Patent Application
20170304482
Significant efforts have been made to produce low density polyolefin materials to improve the use of natural resources and reduction of the carbon footprint in finished products. A typical approach to producing low density polyolefin materials is by foaming the polymer using physical or chemical blowing agents, which create gas cells though the bulk. Chemical blowing agents are compounds that undergo chemical reaction liberating gas that creates the cellular structure through the bulk of the polymer. Physical blowing agents are typically compressed gases that are dispersed in the polymer and expand creating the cells. Regardless, typical foaming processes induce low molecular orientation because the cell formation happens when the polymer is in the molten state. This prevents the polymer from strain hardening, which typically occurs at temperatures well above the melting temperature or glass transition temperature of the polymer, yielding products with low mechanical strength. Furthermore, typical foaming processes generate large cell sizes, such as greater than 100 μm. This reduces the melt strength, thus leading to breaks in high speed production processes with high deformation rates (e.g., fiber spinning, film formation, molding, etc.).
As such, a need currently exists for an improved technique in forming low density polyolefin materials.
In accordance with one embodiment of the present invention, a polyolefin material is disclosed that comprises a thermoplastic composition. The composition contains a continuous phase that includes a polyolefin matrix polymer and a nanoinclusion additive dispersed within the continuous phase in the form of discrete domains. The composition also includes a beta-nucleating agent. A porous network is defined within the thermoplastic composition that includes a plurality of nanopores.
In accordance with another embodiment of the present invention, a method for forming a polyolefin material is disclosed that comprises forming a thermoplastic composition that contains a continuous phase that includes a polyolefin matrix polymer and a nanoinclusion additive dispersed within the continuous phase in the form of discrete domains, the composition further including a beta-nucleating agent; and solid state drawing the thermoplastic composition to form a porous network therein, the porous network including a plurality of nanopores.
Other features and aspects of the present invention are discussed in greater detail below.
A full and enabling disclosure of the present invention, including the best mode thereof, directed to one of ordinary skill in the art, is set forth more particularly in the remainder of the specification, which makes reference to the appended figures in which:
Reference now will be made in detail to various embodiments of the invention, one or more examples of which are set forth below. Each example is provided by way of explanation of the invention, not limitation of the invention. In fact, it will be apparent to those skilled in the art that various modifications and variations may be made in the present invention without departing from the scope or spirit of the invention. For instance, features illustrated or described as part of one embodiment, may be used on another embodiment to yield a still further embodiment. Thus, it is intended that the present invention covers such modifications and variations as come within the scope of the appended claims and their equivalents.
Generally speaking, the present invention is directed to a polyolefin material (e.g., film, fibrous material, molded article, etc.) that is formed by drawing of a thermoplastic composition (e.g., solid state drawing) containing a continuous phase, which includes a polyolefin matrix polymer, and a nanoinclusion additive that is at least partially incompatible with the polyolefin matrix polymer so that it becomes dispersed within the continuous phase as discrete nano-scale phase domains. During drawing, when the composition is subjected to a deformation and elongational strain, the present inventors have discovered that these nano-scale phase domains are able to interact in a unique manner to create a network of pores. Namely, it is believed that elongational strain can initiate intensive localized shear zones and/or stress intensity zones (e.g., normal stresses) near the discrete phase domains as a result of stress concentrations that arise from the incompatibility of the materials. These shear and/or stress intensity zones cause some initial debonding in the polyolefin matrix adjacent to the domains. Once initial pores are formed, the matrix located between domains can deform plastically to create internal stretched areas that locally narrow (or neck) and strain-harden. This process allows the formation of pores through the bulk of the composition that grow in the stretching direction, thereby leading to the formation of a porous network while the molecular orientation leads to strain-hardening that enhances mechanical strength.
