bandages. Elastic tapes or tapes with elasticized regions have also been proposed as closures for diapers, and the like, in U.S. Pat. Nos. 4,389,212, 3,800,796, 4,643,729, 4,778,701 and 4,834,820. In U.S. Pat. No. 4,834,820, an elastic tab is provided with either a removable central section or a inelastic cover layer adhered at only the ends of the elastic. When the removable section is removed, the elastic loses its support and is free to stretch. With an unattached central portion of a cover layer, the central portion has a line of weakness which when broken frees the central elastic region. U.S. Pat. No. 4,778,701 also provides an elasticized central region in a composite tape. An elastic strip is adhered to two nonelastomeric anchor strip tapes used to attach either side of the diaper. Complex constructions having features of the above two patents are described in U.S. Pat. Nos. 4,643,729 and 4,389,212. U.S. Pat. No. 3,800,796 describes tapes with elasticized central portions and rigid ends with adhesive layers. All of these tapes are complex multicomponent composites aimed at providing only limited elastic central tape portions. SUMMARY OF THE INVENTION The present invention relates to non-tacky, microtextured, multi-layer elastomeric laminated tapes. The laminate tape backings of the present invention are comprised both of an elastomeric polymeric core layer(s), which provides elastomeric properties to the laminate and one or more polymeric skin layers which are capable of becoming microtextured. This microtexturing gives the tape natural low adhesion backsize properties, increases ink receptivity, acts as an adhesive primer, and lowers the laminate coefficient of friction and modulus. In preferred embodiments of the present invention the skin layer further can function to permit controlled release or recovery of the stretched elastomer, modify the modulus of elasticity of the elastomeric tape and/or stabilize the shape of the elastomeric tape (i.e., by controlling further necking). The laminate tape backings can be prepared by coextrusion of the selected polymers or by application of one or more elastomer layers onto one or more already formed skin layer(s) or vice versa. Coextrusion is preferred. Pressure-sensitive adhesive (hereinafter adhesive) can be applied by any conventional mechanism including coextrusion. The novel microtextured laminate tape and/or tape backing is obtained by stretching the laminate past the elastic limit of the skin layers. The laminate then recovers, which can be instantaneous, over an extended time period, which is skin in layer controllable, or by the application of heat, which is also skin layer controllable. Stretching of the laminate tape or backing can be uniaxial, sequentially biaxial, or simultaneously biaxial. It has been found that the method and degree of stretch allows significant control over the microtextured surface that results, allowing formation of novel surfaces and adhesion properties. The invention thus further provides various novel surfaces and also a method for the controlled production of these surfaces. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a cross-sectional segment of an extruded laminate tape backing 1 before microstructuring. Fig. 2 is a cross-sectional segment of the Fig. 1 laminate tape backing with microstructuring caused by uniaxial stretching. Fig. 3 is a scanning electron micrograph (200x) of a microstructured laminate tape backing that has been uniaxially stretched. Fig. 4 is a schematic representation of a process and apparatus used to coextrude laminate tapes and/or backings. Fig. 5 is a diagram showing the stress-strain characteristics of a laminate backing and its component layers. Fig. 6 shows an electron micrograph (lOOOx) of a sample of the present invention with a polyethylene skin which was simultaneously biaxially stretched. Fig. 7 is a photograph of a unstretched laminate tape backing that has been marked with ink. Fig. 8 is a photograph of the stretched and recovered laminate of Fig. 7 marked with the same ink. Fig. 9 (T-N) are stress/strain curves for a series of laminate films. Fig. 10 is a scanning electron micrograph (lOO of the surface of a laminate tape backing which has been sequentially biaxially stretched. Fig. 11 is a scanning electron micrograph (lOO of a simultaneously biaxially stretched invention lamina which has a polypropylene(PP) skin. Fig. 12 is a diagram showing the relationship between the shrink mechanism and the core/skin ratio and stretch ratio for a second uniaxially stretched film. Fig. 13 is a diagram showing the relationship between the core/skin ratio, the percent of total recove and activation temperature. Fig. 14 is a diagram of a tape after stretch an activation where the adhesive is a thin coating. Fig. 15 is a diagram as per Fig. 14 with a thicker adhesive coating. Fig. 16 is a scanning electron micrograph (200x of a tape having a thin adhesive layer which forms an undulating surface. Fig. 17 is a scanning electron micrograph (200x of a tape having a thick adhesive forming a relatively flat surface. DETAILED DESCRIPTION OF PREFERRED EMBODIMENTS OF THE INVENTION The present invention relates broadly to novel tape using a non-tacky, multi-layer elastomeric laminate backing comprising at least one elastomeric core layer an at least one relatively nonelastomeric skin layer. The skin layer is stretched beyond its elastic limit and is relaxed with the core so as to form a microstructured surface. Microstructure means that the surface contains peak and valley irregularities or folds which are large enough to be perceived by the unaided human eye as causin increased opacity over the opacity of the laminate before microstructuring, and which irregularities are small enough to be perceived as smooth or soft to human skin. Magnification of the irregularities is required to see the details of the microstructured texture. The elastomer can broadly include any material which is capable of being formed into a thin film layer and exhibits elastomeric properties at ambient conditions. Elastomeric means that the material will substantially resume its original shape after being stretched. Further, preferably, the elastomer will sustain only small permanent set following deformation and relaxation which set is preferably less than 20 percent and preferably less than 10 percent of the original length at moderate elongation, e.g., about 400-500%. Generally, any elastomer is acceptable which is capable of being stretched to a degree that causes relatively consistent permanent deformation in a relatively inelastic skin layer. This can be as low as 50% elongation. Preferably, the elastomer is capable of undergoing up to 300 to 1200% elongation at room temperature, and most preferably up to 600 to 800% elongation at room temperature. The elastomer can be both pure elastomers and blends with an elastomeric phase or content that will still exhibit substantial elastomeric properties at room temperature. Heat-shrinkable elastics have received considerable attention due to the ability to attach the elastic to a product, using the unstable stretched elastomer at ambient conditions, and then later applying heat to shirr the product, such as a diaper. Although these elastomers are contemplated for use in the present invention tape, other non-heat shrinkable elastomers can be used while retaining the advantages of heat shrinkability and with the added dimension of the possibility of substantially controlling the heat shrink process. Non-heat shrinkable means that the elastomer, when stretched, will substantially recover sustaining only a small permanent set as discussed above. Therefore, the elastomeric layer can be formed from non-heat-shrinkable polymers such as block copolymers which are elastomeric such as those known to those skilled in the art as A-B or A-B-A block copolymers. Such copolymers are described for example in U.S. Patent Nos. 3,265,765; 3,562,356; 3,700,633; 4,116,917 and 4,156,673. Styrene/isoprene, butadiene or ethylene-butylene/styrene (SIS, SBS or SEBS) block copolymers are particularly useful. Other useful elastomeric compositions can include elastomeric polyurethanes, ethylene copolymers such as ethylene vinyl acetates, ethylene/propylene monomer copolymer elastomers or ethylene/propylene/diene terpolymer elastomers. Blends of these elastomers with each other or with modifying non-elastomers are also contemplated. For example, up to 50 weight percent, but preferably less than 30 weight percent, of polymers can be added as stiffening aids such as polyvinylstyrenes, polystyrenes such as poly(alpha-methyl ) styrene, polyesters, epoxies, polyolefins, e.g., polyethylene or certain ethylene/vinyl acetates, preferably those of higher molecular weight, or coumarone-indene resin. The ability to use these types of elastomers and blends provides the invention laminate with significant flexibility. Viscosity reducing polymers and plasticizers can also be blended with the elastomers such as low molecular weight polyethylene and polypropylene polymers and copolymers, or tackifying resins such as Wingtack™ , aliphatic hydrocarbon tackifiers available from Goodyear Chemical Company. Tackifiers can also be used to increase the adhesiveness of an elastomeric layer to a skin layer. Examples of tackifiers include aliphatic or aromatic liquid tackifiers, polyterpene resin tackifiers, and hydrogenated tackifying resins. Aliphatic hydrocarbon resins are preferred. Additives such as dyes, pigments, antioxidants, antistatic agents, bonding aids, antiblocking agents, slip agents, heat stabilizers, photostabilizers, foaming agents, glass bubbles, starch and metal salts for degradability or microfibers can also be used in the elastomeric core layer(ε). Suitable antistatic aids include ethoxylated amines or quaternary amines such as those described, for example, in U.S. Pat. No. 4,386,125 (Shiraki), who also describes suitable antiblocking agents, slip agents and lubricants. Softening agents, tackifiers or lubricants are described, for example, in U.S. Pat. No. 4,813,947 (Korpman) and include coumarone-indene resins, terpene resins, hydrocarbon resins and the like. These agents can also function as viscosity reducing aids. Conventional heat stabilizers include organic phosphates, trihydroxy butyrophenone or zinc salts of alkyl dithiocarbonate. Suitable antioxidants include hindered phenolic compounds and amines possibly with thiodipropionic acid or aromatic phosphates or tertiary butyl cresol, see also U.S. Pat. No. 4,476,180 (Wnuk) for suitable additives and percentages. Short fibers or microfibers can be used to reinforce the elastomeric layer for certain applications. These fibers are well known and include polymeric fibers, mineral wool, glass fibers, carbon fibers, . silicate fibers and the like. Further, certain particles can be used, including carbon and pigments. Glass bubbles or foaming agents are used to lower the density of the elastomeric layer and can be used to reduce cost by decreasing elastomer content required. These agents can also be used to increase the bulk of the elastomer. Suitable glass bubbles are described in U.S. Patent Nos. 4,767,726 and 3,365,315. Foaming agents used to generate bubbles in the elastomer include azodicarbonamides. Fillers can also be used to some extent to reduce costs. Fillers, which can also function as antiblocking agents, include titanium dioxide and calcium carbonate. The skin layer can be formed of any semi- crystalline or amorphous polymer that is less elastic than the elastomeric core layer(s) and will undergo permanent deformation at the stretch percentage that the elastomeric laminate will undergo. Therefore, slightly elastic compounds, such as some olefinic elastomers, e.g. ethylene-propylene elastomers or ethylene-propylene-diene terpolymer elastomers or ethylenic copolymers, e.g., ethylene vinyl acetate, can be used as skin layers, either alone or in blends. However, the skin layer is generally a polyolefin such as polyethylene, polypropylene, polybutylene or a polyethylene-polypropylene copolymer, but may also be wholly or partly polyamide such as nylon, polyester such as polyethylene terephthalate, polyvinylidene fluoride, polyacrylate such as poly(methyl methacrylate) (only in blends) and the like, and blends thereof. The skin layer material can be influenced by the type of elastomer selected. If the elastomeric layer is in direct contact with the skin layer the skin layer should have sufficient adhesion to the elastomeric core layer such that it will not readily delaminate. Acceptable skin-to-core contact has been found to follow three modes: first, full contact between core and microtextured skin; second, cohesive failure of the core under the microstructure folds; and third, adhesive failure of the skin to the core under the microstructure folds with intermittent skin/core contact at the fold valleys. However, where a