Under typical drawing conditions, the majority of polyolefin is in the alpha-crystalline form. Such alpha-crystals are highly stable and tend to have a relatively high melting temperature, which can make it difficult to draw and form the desired porous network without a significant amount of breakage. In this regard, the present inventors have discovered that the use of a beta-crystalline nucleating agent in the composition can help enhance and stabilize the formation of the porous network, and also minimize the degree of breakage during drawing. More particularly, the beta-nucleating agent can increase the presence of beta-crystals in the thermoplastic composition prior to drawing. Prior to drawing, for instance, the polyolefin material may contain beta crystals in an amount of from about 5 wt. % to about 80 wt. %, in some embodiments from about 10 wt. % to about 70 wt. %, and in some embodiments, from about 20 wt. % to about 60 wt. % of the polyolefin matrix. Such beta crystals are generally considered to be less thermodynamically stable, which means that less energy is required to melt the beta crystals. This results in a depression of the melting temperature of the pre-drawn thermoplastic composition (e.g., melting temperature of the beta crystals) that is in a range of from about 80° C. to about 150° C., in some embodiments from about 100° C. to about 150° C., and in some embodiments, from about 110° C. to about 145° C., as determined from the endothermic peak exhibited during the second heating cycle of a two-cycle differential scanning calorimetry (“DSC”) analysis in accordance with ASTM D-3417. In this manner, a lower yield stress can be employed during solid state drawing to minimize the likelihood of breakage. The composition may also deform in a more gradual manner and possess a high degree of ductility and toughness. Moreover, because the beta-crystals have a lower density than the alpha crystals, they can facilitate the growth of the porous network because as they compensate for the volume contraction that occurs when a less dense crystal converts into a more dense crystal.
Through the techniques noted above, a stable porous network may be formed in the polyolefin material so that the average percent volume occupied by the pores within a given unit volume of the material may be from about 15% to about 80% per cm3, in some embodiments from about 20% to about 70%, and in some embodiments, from about 30% to about 60% per cubic centimeter of the material. With such a pore volume, the composition may have a relatively low density, such as about 0.90 grams per cubic centimeter (“g/cm3”) or less, in some embodiments about 0.85 g/cm3 or less, in some embodiments about 0.80 g/cm3 or less, in some embodiments from about 0.10 g/cm3 to about 0.75 g/cm3, and in some embodiments, from about 0.20 g/cm3 to about 0.70 g/cm3. A substantial portion of pores in the porous network are also of a “nano-scale” size (“nanopores”), such as those having an average cross-sectional dimension of about 800 nanometers or less, in some embodiments from about 5 to about 700 nanometers, and in some embodiments, from about 10 to about 500 nanometers. The term “cross-sectional dimension” generally refers to a characteristic dimension (e.g., width or diameter) of a pore, which is substantially orthogonal to its major axis (e.g., length) and also typically substantially orthogonal to the direction of the stress applied during drawing. The nanopores may also have an average axial dimension within the range of from about 100 to about 5000 nanometers, in some embodiments from about 50 to about 2000 nanometers, and in some embodiments, from about 100 to about 1000 nanometers. The “axial dimension” is the dimension in the direction of the major axis (e.g., length), which is typically in the direction of drawing. Such nanopores may, for example, constitute about 15 vol. % or more, in some embodiments about 20 vol. % or more, in some embodiments from about 30 vol. % to 100 vol. %, and in some embodiments, from about 40 vol. % to about 90 vol. % of the total pore volume in the polyolefin material.
Besides a reduced density, the nanoporous structure may also provide a variety of additional different benefits to the resulting polyolefin material. For example, such a structure can help restrict the flow of fluids through the material and be generally impermeable to fluids (e.g., liquid water), thereby allowing the material to insulate a surface from water penetration. In this regard, the polyolefin material may have a relatively high hydrohead value of about 50 centimeters (“cm”) or more, in some embodiments about 100 cm or more, in some embodiments, about 150 cm or more, and in some embodiments, from about 200 cm to about 1000 cm, as determined in accordance with ATTCC 127-2008. Other beneficial properties may also be achieved. For example, the resulting polyolefin material may be generally permeable to water vapors. The permeability of the material to water vapor may characterized by its relatively high water vapor transmission rate (“WVTR”), which is the rate at which water vapor permeates through a material as measured in units of grams per meter squared per 24 hours (g/m2/24 hrs). For example, the polyolefin material may exhibit a WVTR of about 300 g/m2-24 hours or more, in some embodiments about 500 g/m2-24 hours or more, in some embodiments about 1,000 g/m2-24 hours or more, and in some embodiments, from about 3,000 to about 15,000 g/m2-24 hours, such as determined in accordance with ASTM E96/96M-12, Procedure B or INDA Test Procedure IST-70.4 (01).
Various embodiments of the present invention will now be described in more detail.
A. Polyolefin Matrix
Polyolefins typically constitute from about 60 wt. % to about 99 wt. %, in some embodiments from about 60 wt. % to about 98 wt. %, and in some embodiments, from about 80 wt. % to about 95 wt. % of the thermoplastic composition. Prior to being combined with the beta-nucleating agent, the polyolefin may initially have a melting temperature of from about 150° C. to about 220° C., in some embodiments from about 155° C. to about 200° C., and in some embodiments, from about 160° C. to about 180° C. The melting temperature may be determined using differential scanning calorimetry (“DSC”) in accordance with ASTM D-3417. Suitable polyolefins may, for instance, include ethylene polymers (e.g., low density polyethylene (“LDPE”), high density polyethylene (“HDPE”), linear low density polyethylene (“LLDPE”), etc.), propylene homopolymers (e.g., syndiotactic, atactic, isotactic, etc.), propylene copolymers, and so forth. In one particular embodiment, the polymer is a propylene polymer, such as homopolypropylene or a copolymer of propylene. The propylene polymer may, for instance, be formed from a substantially isotactic polypropylene homopolymer or a copolymer containing equal to or less than about 10 wt. % of other monomers, i.e., at least about 90% by weight propylene. Such homopolymers may have a melting point of from about 160° C. to about 170° C.
Of course, other polyolefins may also be employed in the composition of the present invention. In one embodiment, for example, the polyolefin may be a copolymer of ethylene or propylene with another α-olefin, such as a C3-C20 α-olefin or C3-C12 α-olefin. Specific examples of suitable α-olefins include 1-butene; 3-methyl-1-butene; 3,3-dimethyl-1-butene; 1-pentene; 1-pentene with one or more methyl, ethyl or propyl substituents; 1-hexene with one or more methyl, ethyl or propyl substituents; 1-heptene with one or more methyl, ethyl or propyl substituents; 1-octene with one or more methyl, ethyl or propyl substituents; 1-nonene with one or more methyl, ethyl or propyl substituents; ethyl, methyl or dimethyl-substituted 1-decene; 1-dodecene; and styrene. Particularly desired α-olefin comonomers are 1-butene, 1-hexene and 1-octene. The ethylene or propylene content of such copolymers may be from about 60 mole % to about 99 mole %, in some embodiments from about 80 mole % to about 98.5 mole %, and in some embodiments, from about 87 mole % to about 97.5 mole %. The α-olefin content may likewise range from about 1 mole % to about 40 mole %, in some embodiments from about 1.5 mole % to about 15 mole %, and in some embodiments, from about 2.5 mole % to about 13 mole %.