high modulus elastomeric layer is used with a softer polymer skin layer attachment may be adequate yet a microtextured surface may not form. The skin layer is used in conjunction with an elastomeric layer and can either be an outer layer or an inner layer (e.g., sandwiched between two elastomeric layers). Used as either an outer or inner layer the skin layer will modify the elastic properties of the elastomeric laminate. Additives useful in the skin layer include, but are not limited to, mineral oil extenders, antistatic agents, pigments, dyes, antiblocking agents, provided in amounts less than about 15%, starch and metal salts for degradability and stabilizers such as those described for the elastomeric core layer. Other layers may be added between the elastomeric core layer and the skin layers, such as tie layers to improve the bonding of the layers. Tie layers can be formed of, or compounded with, typical compounds for this use including maleic anhydride modified elastomers, ethyl vinyl acetates and olefins, polyacrylic imides, butyl acrylateε, peroxides such as peroxypolymerε, e.g., peroxyolefins, silanes, e.g., epoxysilanes, reactive polystyrenes, chlorinated polyethylene, acrylic acid modified polyolefins and ethyl vinyl acetates with acetate and anhydride functional groups and the like, which can also be used in blends or as co patibilizers in one or more of the skin or core layers. Tie layers are particularly useful when the bonding force between the skin layers and elastomeric core layer(s) is low. This is often the case with polyethylene skin as its low surface tension resists adhesion. However, any added layers must not significantly affect the microstructuring of the skin layers. Tie layers may, however, be omitted even when bonding between skin and core is low. For example, for tamper-indicating tapes, low adhesion delamination can be used advantageously. One unique feature of the invention is the ability to control the shrink recovery mechanism of the tape depending on the conditions of the laminate film formation, the nature of the elastomeric layer, the nature of the skin layer, the manner in which the laminate film backing is stretched and the relative thicknesses of the elastomeric layer(s) and skin layer(ε). By controlling these variables in accordance with the teaching of this invention, the laminate tape or backing can be designed to instantaneously recover, recover over time or recover upon heat activation. A laminate capable of instantaneous shrink is one in which the stretched elastomeric laminate will recover more than 15% in 1 sec. A laminate capable of time shrink is one where the 15% recovery point takes place more than 1 sec, preferably more than 5 sec, most preferably more than 20 sec. after stretch, and a laminate capable of heat shrink is where less than 15% shrink recovery occurs to the laminate in the first 20 εecondε after stretch. Percent recovery is the percent that the amount of shrinkage is of the stretched length minus the original length. For heat shrink, there will be an activation temperature which will initiate significant heat activated recovery. The activation temperature used for heat shrink will generally be the temperature that will yield 50% of the total possible recovery (T a _ 50 ) and preferably this temperature is defined as the temperature which will yield 90% (T a _ 90 ) of the total possible recovery. Total possible recovery includes the amount of preactivation shrinkage. Generally, where the skin layer of the laminate tape backing is relatively thin, the laminate will tend to contract or recover immediately. When the skin thicknesε is increased sufficiently the laminate can. become heat shrinkable. This phenomenon can occur even when the elastomeric layer is formed from a non-heat shrinkable material. Further, by careful selection of the thicknesses of the elastomeric layer and the skin layer(s), the temperature at which the laminate recovers by a set amount can be controlled within a set range. . This is termed skin controlled recovery where generally by altering the thickness or composition of the skin, one can raise the activation temperature of an elastomeric core by a significant degree, generally more than at least 10°F (5.6°C) and preferably by 15°F (8.3°C) and more. Although any skin thickness which is effective can be employed, too thick a skin will cause the laminate to remain permanently set when stretched. Generally, where a single skin is less than 30% of the laminate this will not occur. For most heat or time shrink materials the stretched laminate must be cooled so that the energy released during stretching does not cause immediate heat activated recovery. Fine tuning of the shrink recovery mechanism can be accomplished by the amount of stretch. This overall control over the shrink recovery mechanism can be an extremely important advantage, for example, when the unactivated tape is used in a manufacturing process. This control permits adjustment of the recovery mechanism of the elastomeric laminate tape to fit the requirements of a manufacturing process rather than the need to adjust a manufacturing procesε to fit the εhrink recovery mechaniεm of the elastomer itself. One is also able to use skin controlled recovery to control the slow or time shrink recovery mechanism, as with the heat shrink mechanism. This shrink recovery mechanism occurs as an intermediate between instant and heat shrink recovery. Skin layer and stretch ratio control of recovery iε poεεible as in the heat shrink mechanism, with the added ability to change the shrink mechanism in either direction, i.e., to a heat or an instant shrink elastomeric laminate tape. A time shrink recovery laminate tape will also exhibit some heat shrink characteristicε and vice verεa. For example, a time εhrink laminate tape can be prematurely recovered by expoεure to heat, e.g., at a time prior to 20 seconds after stretch. Recovery can also be initiated for most time shrink and some low activation temperature heat shrink recovery laminates by mechanical deformation or activation. In this case, the laminate tape is scored, folded, wrinkled, or the like to cause localized stresε fractureε that cauεe localized premature folding of the εkin, accelerating formation of the recovered microtextured laminate. Mechanical activation can be performed by any εuitable method εuch as by using a textured roll, a scoring wheel, mechanical deformation or the like. It was also noted that for most elastomeric laminates over a core-to-skin ratio of about 3 to somewhat above 7, the laminate retained a relatively constant width after it had been restretched. Specifically, if the width of the stretched and recovered film is measured, and if the film is restretched and measured or allowed to recover again and measured, the width remainε within at leaεt 20% of its first measured stretch width, preferably within at least 10%. This non-necking characteristic helps prevent the laminate tape from biting into the skin of a wearer when it is used to elaεticize a garment or become dimensionally unstable when used as an electrical, wrapping or removable tape, which may cause pop off, tape εlippage or the like. Generally, the εkin layer will hinder the elastic force of the core layer with a counteracting resisting force. The skin will not stretch with the elastomer after the laminate has been activated, the skin will simply unfold into a rigid sheet. This reinforces the core, resisting or hindering the contraction of the elastomeric core including its necking tendency. Fig. 12 shows a shrink mechanism diagram for polypropylene/styrene-isoprene-styrene ( SIS)/polypropylene(PP) laminates prepared in accordance with Example 29. This diagram demonstrates the ability to control the shrink recovery mechanism by the core/skin ratio and the stretch ratio. Although Fig. 12 is illustrative of a particular set of starting materials and thicknesses, it does represent the general relationship between the layer ratios and stretch ratio to the shrink mechanism of the laminate. Other variables will affect the above relationship such as overall laminate thickness, the presence of tie layers and the thicknesε and type of adhesive layer. However, the general relationship between the core/skin ratio and the stretch ratio to the relaxation method will still be present. Additiveε to the core layer diεcuεεed above can εignificantly affect the εhrink recovery mechaniεm. For example, stiffening aids such as polystyrene can shift an otherwise heat εhrinkable laminate into a time or inεtant εhrink laminate. However, the addition of polypropylene or linear low denεity polyethylene (leεε than 15%) to a εtyrene/iεoprene/styrene block copolymer core resulted in exactly the opposite effect, namely transforming time or instant shrink laminates to heat shrink or no shrink laminates. However, the posεibility of polyolefin use in the elastomeric core layer is significant from a processing standpoint in permitting limited recycling of off batcheε and it can lower extruder torque. A further unique feature of the present invention lies in the ability to significantly reduce the coefficient of friction (C.O.F.) of the elastomeric laminate. The microtexturing is the major factor contributing to thiε C.O.F. reduction which, aε discussed above, is controllable not only by the manner in which the laminate is stretched but also by the degree of stretch, the overall laminate thickness, the laminate layer composition and the core to skin ratio. The dependence of C.O.F. on core/εkin ratio iε εhown in Table II, aε the ratio increaεeε the C.O.F. decreaεeε. Thus, fine texture yields lower C.O.F. values. Preferably, the C.O.F. will be reduced by a factor of 0.5 and most preferably by at least a factor of 0.1 of the microtextured laminate to itself in the direction of stretch, when a microstructured surface is formed in accordance with the invention, as compared to the as cast laminate. This ability to reduce C.O.F. is extremely advantageous as it contributes to a softer texture and feel for the laminate, which is desirable for use in the medical and apparel fields. Writability of the tape iε also increased by non-adhesive coated microstructured surfaces that result when the stretched tape recovers. Either organic solvent or water-based inks will tend to flow into the microstructured surface channels and dry there. Fig. 7 showε the εurface of an unstretched, untextured laminate where the ink clearly beads up. Fig. 8 demonstrates the improvement in writability for the laminate of Fig. 7, after stretching and recovery to create a microtextured surface (see example 26). The more viscouε the ink, the leεs it will tend to wick in the microchannels of the εurface and hence bleed. Similarly, the more the surface attraction between the skin layer and the ink, the better will be the writing characteristics of the microstructured surface. The writing surface characteristics of the film can also be altered with conventional additive or surface treatment techniques to the extent that they do not interfere with microtexturing. The laminate tape backings of the present invention may be formed by any convenient layer forming process such as presεing layerε together, coextr-uding the layerε or εtepwiεe extrusion of layers, but coextrusion iε the preεently preferred proceεε. Coextruεion, per εe, iε known and iε described, for example, in U.S. Patent Nos. 3,557,265 to Chiεholm et al . and 3,479,425 to Leferre et al. Tubular coextrusion or double bubble extrusion is also possible. The layers are typically coextruded through a specialized die and/or feedblock that will bring the diverse materials into contact while forming the laminate. Fig. 1 shows a three-layer laminate tape backing construction in cross section, where the 3 iε the elastomeric layer and 2 and 4 are the skin layers, which may be the same polymer or different polymerε. Thiε layer arrangement is preferably formed by a coextrusion process. One particularly advantageous coextrusion process is possible with special multilayer, e.g. a three-layer, combining adapters made by Cloeren Co., Orange, Texas. These adapters are described in U.S. patent No. 4,152,387 (Cloeren). Streams of thermoplastic materials flowing out of extruderε at different viεcosities are separately introduced into the adapter, containing back presεure cavitieε and flow restriction channels, and the εeveral layerε exiting the flow restriction channels converge into a melt laminate. The combining adapter is used in conjunction with extruders supplying the thermoplastic materials to be laminated. Such a scheme for producing the present invention is shown schematically in Figure 4, for a three layer adapter. AA, BB, and CC are extruders. AA' , BB' and CC are εtreamε of thermoplastic materials flowing into the feedblock or manifold die. D is the 3 or more (e.g., 5-layer) layer feedblock. E is the die, F is a heated caεting roll, and G and H are rollε to facilitate take-off and roll-up of the laminate. The die and feedblock uεed are typically heated to facilitate polymer flow and layer adheεion. The temperature of the die dependε upon the polymers employed and the subsequent treatment stepε, if any. Generally, the temperature of the die iε not critical but temperatures are generally in the range of 350 to 550°F (176.7 to 287.8°C) with the polymers exemplified. Whether the laminate backing is prepared by coating, lamination, sequential extrusion, coextrusion or a combination thereof, the laminate formed and its layers will preferably have substantially uniform thicknesεes across the laminate backing. Preferably, the layers are coextensive acrosε the width and length of the laminate. With such a construction the microtexturing is substantially uniform over the elastomeric laminate surface. Laminateε prepared in thiε manner have generally uniform elastomeric properties with a minimum of edge effects such as curl, modulus change, fraying and the like. Further, when wound aε in a roll of tape, thiε will minimize formation of hard bands, winding problems, roll telescoping or the like. The laminate backing of the invention has an unlimited range of potential widths, the width limited solely by the fabricating machinery width limitations. This allows fabrication of microtextured elastomeric tapes for a wide variety of potential useε. After formation, the laminate tape backing can be stretched past the elastic limit of the εkin, which deforms. The laminate tape backing then is recovered instantaneously, with time or by the application of heat, as discussed above. For heat recovery, the temperature of activation is determined by the materialε uεed to form the laminate in the first instance. For any particular laminate, the activation temperature, either T a _ 50 or T _ 90 , can be adjusted by varying the skin/core ratio of the laminate, adjusting the percent stretch or the overall laminate thicknesε. The activation temperature uεed for a heat εhrink laminate iε generally at least 80°F (26.7 β C), preferably at least 90°F (32.2°C) and most preferably over 100°F (37.8°C). When heat-activated, the εtretched laminateε are quenched on a cooling roller, which preventε the heat generated from the elongation from activating laminate recovery. The chill roll is below the activation temperature. Figure 2 is a εchematic diagram of the common dimensions which are variable for uniaxially stretched and recovered laminate tape backings. The general texture iε a series of regular repeating folds. These variables are the total height A-A' , the peak to peak distance B-B' and the peak to valley distance C-C . These variableε were meaεured for a εerieε of polyolefin/εtyrene-iεoprene-εtyrene/polyolefin laminates. General ranges for A-A', B-B' and C-C were noted. For total height (A-A'), the range meaεured waε from 0.79 to 32 mils (0.02 to 0.81 mm). For peak-to-peak distance (B-B'), or the fold period, the measured range was from 0.79 to 11.8 mils (0.02 to 0.30 mm). For peak-to-valley distance (C-C), the measured range was from 0.04 to 19.7 mils (0.001 to 0.5 mm). These ranges are only exemplary of the surface characteristicε obtainable by the practice of the present invention. Laminate tape backings of other compositionε will demonεtrate different microεtructures and microstructure dimenεions. It is also possible to obtain dimensions outside the above ranges by suitable selection of core/skin ratios, thicknesεes, stretch ratioε and layer compositions. A further unique feature of the invention laminate tape backing is depicted in Fig. 2. That is, when the material is stretched and recovered uniaxially, regular, periodic folds are generally formed. That is, for any given transverse section the distance between adjacent peaks or adjacent valleys is relatively constant. Fig. 3 showε a scanning electron micrograph of the surface of a polybutylene/styrene-isoprene-styrene (SIS)/polybutylene laminate backing of Example 6 which has been stretched paεt the elastic limit of the outer skin layers in the longitudinal direction and allowed to recover to form a microstructured εurface. The microεtructured εurface corresponds to that shown schematically in Fig. 2. The microstructured surface consists of relatively systematic irregularities whether stretched uniaxially, as was the Fig. 3 laminate tape backing, or biaxially. These irregularities increase the opacity of the surface layers of the laminate, but generally do not result in cracks or openingε in the εurface layer when the layer is examined under a scanning electron microscope. Microtexturing also affectε the properties of the formed tape. Uniaxial stretching will activate the tape to be elastic in the direction of stretch. Biaxial stretching will create unique surfaces while creating a laminate tape which will stretch in a multitude of directions and retain its soft feel if there is a microtextured skin backside. It has also been found that the fold period of the microstructured surface is dependent on the core/skin ratio, as shown in Example 3. The periodicity is also indicative of the texture of the surfaces per Table II. This is again another indication of the control possible by careful choice of the parameters of the present invention. It has also been found that the manner in which the laminate tape or backing is stretched effects a marked difference in the texture of the microstructured surface. For example, the extruded multi-layer laminate tape or backing can be stretched uniaxially, sequentially biaxially, or simultaneouεly biaxially, with each method giving a unique εurface texture and diεtinct elastomeric properties. When the film is stretched uniaxially, the folds are microscopically fine ridges, as per Fig. 3, with the ridges oriented transversely to the stretch direction. When the laminate tape backing is stretched first in one direction and then in a cross direction, the foldε formed on the firεt εtretch become buckled folds and can appear worm-like in character with interspersed cross folds aε in Fig 10. Fig. 10 iε a laminate of PP/SIS/PP with a core/skin ratio of 18 (Example 24). Other textures are also posεible to provide variouε folded or wrinkled variations of the basic regular fold. When the film is stretched in both directions at the same time, the texture appears as folds with length directions that are random, as shown in Fig. 6 (a laminate prepared as per Example 19A with skin/core/skin thicknesses of 5/115/5 microns respectively) or Fig. 11 (Example 24). Using any of the above methods of stretching, the surface structure is also dependent, as stated before, upon the materials uεed, the thickness of the layers, the ratio of the layer thicknesses and the stretch ratio. The unique continuous microstructured surfaces of the invention can be altered and controlled by the proper choice of materials and processing parameters. Differences in the material properties of the layers can change the resulting microtextured skin, but it has been found that by the careful choice of the layer ratios, total laminate film thickneεε, the number of layerε, εtretch degree, and stretch direction(s) it iε poεεible to exercise significant control over the microstructure of the laminate skin layer. The degree of microtexturing of elastomeric laminate backings prepared in accordance with the invention can also be described in terms of increase in skin surface area. Where the laminate shows heavy textures, the surface area will increase significantly. This is demonstrated for LLDPE/SIS/LLDPE(linear low density polyethylene) laminateε in Table VIII, Example 16. In thiε example, aε the stretch ratio increaseε εo doeε the percent increaεe in εurface area, from the unεtretched to the εtretched and recovered laminate; from 280 at a εtretch ratio of 5, to 530 at a εtretch ratio of 12. Generally the microtexturing will increase the surface area by at least 50%, preferably by at least 100% and most preferably by at least 250%. The increase in surface area directly contributes to the overall texture and feel of the laminate surface. Increased opacity of the skin and hence the laminate backing also results from the microtexturing. Generally, the microtexturing will increase the opacity value of a clear film to at least 20%, preferably to at least 30%. This increase in opacity is dependent on the texturing of the laminate with coarεe textureε increaεing the opacity less than fine textures. The opacity increase is also reversible to the extent that when restretched, the laminate will clear again. It is also possible to have more than one elastomeric core member with suitable εkinε and/or tie layer(s) in between. Such multilayer embodiments can be used to alter the elastomeric and surface characteristics of the laminate. Adhesive can be applied to the laminate backing by any conventional method, such as: solvent coating, by methodε εuch aε reverse roll, knife-over-roll, gravure wire wound rod, floating knife, or air knife; hot melt coating εuch aε by slot orifice coaters, roll coaters, or extrusion coaters; and direct coextrusion during laminate formation. The adhesive will generally be applied to the as cast laminate backing or when the laminate is stretched prior to recovery. Adhesiveε will preferably be applied to or with the cast laminate unless it is an adhesive which does not stretch to the extent that the laminate is stretched. Although adhesive can be applied to a microstructured surface, this is not as desirable in terms of adhesive layer uniformity, ease of application or adheεive bonding to the laminate. For most applications, the adhesive will be applied continuously across the laminate backing. This eases application and collection, e.g. as a roll, and facilitates use. Adhesive can also be applied to both faces of the laminate backing. A unique advantage of a microstructured surface formed after the adhesive, iε applied is the ability to improve bonding of the adheεive layer to the tape backing. It has been found that when the adheεive layer iε in full contact with a microεtructured εurface there appears to be a mechanical priming that reduces adhesive transfer or cohesive failures in the adhesive layer. This highly advantageous feature is noted at even significantly higher peel forces than the forces which cauεe these problems in corresponding tapes without microstructured surfaces and with the same adhesives. The skin layer-to-core layer contact in the stretched and activated film has been observed to vary depending on the skin and core compositions. With certain preferred constructions, the core and skin remain in full contact with the core material, filling the folds formed in the skin layers aε shown in Fig. 2. Thiε conεtruction is extremely durable and not as subject to delamination, particularly when annealed following activation. A variation of this continuous contact construction is also poεεible where the elastomer fillε the εkin folds but is observed to cohesively fail under the folds. It iε believed thiε occurs with thicker and/or more rigid skins that expose the underlying elastomer to more concentrated streεses during relaxation. An entirely different skin/core adhesion mode is also possible. Namely, the core in some cases can completely retract from the skin under the folds, but remain sufficiently attached such that the skin does not delaminate (see Example 38, adhesive failure). This construction generally is not desirable as during use it is more easily subject to delamination as well as exposing the elastic core to air which may accelerate degradation of the elastomer. The microstructured laminate tape is also highly conformable. This is an important feature as it allows the tape to be applied to a variety of surfaces, particularly to uneven surfaces or moving surfaces, and still give an adequate adhesive to substrate bond. A further unique quality of the invention microstructured tape is its ability to exhibit a wide variation in adhesiveness to itself. The feature is particularly pronounced where both the adhesive layer and backεide of the tape are microεtructured. Namely, at higher rolldown preεεureε significantly greater levels of adheεive bonding are obtainable as compared to lower rolldown pressures. The differences in adhesive levels at differing rolldown pressures is more pronounced when a thinner adhesive is used, aε εhown in Figs. 14 (where 5 is the adhesive layer) and 16, as compared to a thicker adhesive, as shown in Figs. 15 and 17. With a thinner adhesive, the adhesive will more likely be microtextured. It is believed that this variable self-adhesion phenomenon is related primarily to the relative amount of adhesive layer to tape backing contact area, which is potentially much higher where both the adhesive layer and the tape backside have microεtructured surfaces. At low rolldown pressures, adhesive will tend to only contact the microεtructure peaks on