Exemplary olefin copolymers for use in the present invention include ethylene-based copolymers available under the designation EXACT™ from ExxonMobil Chemical Company of Houston, Tex. Other suitable ethylene copolymers are available under the designation ENGAGE™, AFFINITY™, DOWLEX™ (LLDPE) and ATTANE™ (ULDPE) from Dow Chemical Company of Midland, Mich. Other suitable ethylene polymers are described in U.S. Pat. No. 4,937,299 to Ewen et al.; U.S. Pat. No. 5,218,071 to Tsutsui et al.; U.S. Pat. No. 5,272,236 to Lai, et al.; and 5,278,272 to Lai, et al. Suitable propylene copolymers are also commercially available under the designations VISTAMAXX™ from ExxonMobil Chemical Co. of Houston, Tex.; FINA™ (e.g., 8573) from Atofina Chemicals of Feluy, Belgium; TAFMER™ available from Mitsui Petrochemical Industries; and VERSIFY™ available from Dow Chemical Co. of Midland, Mich. Suitable polypropylene homopolymers may include Exxon Mobil 3155 polypropylene, Exxon Mobil Achieve™ resins, and Total M3661 PP resin. Other examples of suitable propylene polymers are described in U.S. Pat. No. 6,500,563 to Datta, et al.; U.S. Pat. No. 5,539,056 to Yang, et al.; and U.S. Pat. No. 5,596,052 to Resconi, et al.
Any of a variety of known techniques may generally be employed to form the olefin copolymers. For instance, olefin polymers may be formed using a free radical or a coordination catalyst (e.g., Ziegler-Natta). Preferably, the olefin polymer is formed from a single-site coordination catalyst, such as a metallocene catalyst. Such a catalyst system produces ethylene copolymers in which the comonomer is randomly distributed within a molecular chain and uniformly distributed across the different molecular weight fractions. Metallocene-catalyzed polyolefins are described, for instance, in U.S. Pat. No. 5,571,619 to McAlpin et al.; U.S. Pat. No. 5,322,728 to Davis et al.; U.S. Pat. No. 5,472,775 to Obijeski et al.; U.S. Pat. No. 5,272,236 to Lai et al.; and U.S. Pat. No. 6,090,325 to Wheat, et al. Examples of metallocene catalysts include bis(n-butylcyclopentadienyl)titanium dichloride, bis(n-butylcyclopentadienyl)zirconium dichloride, bis(cyclopentadienyl)scandium chloride, bis(indenyl)zirconium dichloride, bis(methylcyclopentadienyl)titanium dichloride, bis(methylcyclopentadienyl)zirconium dichloride, cobaltocene, cyclopentadienyltitanium trichloride, ferrocene, hafnocene dichloride, isopropyl(cyclopentadienyl,-1-flourenyl)zirconium dichloride, molybdocene dichloride, nickelocene, niobocene dichloride, ruthenocene, titanocene dichloride, zirconocene chloride hydride, zirconocene dichloride, and so forth. Polymers made using metallocene catalysts typically have a narrow molecular weight range. For instance, metallocene-catalyzed polymers may have polydispersity numbers (Mw/Mn) of below 4, controlled short chain branching distribution, and controlled isotacticity.
B. Nanoinclusion Additive
As used herein, the term “nanoinclusion additive” generally refers to a material that is capable of being dispersed within the polymer matrix in the form of discrete domains of a nano-scale size. For example, prior to drawing, the domains may have an average cross-sectional dimension of from about 1 to about 1000 nanometers, in some embodiments from about 5 to about 800 nanometers, in some embodiments from about 10 to about 500 nanometers, and in some embodiments from about 20 to about 200 nanometers. The domains may have a variety of different shapes, such as elliptical, spherical, cylindrical, plate-like, tubular, etc. In one embodiment, for example, the domains have a substantially elliptical shape. The nanoinclusion additive is typically employed in an amount of from about 0.05 wt. % to about 20 wt. %, in some embodiments from about 0.5 wt. % to about 18 wt. %, and in some embodiments, from about 1 wt. % to about 15 wt. % of the thermoplastic composition, based on the weight of the continuous phase (e.g., matrix polymer(s)). The concentration of the nanoinclusion additive in the entire thermoplastic composition may likewise be from about 0.05 wt. % to about 20 wt. %, in some embodiments from about 0.5 wt. % to about 18 wt. %, and in some embodiments, from about 1 wt. % to about 15 wt. % of the thermoplastic composition.