the backing. This low-contact area will be exaggerated if the adhesive layer itself has a peak and valley configuration. At higher rolldown presεureε, the adheεive, microtextured or not, will have a tendency to be forced into the valleys of the backside microstructure. This will tend to substantially increase adhesive/backside surface contact and even permit mechanical adhesive priming to the backside in some circumstanceε (e.g., where the adheεive iε flowable), which also increases adhesion. With εofter, more flowable, adhesives the amount of pressure needed to increase adhesive levels will generally be lower. The degree and type of microstructuring will also be a significant factor in determination of the rolldown pressure variance in self-adhesion values (i.e., the degree to which the microstructures will tend to interlock). Multiaxially εtretched laminateε form more random structures that may interlock better than uniaxially stretched laminates. Placement orientation of the adhesive to the tape backside also plays a significant roll in the observed self-adhesion levels.. The variation in self-adhesive levels obtainable due to the microstructured surface formed, on either the backεide or the adhesive face, will be quite wide due to the great variability in surface structures that one can create in the laminate skin layers, as discussed above. Adhesive thicknesε will alεo play a significant roll in the observed variance of self-adhesion. Thicker adhesiveε will result in lesε or no εelf-adheεion variance due to any surface structure on the adhesive layer face. However, thicker adheεive layerε will tend to flow more into a backεide microεtructure, which is a function of adhesive viεcosity. Thicknesses for thinner adhesives layers capable of forming a surface microstructure will be dependent on the particular microstructure formed. For example, structures, such as those of Fig. 2, with folds having larger peak-to-valley distances and/or greater peak-to-peak distances will be capable of forming adhesive surface εtructureε with thicker adheεive layerε. Further, the relative modulus values for the particular adhesive will be a factor. Generally, an adhesive layer lesε than 30 micronε and preferable leεε than 20 micronε thick εhould be εufficient to form a definite εurface structure. Microstructured adhesive layers will have lower peel values, to any subεtrate, than correεponding flat adhesive layers at moderate application preεεureε. Again, thiε iε due to lower contact between the adheεive and the substrate. This can result in peel values within the range acceptable for a repositionable adheεive formulation, such as those disclosed is U.S. Pat. No. 3,691,140 (Silver) and discuεεed in U.S. Pat. No. 4,684,685 (Shuman et al.). Generally, a 180° peel adheεion from glaεε of leεε than 8 N/25 mm, preferably leεs than 6 N/25 mm is characteristic of a good repositionable adhesive formulation usable with most substrateε. For removable labels, a 180° peel from from glasε of 2.5-6.0 N/25 mm iε most preferred.. For tapes cleanly removable from more delicate substrates, such aε newsprint, a 180° peel from glasε of 0.5 to 2.5 N/25 mm is most preferred. With the invention adhesive tapes, peel values within these ranges are obtainable by varying the adhesive layer thicknesε and the microεtructure of the skin layer(s). By varying these factors, one is able to vary the amount of peak area of the adhesive layer available for contact with a subεtrate. Thiε will affect repositionability as discussed in U.S. Pat. No. 3,857,731 (Merrill et al . ) . As peel values are dependent on thiε available adheεive contact area, other factorε which can affect contact area will alεo influence the repoεitionable character of the microεtructured adhesive. For example, the deformability of the skin layers will affect the amount of peak adhesive surface able to contact a substrate, as more deformable (e.g., softer skin material) fold εtructures will tend to more easily flatten when subjected to higher application pressures. For some tapeε, a microεtructured adheεive layer and/or a nonadhesive coated microstructured backside can function as a mechanical low adhesion backsize. For some tapes wound as a roll, this characteristic would be dependent on wind-up tension. A tape could thuε be wound at a low windup tenεion and be readily removed by the use without the need of a chemical backsize coating. The sam tape could then be applied by the user at a higher pressure and exhibit significantly higher self-adheεion values. This is an advantage over conventional backsizes which do not allow such wide adhesive level variability. Conventional backsized tapes exhibit relatively low self-adheεion regardleεs of the rolldown pressure. High self-adheεion iε a εignificant advantage for tapeε which are wound over themεelveε when used, εuch aε inεulating tape, medical tape, or the like, aε diεcuεsed in U.S. Pat. No. 3,379,562. However, high self-adhesion is incompatible with forming the tape as a roll which is able to unwind. Even activated tapes with high levels of adhesion (e.g., at zero peel angles) to a particular subεtrate can be removed. The high level of extensibility available with most invention tape conεtructionε optionally coupled with the variability in adheεiveness caused by the microstructuring allows tapes with otherwise permanent adhesive peel levels to be removed. When stretched the tapes will tend to incrementally release at the leading edge of tape contact where the tape is being incrementally stretched. This leading edge release zone will travel incrementally down the tape until it is released from its εubεtrate. Many constructions of the invention adhesive tape can also be used as tamper indicating sealing tapes, which will indicate tampering due to the ability of the tape to change form. For example, as cast unactivated laminate tape can indicate tampering by at least three mechanisms. First, it can stretch and indicate tampering by, e.g., a change in opacity. Second, for tapeε which have low adhesion between the skin and core layerε, stretching will cause the layers to dela inate, again indicating tampering. Third, cast laminates can be formed which have relatively thick and/or rigid skinε which will cause the laminate to tear or break up the εkin. Thinner tape backingε will tend to more eaεily εtretch and indicate tampering by the firεt mechaniεm. The actual caliper required for a particular tamper indicating application will depend on the force neceεsary to remove or tamper with the tape on the particular package. Generally, the thinner the overall laminate tape thickness, the more sensitive it will be to tampering by any of the above three mechanisms. Even the activated tape can be tamper-indicating in some instanceε, as when it is stretched, it will change its opacity value. This change in optical properties can also be taken advantage of by coloring the layers different colors. The change in skin morphology and possibly skin/core contact mechanism can change the additive effect (i.e., a color change in the overall laminate) of the multicolored layers. Further, with certain activated tapes, low adheεion between the εkin and core can be uεed to indicate tampering by delamination. For example, the peel force of tape removal for some tape conεtructionε will cause the skin layer to delaminate. With certain constructions, the microtextured skin layers may tend to delaminate and/or the underlying elastomer may tend to degrade over time. This tendency iε particularly problematic with ABA block copolymers. Residual stress created during the stretching and recovery stepε of activating the material to its elaεtomeric form can accelerate this process significantly. For thoεe constructions prone to such degradation or delamination, a brief relaxing or annealing treatment following activation may be deεirable. The annealing would generally be above the glass transition point temperature (T ) of the elastomer, above the B block T for ABA block copolymers, but below the skin polymer melting point. A lower annealing temperature is generally εufficient. The annealing will generally be for longer than 0.1 seconds, depending on the annealing temperature. With commercial ABA block copolymers (e.g., Kraton™ 1107), an annealing or relaxing temperature of about 75°C is found to be sufficient. The laminate tape formed in accordance with the above description of the invention will find numerous use due to the highly desirable properties obtainable. For example, the microtexture gives the elastomeric laminate tape backing a soft and εilky feel. The tape can further be non-necking. Thiε renders the elastomeric laminate tape particularly well suited for a variety of commercially important useε as an elasticizing element particularly in the garment area, where elaεtic webs are used in areas to engage or encircle a body portion alone or as part of a garment. Examples of εuch garmentε include disposable diapers, adult incontinence garments, εhower caps, surgical gowns, hats and bootieε, disposable pajamas, athletic wrapε, clean room garmentε, head bands for capε or visors or the like, ankle bands (e.g., pant cuff protectors), wrist bands, and the like. Removability characteristicε of the tape make it useful as temporary tape, removable label stock, temporary note pads or the like. With labels, it is often useful to provide a non-adhesive coated strip to permit gripping the label for removal. Writability improvements from microtexturing also make the activated laminate tape well suited for label stock and the like. The laminate tape can be extensively used in disposable diapers, for example, aε a waistband, located in either the front or side portions of the diaper at waist level, as leg elaεtic, aε a εoft outer cover sheet or in adjuεtable εlip-on diapers, where the elastomeric laminate could be used as, or in, side panels around the hip that create a tight fitting garment or as a fastening tab. The laminate tapes can be applied as continuous or intermittent lengths by conventional methods. When applied, a particular advantage of the laminate tape is the ability to use thin elastomers with high stretch ratios. This creates a great deal of gathering or shirr when applied to the garment when stretched, which gives the shirred portion a cushion-like feel. Garments often are shirred to give a εnug fit. Thiε εhirring can be eaεily obtained by applying the laminate while in an unstable stretched condition and then affecting the shirr by application of heat. The elastomeric laminate can be adhered to the garment by ultrasonic welding, heat sealing and adhesiveε by conventional methodε. The controlled relaxation obtainable by adjusting the layer ratios, stretch ratio and direction, and layer composition makes the elaεtomeric tape of the invention well εuited to high εpeed production processeε where heat activated recovery can be controlled eaεily by hot fluidε εuch aε hot air, microwaves, UV radiation, gamma rays, friction generated heat and infrared radiation. With microwaves, additives, εuch aε nickle powder, aluminum flakeε and iron whiεkerε, may be needed to ensure softening of the skin to effect skin controlled recovery. The counter-balancing of the elastic modulus of the elaεtomeric layer and the deformation reεiεtance of the εkin layer alεo modifieε the εtress-εtrain characteristics of the laminate tape. This alεo can be modified to provide greater wearer comfort when the laminate tape is used in a garment. For example, a relatively constant εtreεε-εtrain curve can be achieved. Thiε relatively conεtant εtreεs-strain curve can also be designed to exhibit a sharp increase in modulus at a predetermined stretch percent, i.e., the point at which the εkin waε permanently deformed when activated aε shown in Fig. 5, line Y. Prior to activation, the laminate iε relatively rigid, line Z of Fig. 5, i.e., having a high modulus imparted due to the skin layer. The non-activate or non-stretched laminate is easier to handle and much better suited to high speed production processes than would be a conventional elastic. To achieve these benefits, the skin can be either an inner layer, an outer layer or both. In Fig. 5, line ZZ is the skin alone and line X is the elastomeric layer alone. The elastomeric laminate tape is well suited for use as a repositionable tape, wrapping tape, insulating tape, label stock or general purpose tape. The heat shrink character of the tape can also render it suitable for heat shrink applicationε, particularly in view of the conformable nature of the tape. The tape haε the advantage of the ability to form a natural LAB, ink receptivity, mechanical adheεive priming and variable adhesive levels. The elastomeric laminate tape wi.ll also easily electrostatically charge when rubbed. This ability, coupled with the enclosed spaces, makes sheets of the microstructured laminate tapes useful as duεt wipeε, or aε duεt mats (e.g., in a