The nanoinclusion additive is partially incompatible with the polyolefin in the sense that it can be substantially uniformly distributed within the polyolefin matrix, but in the form of discrete domains. Such partial incompatibility can be accomplished in a variety of ways. In certain embodiments, for example, the nanoinclusion additive may possess a nonpolar component (e.g., olefin) that is compatible with the polyolefin matrix and allows it to become uniformly distributed therein. Nevertheless, the additive may also include a polar component that is incompatible with the polyolefin matrix, thereby allowing it to coalesce or segregate into discrete domains. Such a component may include low or high molecular weight polar molecular segments or blocks, ionic groups, charged or uncharged polar domains, and/or polar molecular groups. Alternatively, the additive may be entirely nonpolar in nature, but possess certain physical properties that still allow for discrete domains to be formed. For example, in certain embodiments, the nanoinclusion additive may be compatible or miscible with the polyolefin above a certain temperature, but phase separate at temperatures lower than the critical solution temperature. In this manner, the nanoinclusion additive can form a stable blend with the polyolefin in the melt phase, but as the temperature decreases, the continuous phase crystallizes and segregates so that the nanoinclusion additive can phase separate, coalesce, and form separate nano-scale domains.
The particular state or form of the nanoinclusion additive is not critical so long as the desired domains can be formed. For example, in some embodiments, the nanoinclusion additive can be in the form of a liquid or semi-solid at room temperature (e.g., 25° C.). Such a liquid can be readily dispersed in the matrix to form a metastable dispersion, and then quenched to preserve the domain size by reducing the temperature of the blend. The kinematic viscosity of such a liquid or semi-solid material is typically from about 0.7 to about 200 centistokes (“cs”), in some embodiments from about 1 to about 100 cs, and in some embodiments, from about 1.5 to about 80 cs, determined at 40° C. Suitable liquids or semi-solids may include, for instance, silicones, silicone-polyether copolymers, aliphatic polyesters, aromatic polyesters, alkylene glycols (e.g., ethylene glycol, diethylene glycol, triethylene glycol, tetraethylene glycol, propylene glycol, polyethylene glycol, polypropylene glycol, polybutylene glycol, etc.), alkane diols (e.g., 1,3-propanediol, 2,2-dimethyl-1,3-propanediol, 1,3-butanediol, 1,4-butanediol, 1,5-pentanediol, 1,6-hexanediol, 2,2,4-trimethyl-1,6 hexanediol, 1,3-cyclohexanedimethanol, 1,4-cyclohexanedimethanol, 2,2,4,4-tetramethyl-1,3-cyclobutanediol, etc.), amine oxides (e.g., octyldimethylamine oxide), fatty acid esters, fatty acid amides (e.g., oleamide, erucamide, stearamide, ethylene bis(stearamide), etc.), mineral, and vegetable oils, and so forth. One particularly suitable liquid or semi-solid is polyether polyol, such as commercially available under the trade name Pluriol® WI from BASF Corp.
In yet other embodiments, the nanoinclusion additive is in the form of a solid, which may be amorphous, crystalline, or semi-crystalline. For example, the nanoinclusion additive may be polymeric in nature and possess a relatively high molecular weight to help improve the melt strength and stability of the thermoplastic composition. As indicated above, the nanoinclusion additive is partially incompatible with the polyolefin matrix. One example of such an additive is a microcrystalline polyolefin wax, which is typically derived from ethylene and/or C3-C10-alk-1-enes, such as from propylene, 1-butene, 1-pentene, 1-hexene, 1-heptene, 1-octene, 1-nonene, and 1-decene. Microcrystalline waxes typically have a relatively low melting temperature, such as from about 30° C. to about 150° C., in some embodiments from about 50° C. to about 140° C., and in some embodiments, from about 80° C. to about 130° C. At such low melting temperatures, the wax can form a miscible blend with the polyolefin when in the melt phase, but as the temperature decreases and polymer crystalizes or solidifies, the wax will segregate and coalesce forming separate nano-scale domains.