clean room). Further, the polymer skin will often attract and store oils. The tapes could be formed into a multitude of stacked sheets, and as they are removable, could be removed when used to expose an underlying clean sheet. The following Examples are provided to illustrate presently contemplated preferred embodiments and the best mode for practicing the invention, but are not intended to be limiting thereof. Examples 1-32 are illustrations of laminates suitable for use as backings for the invention adhesive tapes. EXAMPLE 1 A five-layer laminate was prepared from two outer layers of 5.08 cm by 5.08 cm, 2000 molecular weight polystyrene and two layers of 5.08 cm by 5.08 cm of 2 mil (0.0508 mm) thick linear low density polyethylene (LLDPE) film (Dow™ 61800, Dow Chemical Corp., Midland, MI) and a core layer of 5.08 cm by 5.08 cm of 125 mil (3.175 mm) thick εtyrene-isoprene-styrene (SIS) film (Kraton™ 1107, available from Shell Chemical Company, Belpre, OH) by heating at 160°C under 2000 pounds per εquare inch (140 kilogramε per εquare cm) of a flat preεε. The resulting film laminate was about 5 mil (0.127 mm) thick. The poly¬ styrene layerε were a processing aid to help form a uniform layered film. The thin brittle polystyrene layerε of the laminate were peeled away, and a clear film re¬ mained. After stretching the clear film by hand to 500%, and allowing it to recover, a smooth and pleasing surface was observed with the naked eye, and surprisingly, exami¬ nation under a microscope discloεed a continuouε, deeply textured, microεtructured surface. Since this sample was uniaxially stretched, fine ridges were observed, oriented transverεely to the εtretch direction, εaid ridgeε having a height to width ratio of about 2 to 1. EXAMPLE 2 A continuouε coextruεion was carried out to prepare a three-layer laminate with two outer skin layers of LLDPE and a core layer of SIS using polymers aε deεcribed in Example 1. Three laminates of 8.5, 4.7, and 3 mil (215, 120 and 78 microns) thicknesε were prepared uεing a Rheotec™ (Rheotec Extruder Co., Verona, NJ) extruder to feed the SIS layer from a tee union into the center of a cross union and a Berlyn™ (Berlyn Corp., Worchester, Masε) extruder was uεed to feed the two LLDPE layers into the two opposite εideε of the croεs union and then the three laminated layers of film were drawn from the 425°F (218°C) die in widths of 18 inches (45.7 cm). The laminateε had skin/core εkin thickneεεeε in microns of 20/175/20, 16/90/14 and 10/60/8, respectively, determined under a light microscope. After the film was stretched past the elaεtic limit of the outer εkin layerε, it deformed and demonstrated a microεtructured surface upon recovery. When initially uniaxially stretched about 500%, these laminates necked down, width wise, to about 40% of their unstretched width. Upon εubεequent reεtretching to about 500%, the films surpriεingly necked down very little, aε shown in Table I. TABLE I The films thus essentially remained constant in width after initial stretching. Not all stretched films will show this non-necking property. The non-necking is a property of the unique unfolding of the stretched surface layers of the present invention, and is a function of the εkin thickneεs and modulus, i.e., strength. This strength must be high enough to prevent width contraction of the core layer upon re-stretching. That is, it iε a balance of εkin and core forces. Very soft or very thin skinned materials, therefore, need to be thicker for the laminate to possess this property. EXAMPLE 3 A continuous coextrusion waε carried out to prepare three-layer laminateε with two outer layerε of polypropylene and a core elastomeric layer of a εtyrene-isoprene-styrene block copolymer. A 2 inch (5.1 cm) screw diameter Berlyn™ extruder was used to feed the elastomer (Kraton™ 1107, Shell Chemical Company, Beaupre, OH) and a Brabender™ 1.25 inch (3.18 cm) screw diameter extruder (available from C. W. Brabender Instrumentε, Inc., NJ) was used to feed the two polypropylene (Escorene™ 3085, available from Exxon Corporation, Houston, TX) layers into the Cloeren™ (Cloeren Co., Orange, TX) feedblock, and were extruded through a single manifold 18 inch(46 cm) wide film die. The film was cast onto a 60°F (16°C) cast roll at 14.7 ft/min (509 cm/min) at varying total caliper as described in Table II. Films of varying outer layer thickneεε were prepared. The filmε were teεted for relaxation by initially uniaxially stretching each sample by hand to just short of its breaking point, which was generally about 650%, releasing the sample, and obεerving any recovery. Recovery after initial draw was then categorized as instantaneouε recovery (I), εlow recovery with time (T), heat required for recovery (H) and permanent deformation (P), i.e. no εignificant recovery. Results are shown in the following table. The texture of the laminate is evaluated both visually and by touch after recovery and claεεified as fine (F), medium (M), coarεe (C) or smooth (no texture discerned). The texture was also measured objectively in εampleε B, C and E by the periodicity (diεtance between foldε) of the samples. It was noted that aε the regular folds get coarser, they alεo appear larger and more widely spaced. Although the large folds are more subject to having more random peak-to-peak distances, they are still quite regularly spaced. The samples were alεo tested for necking characteristics expressed as % change in width upon restretching of the sample. Although necking was not significant for any of these εampleε, generally, as εkin thickneεε fell and the core-to-εkin thickness ratio rose, necking increased. Periodicity and C.O.F. are also shown for sampleε B, C and D which are both inverεely related to the core/skin thickness ratio. The original C.O.F. for the samples was over 3.8, thus the microtexturing produced a significant overall reduction of C.O.F. EXAMPLE 4 A multilayer laminate waε prepared by laminating cast laminates of polypropylene/Kraton™ 1107/polypropylene prepared as in the previous example. The total thickness of each cast laminate was 2.8 mil (0.062 mm). The core/skin ratio waε 12:1. The laminated laminate waε formed of 6 caεt laminateε in a hot press at 200°C at 140 kilograms per square centimeter pressure for five minutes. The formed film was then cooled in a 21°C water bath. The resulting laminate was 6 mil(0.15 mm) thick and appeared like the cast film but thicker. After εtretching approximately 300% and inεtantaneouε recovery, the film diεplayed a coarεe microtextured skin and microtextured inner skin layers. EXAMPLE 5 A continuous coextrusion was carried out to prepare three-layer laminates with two outer layerε of a 70/30 by weight blend of poly(vinylidene fluoride) (Solef™ 1012, Solvay Co., France) and poly(methyl methacrylate) (V044, Rohm and Haaε Corp., Briεtol PA) and a core layer of Kraton™ 1107. A 2 inch(5.1 cm) diameter BerlynTH screw extruder, at 10 RPM εcrew speed, was used to feed the core layer polymer and a 2 inch(5.1 cm) diameter screw Rheotec™ extruder, at 25 RPM, waε uεed to feed the skin layer polymer blendε into a Cloeren TH feedblock and the melt laminate was extruded through a single manifold die, 18 inches(46 cm) wide (Extruεion Dies, Inc., Chippawa Falls, WI), at 420 to 450°F(215 to 232°C) onto a 78°F(26°C) cast roll at 17.0 or 15.3 revolutionε per minute (RPM), reεpectively. The film laminate thickneεses obtained were 5.5 and 6.0 mil (0.14 and 0.15 mm) with core/skin ratioε of 6:1 and 7.5:1, reεpectively. Both laminateε were stretched 400% and allowed to immediately recover. In each caεe, a laminate with a fine gloεεy microtextured εurface waε obtained. EXAMPLE 6 A continuous coextrusion was carried out to pre¬ pare two distinct three-layer laminates with two outer layers of a 50/50 blend of two polybutyleneε reεinε, Shell™ 0200 and Shell™ 0400, and a core elastomeric layer of Kraton™ 1107. A 2 inch (95.2 cm) diameter screw Berlyn™ extruder was used to feed the Kraton™ 1107 at a screw εpeed of 10 RPM. A 1.25 inch (3.18 cm) diameter Brabender™ εcrew extruder waε uεed to feed the two polybutylene blend layers at screw speeds' of 10 and 12 RPM into a Cloeren™ feed block. The laminates were extruded through a εingle manifold 18 inch (46 cm) wide film die at 430°F (221°C) onto a 60°F (16°C) caεt roll at either 8.8 or 7.6 ft/min (2.7 or 2.3 m/min), maintaining a total caliper of 0.003 incheε (0.076 mm) for both εampleε. Thiε produced two films of varying outer skin thicknesseε with the same total laminate thicknesε. The core/εkin ratios were 13:1 and 5:1, respectively. Also, the same equipment waε run at a Brabender™ extruder εpeed of 35 RPM and a caεt roll εpeed of 8.6 ft/min (2.6 m/min), all other conditionε the εame as above, to give a 0.005 in (0.127 mm) thick laminate (comparative) with thick overall skin layers, and a core/skin ratio of 2.6:1. The texture for each sample waε noted after each laminate was stretched by hand just short of its breaking point, about 4:1, and allowed to recover, the first two runs instantly and the third (comparative) with heat. The textureε were classified as very fine, fine and none Thiε data is shown in Table III below. A continuous coextrusion was carried out to prepare five-layer laminates with two outer layers of linear low density polyethylene, ethylene vinyl acetate tie layers of Elvax™ 260(EVA) (available from Dupont Corporation, Wilmington, DE) and a core elastomer layer of styrene-isσprene-styrene block copolymer. A 2 inch(5.1 cm) εcrew diameter, 4D ratio Berlyn™ extruder was used to feed the elastomer layer (Kraton™ 1107). A Rheotec™ 2 inch(3.18 cm) screw diameter extruder was used to feed the two polyethylene layers, and a 1 inch(2.54 cm) screw diameter 3M-made extruder was used to feed the two Elvax layers into a Cloeren 7 feedblock. The laminates were extruded through a single manifold 18 inch(46 cm) wide film die at 375°F(190°C) onto a 60°F(16°C) caεt roll at varying total caliper or thickneεε aε described in Table IV. Films of varying layer thicknesε were thuε prepared. This example also demonstrates how caεting roll speed affects film thickness. The EVA tie layers add bonding εtrength between the LLDPE outer layerε and the SIS core layer, reεulting in a more durable laminate than such a film without the EVA, yet does not interfere with the way the laminate behaves with respect to surface texture. This tie layer is, of courεe, very thin compared to the other layerε. TABLE IV PROCESSING CONDITIONS FOR SAMPLES CASTING NIPP FILM SUR- + Berlyn™ extruder temperature εame for all εampleε: Zone 1«149°C, Z2-177, Z3-193, Z4=204, Z5-204, Z6-204 ++ Rheotec™ extruder temperature same for all sampleε: Zone 1=110°C, Z2«149, Z3=149, Z4=160 ' 1" (2.54 cm) extruder temperature εame for all runε: Zone 1=143°C, Z2-191, Z3=191 * F=Fine microtexture, MF=medium fine, VF=very fine, SF=super fine, C=coarse Since the extruder conditions were close to constant for all of the above runs, the core thickness to skin thickness ratio will be the same for all of the above runs, approximately 13:1 as will be the core/tie layer ratio at 30:1. Thus, it will be noted that the total film thickness column of Table IV correlates exactly with the surface texture column. The range of values goes from a total film thickness of 1.0 mil(25 micronε) and a texture of εuper fine, to 20.0 mil(508 micronε) and a texture of coarse, all from a stretch of 5:1 and an instantaneous recovery. Thus, it can be seen that the thicker materials give coarser textureε and that by controlling the physical parameters, the texture can be controlled. EXAMPLE 8 A three-layer LLDPE/SIS/LLDPE film was made as in the previous examples using a Berlyn™ extruder with a εcrew εpeed of 20 RPM to feed the Kraton™ 1107, and a Brabender™ extruder with a εcrew εpeed of 17 RPM to feed the Dow Chemical 61800 linear low density polyethylene (LLDPE) to a Cloeren™ feedblock. The laminate was extruded through a single manifold 18 inch(46 cm) wide film die onto a casting roll at 85°F(29°C), and a speed of 13.7 ft/min(4.18 m/min) to give a laminate with a core/skin ratio of 15.6:1 and a total thicknesε of 125 micronε. The film was uniaxially εtretched 4:1 and instantaneouεly recovered, the coefficient of friction of the film was measured from the stretched and recovered film, and compared to the unstretched film. The data iε shown in Table V. MD denotes Machine direction and TD denotes transverεe direction. Sample unstretched MD unstretched TD stretched MD stretched TD This data is indicative of the large drop in the coefficient of friction for the stretched film compared to its unstretched precursor and is also indicative of the unique microtextured surface of laminates of the present invention. EXAMPLE 9 A three-layer laminate of the preεent invention waε made uεing the set-up of Example 8. The Berlyn™ extruder, operating at a screw speed of 10 RPM, was used to feed a polyurethane (Pellethane™ 2102-75A from Dow