Another example of a polymeric nanoinclusion additive is a functionalized polyolefin that contains a polar and nonpolar component. The polar component may, for example, be provided by one or more functional groups and the nonpolar component may be provided by an olefin. The olefin component of the nanoinclusion additive may generally be formed from any linear or branched α-olefin monomer, oligomer, or polymer (including copolymers) derived from an olefin monomer, such as described above. The functional group of the nanoinclusion additive may be any group, molecular segment and/or block that provides a polar component to the molecule and is not compatible with the polyolefin matrix polymer. Examples of molecular segment and/or blocks not compatible with polyolefin may include acrylates, styrenics, polyesters, polyamides, etc. The functional group can have an ionic nature and comprise charged metal ions. Particularly suitable functional groups are maleic anhydride, maleic acid, fumaric acid, maleimide, maleic acid hydrazide, a reaction product of maleic anhydride and diamine, methylnadic anhydride, dichloromaleic anhydride, maleic acid amide, etc. Maleic anhydride modified polyolefins are particularly suitable for use in the present invention. Such modified polyolefins are typically formed by grafting maleic anhydride onto a polymeric backbone material. Such maleated polyolefins are available from E. I. du Pont de Nemours and Company under the designation Fusabond®, such as the P Series (chemically modified polypropylene), E Series (chemically modified polyethylene), C Series (chemically modified ethylene vinyl acetate), A Series (chemically modified ethylene acrylate copolymers or terpolymers), or N Series (chemically modified ethylene-propylene, ethylene-propylene diene monomer (“EPDM”) or ethylene-octene). Alternatively, maleated polyolefins are also available from Chemtura Corp. under the designation Polybond®, Eastman Chemical Company under the designation Eastman G series, and Arkema under the designation Orevac®.
In certain embodiments, the polymeric nanoinclusion additive may also be reactive. One example of such a reactive nanoinclusion additive is a polyepoxide that contains, on average, at least two oxirane rings per molecule. Without intending to be limited by theory, it is believed that such polyepoxide molecules can undergo a reaction (e.g., chain extension, side chain branching, grafting, copolymer formation, etc.) with certain components of the composition to improve melt strength without significantly reducing glass transition temperature. The reactive additive can also provide compatibilization between the polyolefin and other more polar additives, such as microinclusion additives, and can improve the uniformity of dispersion and reduce the size of microinclusion additives. For example, as will be described in more detail below, certain embodiments of the present invention may employ a polyester as a microinclusion additive. In such embodiments, the reactive nanoinclusion additive may enable a nucleophilic ring-opening reaction via a carboxyl terminal group of the polyester (esterification) or via a hydroxyl group (etherification). Oxazoline side reactions may likewise occur to form esteramide moieties. Through such reactions, the molecular weight of a polyester microinclusion additive may be increased to counteract the degradation often observed during melt processing. The present inventors have discovered that too much of a reaction can lead to crosslinking between polymer backbones. If such crosslinking is allowed to proceed to a significant extent, the resulting polymer blend can become brittle and difficult to process into a material with the desired strength and elongation properties.
In this regard, the present inventors have discovered that polyepoxides having a relatively low epoxy functionality may be particularly effective, which may be quantified by its “epoxy equivalent weight.” The epoxy equivalent weight reflects the amount of resin that contains one molecule of an epoxy group, and it may be calculated by dividing the number average molecular weight of the modifier by the number of epoxy groups in the molecule. The polyepoxide of the present invention typically has a number average molecular weight from about 7,500 to about 250,000 grams per mole, in some embodiments from about 15,000 to about 150,000 grams per mole, and in some embodiments, from about 20,000 to 100,000 grams per mole, with a polydispersity index typically ranging from 2.5 to 7. The polyepoxide may contain less than 50, in some embodiments from 5 to 45, and in some embodiments, from 15 to 40 epoxy groups. In turn, the epoxy equivalent weight may be less than about 15,000 grams per mole, in some embodiments from about 200 to about 10,000 grams per mole, and in some embodiments, from about 500 to about 7,000 grams per mole.