Chemical) core material. The Brabender™ extruder operating at a εcrew speed of 7 RPM was uεed to feed a blend of Amoco™ 3150B(Amoco oil Co., Chicago IL) high density polyethylene (HDPE) and Kraton™ 1107 in a 95:5 ratio, as the εkin material, to the Cloeren™ feedblock. The small amount of Kraton™ 1107 was added to the skin layer to increase the adhesion of the skin layer to the core layer. The laminate waε extruded through a single manifold, 18 inch(46 cm) wide, film die onto a casting roll at a temperature of 70°F(21°C) and a speed of 21 ft/min(6.4 m/min) to give a 69 micron laminate with a core/skin ratio of 13.7:1. The laminate exhibited a microtextured εurface after stretching 600% and instantaneous recovery. EXAMPLE 10 A three-layer laminate of the present invention was made using the set up of Example 8. The Berlyn™ extruder operating at a screw speed of 60 RPM was uεed to feed a triblock copolymer elastomer of styrene-butadiene-styrene (SBS) (Kraton™ 1101) aε a core material, and a Killion™ (Killion Extruder Co., Cedar Grove, NJ) extruder was used to feed a Dow™ 3010 LLDPE material to a Cloeren™ three layer die. The extrudate was cast upon a caεting roll at a temperature of 85°F(29°C) and a εpeed of 41 ft/min(12.5 meterε/minute ) . The resulting 5 mil(0.127 mm) thick film with a core/skin ratio of 8.9:1 was easily stretched 7.5:1 and upon instantaneouε recovery a fine textured laminate waε formed. EXAMPLE 11 A three-layer laminate of the preεent invention was made using the set up of Example 4, with the Berlyn TM extruder feeding a Kraton™ G 2703 styrene-ethylene butylene-styrene (SEBS) block copolymer at a screw speed of 20 RPM, and the Brabender™ extruder feeding an Exxon™ PP-3014 polypropylene at a screw speed of 5 RPM, to a Cloeren™ feedblock. This material was then extruded through a 18 inch(46 cm) film die onto a casting roll at a temperature of 34°F(1.1°C). The film produced was easily stretched 600% and formed a fine textured surface after it was allowed to recover instantaneouεly. The layer thickneεεeε determined under a light microεcope were 15/162/12 micronε εkin/core/εkin, reεpectively. EXAMPLE 12 This example demonstrateε the uεe of varying εkin and core materialε. In all runε, the line conditionε were identical uεing a Cloeren feedblock at 400°F(204°C) . The core extruder waε the Brabender™ diεcuεεed above with temperatureε in zoneε .1-4 of 178, 210, 210 and 216°C, reεpectively. The die waε at 400°F(204°C) and the casting wheel at 51°F(11°C). TABLE VI CORE SKIN % SHRINK- _# CORE SKIN RATIO STRETCH AGE TEXTURE 12A Kraton™ ELVAX™ 360 9.6 700 I F 1107 12B Kraton -TM" (Polyester) 4.4 600 1107 (Eastabond™ FA-300) 12A in Table VI demonεtrateε that elastomers can be uεed for the skin when a more elastic core iε used and with appropriate stretch for a 115 micron(u) film. 12B demonstrates the use of a polyester skin in a 120 micron film. The laminate designated 12B, despite the relatively large core-to-skin ratio, was of a relatively fine texture and instant shrink recovery. This is due primarily to the low modulus of the polyester (compare to Example 3). FA-300 is available from Eastman Cemicals Co., Kingsport, TN. EXAMPLE 13 Nylon 66 (Vydyne™ 21 of the Monsanto Co., St. Louis, MO), the condensation product of adipic acid and hexamethylene diamine, waε uεed as the skin in accordance with the procedure outlined in Example 8. The core was a SIS (Kraton™ 1107) block copolymer. The nylon and Kraton™ were extruded at 525°F(274°C) and 450°F(232°C) , respectively into a 500°F(260°C) die. A 4 mil(0.1 mm) thick film was formed with a core-to-ratio of 18:1. A microtextured surface formed after a 4:1 stretch and instant recovery. EXAMPLE 14 In order to increase the tackiness of the core and lower core layer modulus and decrease its viεcoεity, a solid tackifying roεin Wingtack™ (Goodyear) was blended with Kraton™ 1107 in ratios of 10/90, 20/80 and 30/70 using the arrangement of the previous example, in 91, 114 and 165 micron filmε, respectively. The die temperature was 380°F(193°C) with the Kraton™ blend fed at a rate of 18.5 pounds/hour( 0.14 kg/min) and the polyethylene skin (LLDPE; Dowlex™ 2500, Dow Chemical Co., Rolling Meadows, ILL) fed at a rate of 6 pounds/hour(2.72 kg/hr). The core-to-skin ratios were 6.2:1. For all three Kraton™ blends, a fine microtextured εurface of the laminate waε obtained when a 6:1 stretch was employed and gave instant shrink recovery. EXAMPLE 15 The relationship between skin thickness and percent stretch to surface texture (measured by periodicity) was explored using a SEBS core (Kraton™ G1657) and a polypropylene skin (Exxon™ 3085). The Berlyn™ extruder was used for the core and the Rheotec™ extruder was used for the skin, fed into a Cloeren™ feedblock. A single-layer drop die was used at 420°F(216°C) , the casting roll operated at 38.9 ft/min(11.9 m/min.) and 50°F(10°C). The reεultε are εhown in Table VII below. TABLE VII AVG. SKIN CORE/ THICKNESS SKIN PERIODICITY SHRINK _ (_μ_) RATIO STRETCH % (_μ ) MECHANISM 15A 14 6 600 29 I 250 56 I 15B 17.5 6.1 550 39 I 350 15C 21 4.4 550 " 46 ' H 350 71 H 15D 20 4.3 550 47 H 300 15E 23 3.7 500 63 H 350 69 H As the stretch percent increaεed for each εample, the periodicity decreaεed indicative of the finer microtexturing obtained. Thiε εhowε that εtretch percent can be uεed to vary the surface structure of the laminate. Further, as skin thicknesε increased, so did the periodicity. In all samples, the core thickneεε was approximately conεtant at 85 μ ' s . Skin thickness on a constant core can thus be directly related to the surface texture obtainable. As can be seen in the above Table IV, for relatively conεtant εtretch % aε the skin thicknesε increaεed so did the periodicity. The thick skinned sampleε thuε produced coarser textureε. Thiε can, of course, be used to manipulate the skin and hence laminate characteristics. EXAMPLE 16 The sample tested was that prepared in Example 8 the stretch ratio was varied from 2:1 to 13:1. TABLE VIII % Area Increase 280 390 530 As can be seen from Table VIII, the relationship between stretch ratio and periodicity demonstrated in Example 15 holds up for thiε LLDPE/SIS/LLDPE laminate. Aε the εtretch ratio increaεeε, the periodicity decreases first rapidly, then slowly in a subεtantially exponential manner. Further, the increase in area increases with an increase in stretch ratio. EXAMPLE 17 The relationεhip between εtretch, core/εkin ratio and shrink mechanism was demonstrated using the procedure of Example 4 and Example 15 for polypropylene/Kraton™ 1657 (SEBS)/polypropylene laminates. The material was εtretched at the rate of 5 cm/εec. and held for 15 secondε. The film waε allowed to shrink for 20 seconds and then heat shrunk in a water bath for 5 seconds at 160°F(71.1°C) . The length of the film after shrink was then compared to the length of the film after the 20 εecond hold period and the length after εtretch to determine the εhrink mechanism in operation. The results of this comparison iε εhown in Table IX below. N = None, H = Heat, S = S ow t me, T = Time, F = Faεt time, I = Inεtant Fast is when more than 15% recovery occurred at 5 seconds. Medium time is where greater than 15% recovery occurred at 20 seconds. Slow time is where greater than 15% recovery was not noted until 60 secondε after εtretch. EXAMPLE 18 Polypropylene (Exxon™ 3145) was added to a Kraton™ 1107 (SIS) elastomer aε a modifier for the core material. The skin used was an Exxon™ 3014 polypropylene (PP). The cores prepared contained 5 and 10 percent Exxon™ 3145 polypropylene by weight. The relationship between stretch, the shrink mechanism and texture was tested. The results are in the following Table. TABLE X Core/Skin Ratio » 6.9, 112 microns thick, 10% PP in Core % Stretch 320 410 510 590 Shrink Mechanism None None Heat Heat Texture - - Coarse Coarse Core/Skin Ratio = 8.0, 125 microns thick, 10% PP in Core % Stretch 280 380 480 570 shrink Mechanism None None Heat Heat Texture - - Coarse Coarse Core/Skin Ratio « 8.8, 84 microns thick, 5% PP in Core % Stretch 270 320 400 500 590 Shrink Mechanism Heat Heat Heat Slow Faεt Time Time Texture Coarεe Coarεe Coarse Med Fine As can be seen, the addition of PP to the core decreaseε the shrinkability of the laminate. The polypropylene appears to reduce the elasticity of the core thereby permitting the restraining forces of the skin to more easily dominate the elastic strain imposed by the deformed elastic core. EXAMPLE 19 The effect of adding a stiffening aid, polystyrene, to an elastomeric core material waε teεted. The εkin compriεed a linear low denεity polyethylene (Dowlex™ 6806). The core waε a blend of SIS (Kraton™ 1107) and polyεtyrene (500PI or 685W, both from Dow Chemical Co.). All samples were of a 3-layer construction (skin/core/skin) with a total thickness of 4.5 mil(0.11 mm) and a core/skin ratio of 8:1. All εampleε were then stretched 400% and instantaneously recovered. Tensile curves were then generated which demonstrated that the laminates became stiffer with increaεing polyεtyrene content (aε shown in Fig. 9 (T-N), εhown alεo in the following Table XI. TABLE XI SAMPLE # % P.S. (Type ) 5% YOUNGS MODULUS(kg/cm, ) 19A(T) 0 11.5 19B(S) 10 (500 PI) 20.7 19C(R) 30 (500 PI) 29.4 19D(P) 40 (685 W) 68.6 19E(N) 50 (685 W) 188.4 EXAMPLE 20 In thiε example, the effect of the addition of Wingtack™ tackifier to the core elastomer waε inveεtigated. The laminate material of Example 14 waε compared to a 3-layer laminate (20) compriεing LLDPE/Kraton™ 1107/LLDPE. Both εampleε were 4 mil(0.10 mm) in total thickneεε with core/skin ratios of approximately 8:1. These materials were of the instant shrink type when εtretched from 4:1 to 13:1. TABLE XII EXAMPLE 5% YOUNGS MODULUS 20 (Comp) 109 kg/sq.cm. 14 47.9 Aε can be εeen from Table XII, the uεe of a viscoεity reducing aid/tackifier has the opposite affect as the addition of a polystyrene εtiffening aid. EXAMPLE 21 A two-layer laminate of a core and one skin layer was formed of Kraton™ 1107 (SIS)/Exxon™ polypropylene 3014. A Berlyn™ extruder operating at 6 RPM was uεed with the polypropylene and a Killion™ extruder operating at 125 RPM was used for the Kraton™ . The polymers were fed to an 18 inch(45.7 cm) 440°F(227°C) Cloeren™ die with one manifold shut down. The resulting film was cast on a roll at 60°C and rotating at 35.2 RPM. The laminate formed was 2 mil(0.051 mm) thick with a core/skin ratio of 2.5:1 and exhibited a coarεe microtexture when stretched 5:1 and allowed. to recover instantly. Necking on subεequent reεtretching waε only 2.5%. EXAMPLE 22 A laminate was formed having skins of different compositions. The elastic core was Kraton TM 1107 with one polyethylene (Dow TM LLDPE 61800) and one polypropylene (Exxon TM 3085) skin. The core was extruded with a Berlyn TM extruder, while the εkinε were extruded with Rheotec . M and Brabender extruders, respectively. The Cloeren die was at 350°F(177°C) and the casting roll at 60°F(16°C). Two films were formed. For the first, the extruders operated at 20, 8 and 26 RMP'ε, respectively, while the caεt roll operated at 17.3 RPM to form laminates with core/skin ratios of 18:1. The sample formed was instant shrink at a 5:1 εtretch, with a fine microtexture. For the second film, the extruders and cast roll operated at 10, 16, 26 and 14.2 RMP'ε, reεpectively, to form a laminate with a core/skin ratio of 18:1. The second laminate waε alεo inεtant shrink at 5:1 stretch yet exhibited coarse surface texture. Both laminated were 4.0 mil(0.1 mm) thick. EXAMPLE 23 The laminate tape backing of Example 16 was stretched in a first direction by 8:1 and sequentially in a cross direction by 4:1. This laminate was of the instant shrink type. EXAMPLE 24 The laminate of Example 3A was stretched in one first direction at 4:1 and sequentially in a cross direction by 4:1. This laminate was of the instant shrink type. The texture formed is shown in Fig. 10. EXAMPLE 25 The laminate of 3A waε stretched simultaneously biaxially at 4:1 by 4:1. The laminate recovered instantly. The core/skin thickness of unstretched laminate waε 90/5 micronε, reεpectively. EXAMPLE 26 A three-layer laminate of polypropylene/SEBS(Kraton™ 1657 )/polypropylene uεed in Example 17 was tested for writability. The core/skin ratio waε 5:1 with a total laminate thickneεs of 5 mil(0.13 mm). The film was stretched to 5:1 and allowed to recover. The writability before and after stretching is shown in Figs. 7 and 8, reεpectively. EXAMPLE 27 A series of LLDPE/SIS/LLDPE laminates were compared for their non-necking characteriεticε, aε εhown in Table XIII below. The firεt 3 exampleε are from Example 2, and SIS waε alεo teεted for compariεon purpoεeε. As the C/S ratio and stretch ratios rose, the problems with necking increased. EXAMPLE 28 The uεe of adheεive coreε waε demonεtrated. Firεt a copolymer of isooctyl acrylate (IOA) and acrylic acid (AA) in monomer ratios of (90/10) was uεed aε a core with polypropylene (Exxon™ 