The polyepoxide may be a linear or branched, homopolymer or copolymer (e.g., random, graft, block, etc.) containing terminal epoxy groups, skeletal oxirane units, and/or pendent epoxy groups. The monomers employed to form such polyepoxides may vary. In one particular embodiment, for example, the polyepoxide contains at least one epoxy-functional (meth)acrylic monomeric component. As used herein, the term “(meth)acrylic” includes acrylic and methacrylic monomers, as well as salts or esters thereof, such as acrylate and methacrylate monomers. For example, suitable epoxy-functional (meth)acrylic monomers may include, but are not limited to, those containing 1,2-epoxy groups, such as glycidyl acrylate and glycidyl methacrylate. Other suitable epoxy-functional monomers include allyl glycidyl ether, glycidyl ethacrylate, and glycidyl itoconate.
The polyepoxide typically has a relatively high molecular weight, as indicated above, so that it may not only result in chain extension, but also help to achieve the desired blend morphology. The resulting melt flow rate of the polymer is thus typically within a range of from about 10 to about 200 grams per 10 minutes, in some embodiments from about 40 to about 150 grams per 10 minutes, and in some embodiments, from about 60 to about 120 grams per 10 minutes, determined at a load of 2160 grams and at a temperature of 190° C.
The polyepoxide also typically includes at least one linear or branched α-olefin monomer, such as those having from 2 to 20 carbon atoms and preferably from 2 to 8 carbon atoms. Specific examples include ethylene, propylene, 1-butene; 3-methyl-1-butene; 3,3-dimethyl-1-butene; 1-pentene; 1-pentene with one or more methyl, ethyl or propyl substituents; 1-hexene with one or more methyl, ethyl or propyl substituents; 1-heptene with one or more methyl, ethyl or propyl substituents; 1-octene with one or more methyl, ethyl or propyl substituents; 1-nonene with one or more methyl, ethyl or propyl substituents; ethyl, methyl or dimethyl-substituted 1-decene; 1-dodecene; and styrene. Particularly desired α-olefin comonomers are ethylene and propylene. Another suitable monomer may include a (meth)acrylic monomer that is not epoxy-functional. Examples of such (meth)acrylic monomers may include methyl acrylate, ethyl acrylate, n-propyl acrylate, i-propyl acrylate, n-butyl acrylate, s-butyl acrylate, i-butyl acrylate, t-butyl acrylate, n-amyl acrylate, i-amyl acrylate, isobornyl acrylate, n-hexyl acrylate, 2-ethylbutyl acrylate, 2-ethylhexyl acrylate, n-octyl acrylate, n-decyl acrylate, methylcyclohexyl acrylate, cyclopentyl acrylate, cyclohexyl acrylate, methyl methacrylate, ethyl methacrylate, 2-hydroxyethyl methacrylate, n-propyl methacrylate, n-butyl methacrylate, i-propyl methacrylate, i-butyl methacrylate, n-amyl methacrylate, n-hexyl methacrylate, i-amyl methacrylate, s-butyl-methacrylate, t-butyl methacrylate, 2-ethylbutyl methacrylate, methylcyclohexyl methacrylate, cinnamyl methacrylate, crotyl methacrylate, cyclohexyl methacrylate, cyclopentyl methacrylate, 2-ethoxyethyl methacrylate, isobornyl methacrylate, etc., as well as combinations thereof.
In one particularly desirable embodiment of the present invention, the polyepoxide is a terpolymer formed from an epoxy-functional (meth)acrylic monomeric component, α-olefin monomeric component, and non-epoxy functional (meth)acrylic monomeric component. For example, the polyepoxide may be poly(ethylene-co-methylacrylate-co-glycidyl methacrylate), which has the following structure:
wherein, x, y, and z are 1 or greater.