3014) and PET (intrinεic viεcoεity 0.62) as the skinε in the firεt two exampleε. The IOA/AA copolymer waε prepared in accordance with U.S. Patent No. 4,181,752. The core/εkin ratioε and total thickneεses were 20 and 10, and 22 mil(0.56 mm) and 6 mil(0.15 mm) before lamination for the PP and PET examples, respectively. The laminates were cured for 5 minutes uεing a 15 watt UV light to cure the coreε. The PP skin embodiment waε an inεtant εhrink at 500% stretch while the PET εkin embodiment waε a heat εhrink laminate at 400% εtretch. PET was also used as a skin layer for a Kraton™ 1107 (56 parts) Wingtack Plus™ (35 parts) and Wingtack™ 10 (9 parts) core with a core/skin ratio of 83:1 and a total thickneεε of 25.6 mil(0.65 mm) before lamination. Thiε laminate was of the instant εhrink type at 400% stretch. EXAMPLE 29 This example demonstrates skin controlled relaxation in the heat shrink region and control of the heat shrink mechanism by % elongation and core/skin ratio. A εerieε of 5 mil(0.12 mm) laminateε were made with a core of Kraton™ 1107 (89 partε) poly(alpha-methyl)εtyrene (10 partε) and Irganox™ (Ciba-Geigy Corp., Hawthorne NY) (1 part-antioxidant) . The skins were polypropylene (Exxon™ 3085). A Berlyn™ extruder was used for the core and Rheotec™ extruders for the skin uεing a Cloeren™ 3 layer feedblock and a 18 inches(45.7 cm) film die. The cast wheel temperature was 80°F(27°C) with the speed determined by the core/skin (C/S) ratio and the εkin extruder speed. The shrink mechanism as a function of C/S ratio and % stretch is shown in Fig. 12. Fast is when more than 15% recovery occurred at 5 seconds. Medium time is where greater than 15% recovery occurred at 20 seconds. Slow time is where greater than 15% recovery was not noted until 60 seconds after stretch. Skin control of the temperature of activation for the heat shrink material is demonstrated in Fig. 13. The temperature of activation is defined aε the temperature required to achieve 50% or 90% of the recovery obtainable. Lineε V and W repreεent samples with core/skin ratios of 4.71 and 4.11, respectively. Aε is seen, as the core/skin ratio went down the temperature of activation (both T a _ 90 and T a _ 50 ) went up, indicating a skin controlled relaxation. In this Figure, the 100% value is defined as the % εhrinkage at 160°F(71°C), which for moεt practical purpoεeε waε the upper limit of available recovery. The pointε below 80°F(27°C) are the amountε of preactivation εhrinkage for each example. Three samples were also tested to measure the increase in opacity from the unstretched clear film aε seen in Table XIV below. TABLE XIV * The core had a 1/2% blue pigment. EXAMPLE 30 A foamed core three-layer film was made. The skins were Dow™ LLDPE 6806 and the core was 99.5% Kraton™ 1107 with 0.5% AZNP 130 blowing agent (Uniroyal Chemical Co., Naugatuck, Conn). Total film thicknesε waε 20 mil(0.5 mm). The skins were 2.0 mil(0.05 mm) thick each. The foamed core specific gravity was 0.65 as compared to unfoamed Kraton™ specific gravity of 0.92. A three-layer coextrusion die was used. This was an instant εhrink εheet exhibiting a coarεe texture at about 300% stretch. EXAMPLE 31 The film from Example 2 with a core/εkin ratio of 6:1 was characterized for its unstretched and stretched modulus value, the reεultε of which are εhown in Fig. 5; X iε the Kraton™ 1107 elaεtomer alone, ZZ iε the polyethylene skin alone, Z iε the laminate as cast and Y is the laminate after stretching to 500% and recovery. EXAMPLE 32 The film laminate of certain examples were examined to determined the contact mechaniεm between the skin and core layers. The stretched and activated sampleε were cut with a razor blade on a hard surface. The sampleε were then examined at the cut edgeε with a εcanning electron microεcope. The core/skin contact waε then determined viεually with the reεults summarized in Table XV below. TABLE XV Stretch Ex Compoεition Ratio Commentε 5 PVDF+PMMA/SIS/PVDF+ PMMA 2, Elaεtic coheεive failure 6 PB/SIS/PB 3 Elaεtic coheεive failure 7 PE/EVA/SIS/EVA/PE 5 Adhesive failure 12A EVA/SIS/EVA 4 Adhesive failure 12B FA300/SIS/FA300 7 Adheεive failure 19E PE/SIS+PS/PE 3 Some voidε ' 8 LLDPE/SIS/LLDPE 3 Filled 5 Filled 7 Filled 15A PP/SEBS/PP 4 Filled 15C PP/SEBS/PP 5. Elaεtic coheεive failure A PP/SIS/PP 5, Filled New sample A correεpondε to Example 29. Sample A had approximately the caliper of the Example 29 εampleε with a core/εkin ratio of 5.1 and was a heat shrink laminate. COMPARATIVE EXAMPLE 1 A three-layer film of Dow™ LLDPE 2517 (Polyethylene)/Pebax™ (Autochem Co, France) 3533/LLDPE 2417 waε made. The film was formed by presεing three precursor films together at 400°F(204°C) and about 2000 pounds of presεure(140 kg/εq.cm) for 5 minuteε. The film formed waε 5 mil(0.13 mm) thick with a core/εkin ratio of 12.7. The laminate waε εtretched 400% (from 1 to 5 cm). The stretched laminate then contracted to 3.2 cm (36% of stretched length) at room temperature. The relaxed laminate was then heat shrunk by 180°F(82°C) air and it contracted to 1.5 cm (53% of relaxed length). An edge of the sample was then cut and observed for microtexturing. No folds were observed at lOOOx magnification. Microscopic bumps, probably formed by recompression of the cover layer, and skin delamination was observed. The C.O.F. and opacity for the cast laminate was 0.901 and 2.77% while that for the relaxed activated laminate was 0.831 and 12.4%, respectively. EXAMPLE 33 The tape constructionε described in Table XVI were prepared with the laminate backing produced in accordance with the above described coextrusion techniques with the adhesive layer applied as diεcloεed. Adhesive wa applied to the polypropylene side of the laminate. These tapes were then tested for properties such aε peel from glass, peel from a microtextured tape backing (e.g., from itself), writability and conformability. Conformability is a test of the force necessary for a εubεtrate to deform into a curved εurface uεing a matching bar. Conformability waε teεted uεing a Handle-O-Meter™ (Model 210) available from Thwing-Albert Instrument Company, Philadelphia, Pennsylvania. The test was run with the film parallel with the slot in the machin direction (M.D.) of the film and the cross direction of th film. The film width in both caseε waε 4 inches(10.26 cm) and the slot width waε set at 1/4 inch(0.635 cm). The test was run with unεtretched laminate, laminate uniaxially stretched and recovered in the M.D. and laminated biaxially stretched and recovered in the M.D. and CD. As summarized in Table XVIII, conformability is the force necessary to force the laminate fully into the slot with a corresponding bar. For uniaxially (M.D.) stretched films the formation of microstructure generally made the laminate more conformable to deformation in the machine direction yet reinforced the laminate to deformation in the cross direction (CD.), i.e., made it more rigid. The result iε a laminate having highly aεymmetrical conformability. Thiε is useful for a tape that iε to be attached to a εurface with a two dimenεional curve (e.g., a pipe) where conformability in the flat direction is unneeded or undesirable. For a multiaxially stretched laminate, conformability increaseε in both the M.D. and CD. The peel teεts from glass and from the tape backεize were both performed according to ASTM 180° Peel Teεt D 3330-87 as reported in Table XVII. Dispoεable glaεε εlides cleaned with ethyl acetate were used once for each reading. The tapeε in the backεize teεt were placed M.D. to M.D. A 5 lb(2.3 kg) roller was used to adhere the tapeε, with one paεε at 90 in/min(2.3 m/min) with a 1 min dwell time. The tape was then attached to the jaw of an adhesion testing machine with a lower platen εpeed of 2.3 meterε/min (90 in/ in). Two εecond average readings were taken. In Table XVIII, the numbers in parenthesis are readhesion tests, where the sample originally peel tested iε readhered and reteεted for peel. Writability waε determined viεually on a εcale of poor (P), fair (F), good (G), very good (VG) , and excellent (E). The ink waε a water-baεed compoεition from a broad tip pen applied at normal hand pressure. Poor (P) writability indicates that the ink beaded immediately and easily wiped off the surface. Fair (F) indicates that the ink beaded up over time and could be partially wiped off. Good (G) indicates that the ink could not be wiped off, bu that there was some blurring of the lines drawn. Very goo (VG) indicates that ink could not be wiped off and that only a small amount of blurring occurred. Excellent (E) indicates that the ink could not be wiped off and that there was no perceivable blurring of the lines. Writability appeared to clearly improve with uniaxial stretching and even more so with biaxial stretching. Readheεion peel tests are second peel tests run on the same tape sample used in the first corresponding test. Thiε iε a meaεure of the repositionability of the tape. The εhrink mechanism, repositionability, and tamper indication mechanism of each tape sample is discloεed in Table XIX. •fCaCO j contaminant TABLE XVI cent... EXP CORE SKIN TIE ADHESIVE No. Comp. Thick Coinp. Thick Comp. Thick Coat Comp. Thick Q 55.0 EVA 260 10.0 III Y 37.5 10.0 R 50.0 PP 3085 5.0 XII V 55.0 5.0 S 80% PU-2352 65.0 PP 65F54 10.0 III Y 37.5 -70A and 20% EVA 40 T Kraton ,τ"κ 1107 150.0 50% PP 4092 and 50% Mineral Oil U 55.0 PS 685-26W V P.U.2102-75A 75.0 P.E. 3150B 5% Kraton T 1 H" 1107 W Kraton™ 1107 227.5 PE 2517 PANS 18-210; Polyalphamethylstyrene 18-210 from Amoco, Chicago, IL. Polyethylene 3520 and 3150B; available from Amoco, Chicago, IL. EVA 260_and 40W; ethylenevinylacetate from E.I. DuPont de Nemours Co., Wilmington, DE. P.S. 685-26W; polystyrene 685-26W available from Dow Chemical Co., Midland, HI. P.E. 30107^1800 . 6806, and 2517; polyethylene from Dow Chemical Co., Midland, MI. PP (polypropylene) 65F53 and 65F54; available from Himont U.S.A., Inc., Wilmington, DE. polypropylene 15486; available from Charles B. Edwards, Minneapolis, MN PB 0200 and 0400; polybutylene availalbe from Shell Chemical Co. Sol ay τ " 1008; polyvinylidene luoride available from Soltex Polymer Corp., Houston TX PMMA; VMiOO poly ethylmethacrylate available from Rohm & Haas, Philadelphia, PA. Polyester FA300; available from Eastman Chemical Products, Inc., Kingsford, TN. PU 2352-70A; polyurethane available from DuPont PP 3085 aru-t 4092; available from Exxon Chemical Co. X : 40% isooctyl acrylate-acrylic acid (IOA-AA) 95.5/4.5 and 60% Foral™ 85, Hercules, Wilmington, Del. Y : 3M 9671SL, available from 3M Corp., St. Paul, MN. Z : 50% Kraton™ 1107 and 50% Wingtack Extra with antioxidants W : IOA-AA (94.5-5.5) V : 96% IOA-AA (90-10) and 4% Irgacure 651, Ciba Geigy Corp. Hawthorne, NJ I : solvent coat from a solution of two parts heptane to 1 part isopropyl alcohol onto the cast film II : laminate to stretched film III : laminate to cast film IV : hot melt coat at 350°F (177°C) X : coextrusion XI : laminate to microtextured film XII : coated onto cast film and U.V. cured for 5 min. at 15 watts XIII : solvent coat microtextured film from 2 parts heptane to 1 part IPA In Table XV of the solvent coated samples, sample I was dried in 90°F oven for 1 min. All other solvent coated samples (A-D, F, L, O and T) were dried at room temperature for 24 hours. TABLE XVII cont... 180° Peel from Glass (N 25mm) 180° Peel from Backside (N/25ran) Sample Draw As Cast Uniaxed Biaxed As Cast uniaxed Biaxed Number Ratio Peel Peel Peel ϊ Peel _Peel Peel 0 2.69B U 0 0.14D V 4.0 12.35D W 7.0 1.45 (1.71) 0.29 (0.27) 0.16 0.17 D : delaminate AT : adhesive transfer B : breaks TABLE XVIII Water Based Exp Ink Conformability (grams) I Writability Cast MD Cast CD UMD UCD BHD BCD U B A P F B P F VG 146 17 D F G H I P VG 15 J P VG 29 10 P F L P G 19 25 12 H P G 0 P G 158 44 P P VG 19 8 T w VG VG 517 100 137 61 RΞPOSITIONABir-ITΪ y n π n fl n If J " K " n " " π M « " n JJ n if n Q n n " p if II π Q « II n R n " n S " delaminate N T " tear N U " delaminate N Y n π IT W " derimple Y EXAMPLE 34 Sample I of Example 33 was further tested for peel adhesion at 90° and 0° as shown in Table XX. When th tape was removed from glass, it partially stretched with a 90° peel and fully stretched (i.e., to its natural draw) with a 0° peel. Generally, the 90° peel was less than the corresponding 180° peel except it was significantly higher for the biaxial peel from glasε and slightly higher for th peel from backside test. It is believed the low 180° peel for biaxially stretched film is due primarily to the fine texture and high surface area that is formed with the sample. This will result in a low contact surface to glass at moderate rolldown pressures. In contrast, the microstructured backside will tend to intermesh with the microtextured adhesive layer and correspondingly will yield a higher peel from itself. It is believed that this intermeshing of microstructures iε also responsible for the comparatively high peel from backsize values for both 90° and particularly 0°. Table XX Peel (N/25mm) From Glass 1 90° 1 All peel values are in Newtons/25 mm The tape stretched slightly when removed the first time 3 TThhee ttaappee ffuullllyy stretched when removed the first time 4 The tape broke EXAMPLE 35 Samples I and W were further peeled tested at 0°, 90° and 180° varying the rolldown force used to adhere the tape to the substrate from which it was peeled. The same ASTM test as described in Example 33, using a IMASS™ 3M90( available from IMASS Inc., Hingham, MASS). However, tape was applied and tested first with a 5 lb(2.3 Kg) roller at 90 in/min(2.3 m/min) with only one pass and teεted second with a 10 lb(4.5 Kg) rolldown. The results in Newtons/25 mm are shown in Table XX. The tapes of sampleε A, B, C and D were prepared using the laminate backings of samples I and W of Example 32 for (A and B) and (C and D), respectively. The adheεive system applied was X of Example 32 applied by solvent coating in a solution of two parts heptane and one part isopropyl-alcohol. Samples A and C had an adheεive layer thickness of 22.2μ, while that for sample B and D was Again, a wide variation in adhesive values were obtained for the stretched and activated tape lamination. The variations are due to the microεtructure formed and final adhesive layer thicknesε. All the εampleε were solvent-coated and dried at room temperature for 24 hours. However, one generally noted trend is that the relative increase in peel was much higher for activated tape than that for cast tapes when the rolldown pressure was increased (excluding the caseε where there waε adheεive tranεfer(AT) or delamination(D) ) . C on C 0.3 0.4 1.1 1.0 0.2 0.5 0.6 0.8 0.06 0.4 0.2 0.2 Cast >18.2 Broke 0.9 1.2 2.3 2.4 Uniax 14.4 16.3 2.3 3.4 4.9 5.1 Biax 13.0 17.2 3.5 4.4 3.1 4.5 EXAMPLE 36 Laminate tape backings with polystyrene were made in accordance with the procedures outlined in the above examples. The skinε compriεed polypropylene (Exxon™ 3014) with a Kraton™ 1107 based core for a three layer construction. Sample A had no polystyrene in the core, while samples B, C and D had 20%, 35% and 50% polystyrene (Dow Chemical Co. 685W) , respectively. All had core/skin ratioε of approximately 7:1. The tape laminateε were laminated with a 1 mil acrylic adheεive (RD-975 - available from 3M Co.). The εampleε were tested for 0° peel from glasε uεing the procedureε outlined above. However, the rolldown waε once with a 5 lb(2.27 kg) roller, and teεting waε performed on an IMASS™ 3M90 Peel Teεter. The peel was tested with the aε caεt tape laminate, and then with readheεion of the εame tape a second and third time. Each measurement is an average of three test runs. The readhered runs 2 and 3, as shown in Table XXII, have significantly lower peel values particularly at low polystyrene content. This indicates the degree of stretch activation initiated in the prior 0 o peel test. Table XXII Sample Thickness 0° Peel(l) 0° Peel(2) 0° Peel(3) Number mils(mm) N/25mm N/25mm N/25mm A 3.5(0.089) 13.0 6.6 6.16 B 4.1(0.104) 16.0 7.71 7.95 C 4.1(0.104) 21.4 21.0 15.5 D 4.3(0.109) 26.7 26.4 22.3 The percent stretch, here the percent increaεe in length over that of the original sample, and percent recovery, of the stretched length, for each peel are set forth in Table XXIII. Table XXIII Sample First Peel Second Peel Third Peel Number Stretch |Recovery Stretch|Recovery Stretch |Recovery A 645% 89.5% 645% 89.5% 645% 89.5% B 485% 89.7% 485% 89.7% 485% 89.7% C 330% 79.5% 430% 72% 430% 72.0% D 250% 58.0% 270% 59.3% 270% 59.3% EXAMPLE 37 The tape of Example 33, sample E, was stretched to itε ultimate draw ratio. The tape waε allowed to immediately recover. The tape waε then cut on edge and iε εhown in Fig. 17. EXAMPLE 38 A tape with a Kraton™ 1107 core and polypropylene εkins (PP3085) waε laminated with an acrylate adheεive 3M 9458, available from 3M Corporation, St. Paul, MN. The original adhesive was 1 mil(25.4 μ ) thick. The tape was stretched to its ultimate draw ratio with the results shown in Fig. 16. EXAMPLE 39 A sample having the layer composition of Example 27 (with 1% blue pigment in the core) was formed with an overall caliper of 3.0 mil(0.076 mm) and a core/skin ratio of 5.1:1. The film waε caεt onto a chrome caεting wheel with a rubber nip. The 60° gloεε waε meaεured using ASTM D 2457-70 using a Gardner Instrumentε(Betheεda, MD) 60° gloεs tester. The results are summarized in Table XXIV below for the as cast and three microtextured filmε (with different εtretch rateε) . Aε Cast Chrome Side EXAMPLE 40 Laminates from Example 32 were tested for layer adhesion using a variation of 180° peel test ASTM D 3330-87. Laminate (0.75 in, 1.9 cm) was placed between two pieceε of masking tape (3M-2503, available from 3M Co., St. Paul, MN) of the same width. Tabs of one tape piece were adhered to the peel tester platen with additional pieceε of masking tape. The three layers were presεed together with four paεεeε of a 5 pound(2.3 Kg) roller and allowed to sit for 10 minutes. The leading edge of the upper piece of masking tape was attached to the jaws of a peel tester leaving 0.5 in(1.27 cm) of maεking tape to masking tape contact at the leading edge. The peel tester was run at 90 in(228.6 cm)/min. The reεults are set out in Table XXV below. Table XXV Delamination The various modifications and alterationε of thiε invention will be apparent to those skilled in the art without departing from the scope and spirit of this invention, and this invention should not be restricted to that set forth herein for illustrative purpoεeε.

Claims: We claim : 1. A roll of elaεtomeric laminate tape characterized in that it compriεeε a laminate comprised of - at least one elastomeric core layer capable of elastic elongation, and at least one outer skin layer which is capable of forming a microtextured surface, wherein when said laminate is stretched past the elastic deformation limit of at least one skin layer the laminate will form a microtextured εurface on that layer upon recovery, and at 0 leaεt one substantially continuous adheεive layer on at leaεt one face of εaid laminate. 2. An elaεtomeric laminate tape compriεing an elaεtomeric laminate compriεed of at least one elastomeric layer and at least one outer skin layer wherein the skin layer haε a microtextured surface formed by inelastic deformation of the skin layer in more than one direction and at least one substantially continuouε adhesive layer on at least one face of said laminate. 3. A method for forming a roll of microtextured elastic tape characterized in that it compriseε the steps of stretching a multilayer laminate backing, comprised of at leaεt one elaεtomeric layer and at leaεt two εkin layers, one of which iε a relatively inelastic layer capable of forming a microtextured surface, past the point of permanent deformation of the relatively nonelaεtic skin layer over substantially the entire laminate crosε section such that substantially all of the laminate iε rendered elaεtic for εubsequent use, recoving the laminate to form a microtextured εkin layer and applying a subεtantially continouε adhesive layer to said laminate backing. 4. An adhesive sheet laminate characterized in that it compriseε an elaεtomeric laminate tape compriεed of a laminate with at least one elastomeric core layer and at leaεt one outer microtextured εkin layer wherein the εheet has enclosed or partially encloεed spaces for entrapping dust or oil and an opposing outer adhesive layer. 5. A garment having an elaεticized region characterized in that it comprises an elastomeric laminate tape comprising a laminate, comprised of an elastomeric core layer and at least one microtextured skin layer, and at least one continuous adhesive layer on at least one face of said laminate. 6. The elaεtomeric laminate tape of any of claimε 1 to 5 characterized in that the microtextured εurface formed compriεes folds. 7. The elastomeric laminate tape of claims 1 or 3 characterized in that the laminate will recover from itε stretched length by 15% or more after 1 second. 8. The elastomeric laminate tape of claims 1 or 3 charcterized in that the laminate will recover from its εtretched length 15% after at leaεt 5 εecondε. 9. The elaεtomeric laminate tape of any of claimε 1 to 5 characterized in that the coefficient of friction of a laminate with microtextured outer εkin layer is 0.5 or less than that of a corresponding non-textured laminate. 10. The elaεtomeric laminate tape of claimε 1 or 3 characterized in that the laminate will recover from its stretched length by lesε than 15% after 20 seconds and when then exposed to an activation temperature above 26.7°C will recover by at leaεt 50% of the total recovery. 11. The elaεtomeric laminate tape of any of claims 1 to 5 characterized in that the core and skin layerε are bonded together by a tie layer. 12. The elastomeric laminate tape of any of claims 1 to 5 characterized in that the laminate width decreases by less than 20% when restretched to the point of permanent deformation of at least one previously deformed skin layer. 13. The elastomeric laminate tape of any of claims 1 to 5 characterized in that the surface area of the microtextured skin layer is at least 50% greater than an untextured surface. 14. The elastomeric laminate tape of any of claims 1 to 5 characterized in that said adhesive layer is adjacent to at leaεt one outer εkin layer of εaid laminate. 15. The elaεtomeric laminate tape of any of claims 1 to 5 further characterized by at least two skin layers, capable of forming a microtextured surface, as outer layerε. 16. The elastomeric laminate tape of any of claimε 1 to 5 further characterized in that the adhesive layer thicknesε is lesε than 30 microns. 17. The elastomeric laminate tape of any of claims 1 to 5 further characterized in that the elaεtomeric core comprises a non-heat-shrink elastomer. 18. The elastomeric laminate tape of any of claims 1 to 5 further characterized in that the elastomeric core comprises an A-B-A block copolymer. 19. The elastomeric laminate tape of claim 18 characterized in that the A-B-A block copolymer comprises a styrene- isoprene-styrene, styrene-butadiene-styrene or styrene-ethylene butylene-styrene block copolymer. 20. The elastomeric laminate tape of any of claimε 1 to 5 characterized in that the stretched laminate recovers by 15% after at least 20 seconds. 21. The elastomeric laminate tape of claim 2 characterized in that the deformation of the skin layer is created by simultaneous biaxial stretching. 22. The method of claim 3 characterized in that the laminate is recovered at an activation temperature above 26.7°C further characterized by cooling the stretched laminate to below the activation temperature prior to recovery. 23. The method of claim 3 characterized in that the adhesive layer iε applied to the laminate prior to stretching. 24. The method of claim 3 characterized in that adhesive layer is applied to the laminate after stretching. 25. The method of claim 3 characterized in that the adhesive layer is applied prior to recovery. 26. The sheet laminate of claim 4 comprising a dust mat. 27. The elaεtomeric laminate tape of any of claims 1 to 5 characterized in that the laminate iε capable of recovering instantaneously, over time or upon the application of heat, depending on the degree of stretch past the deformation limit of at least one skin layer. 28. The elaεtomeric laminate tape of any of claims 1 to 3 comprising a tamper-indicating tape. 29. The elaεtomeric laminate tape of claim 1 characterized in that the tape dela inateε or tears when stretched. 30. The elastomeric laminate tape of any of claims 1 to 3 compriεing a removable label having a non-adhesive coated outer skin layer. 31. The garment of claim 5 characterized in that at least one microtextured skin layer is not adheεive coated to provide a low friction surface for engagement with a wearer. 32. The garment of claim 5 characterized in that it comprises a diaper and said elastomeric tape is used to engage the wearer. 33. The elastomeric laminate tape of any of claims 1 to 5 characterized in that the laminate is a film formed of substantially coextensive layers having relatively constant average thicknesεeε acroεε the width of the laminate. 34. The elastomeric laminate tape of any of claims 1 to 5 characterized in that the core and skin layers remain in substantially continuous contact following stretching and recovery. 35. The elaεtomeric laminate tape of any of claimε 1 to 5 characterized in that the εkin and core layerε remain in εubstantially intermittent contact following stretching and activation.

Inventors: CAPIK KAREN M, DELGADO JOAQUIN, KRUEGER DENNIS L, CAPIK, KAREN, M., DELGADO, JOAQUIN, KRUEGER, DENNIS, L.
Applicants: MINNESOTA MINING & MFG, MINNESOTA MINING AND MANUFACTURING COMPANY
Application year: 1991
Main classification: B29C55
IPC codes: A61F13, A61L15, B05B15, B29C55, B29C61, B32B25, C09J7