The epoxy functional monomer may be formed into a polymer using a variety of known techniques. For example, a monomer containing polar functional groups may be grafted onto a polymer backbone to form a graft copolymer. Such grafting techniques are well known in the art and described, for instance, in U.S. Pat. No. 5,179,164. In other embodiments, a monomer containing epoxy functional groups may be copolymerized with a monomer to form a block or random copolymer using known free radical polymerization techniques, such as high pressure reactions, Ziegler-Natta catalyst reaction systems, single site catalyst (e.g., metallocene) reaction systems, etc.
The relative portion of the monomeric component(s) may be selected to achieve a balance between epoxy-reactivity and melt flow rate. More particularly, high epoxy monomer contents can result in good reactivity, but too high of a content may reduce the melt flow rate to such an extent that the polyepoxide adversely impacts the melt strength of the polymer blend. Thus, in most embodiments, the epoxy-functional (meth)acrylic monomer(s) constitute from about 1 wt. % to about 25 wt. %, in some embodiments from about 2 wt. % to about 20 wt. %, and in some embodiments, from about 4 wt. % to about 15 wt. % of the copolymer. The α-olefin monomer(s) may likewise constitute from about 55 wt. % to about 95 wt. %, in some embodiments from about 60 wt. % to about 90 wt. %, and in some embodiments, from about 65 wt. % to about 85 wt. % of the copolymer. When employed, other monomeric components (e.g., non-epoxy functional (meth)acrylic monomers) may constitute from about 5 wt. % to about 35 wt. %, in some embodiments from about 8 wt. % to about 30 wt. %, and in some embodiments, from about 10 wt. % to about 25 wt. % of the copolymer. One specific example of a suitable polyepoxide that may be used in the present invention is commercially available from Arkema under the name LOTADER® AX8950 or AX8900. LOTADER® AX8950, for instance, has a melt flow rate of 70 to 100 g/10 min and has a glycidyl methacrylate monomer content of 7 wt. % to 11 wt. %, a methyl acrylate monomer content of 13 wt. % to 17 wt. %, and an ethylene monomer content of 72 wt. % to 80 wt. %. Another suitable polyepoxide is commercially available from DuPont under the name ELVALOY® PTW, which is a terpolymer of ethylene, butyl acrylate, and glycidyl methacrylate and has a melt flow rate of 12 g/10 min.
In addition to controlling the type and relative content of the monomers used to form the polyepoxide, the overall weight percentage may also be controlled to achieve the desired benefits. For example, if the modification level is too low, the desired increase in melt strength and mechanical properties may not be achieved. The present inventors have also discovered, however, that if the modification level is too high, processing may be restricted due to strong molecular interactions (e.g., crosslinking) and physical network formation by the epoxy functional groups. Thus, the polyepoxide is typically employed in an amount of from about 0.05 wt. % to about 10 wt. %, in some embodiments from about 0.1 wt. % to about 8 wt. %, in some embodiments from about 0.5 wt. % to about 5 wt. %, and in some embodiments, from about 1 wt. % to about 3 wt. %, based on the weight of the continuous phase. The polyepoxide may also constitute from about 0.05 wt. % to about 10 wt. %, in some embodiments from about 0.05 wt. % to about 8 wt. %, in some embodiments from about 0.1 wt. % to about 5 wt. %, and in some embodiments, from about 0.5 wt. % to about 3 wt. %, based on the total weight of the composition.
Other reactive nanoinclusion additives may also be employed in the present invention, such as oxazoline-functionalized polymers, cyanide-functionalized polymers, etc. When employed, such reactive nanoinclusion additives may be employed within the concentrations noted above for the polyepoxide. In one particular embodiment, an oxazoline-grafted polyolefin may be employed that is a polyolefin grafted with an oxazoline ring-containing monomer. The oxazoline may include a 2-oxazoline, such as 2-vinyl-2-oxazoline (e.g., 2-isopropenyl-2-oxazoline), 2-fatty-alkyl-2-oxazoline (e.g., obtainable from the ethanolamide of oleic acid, linoleic acid, palmitoleic acid, gadoleic acid, erucic acid and/or arachidonic acid) and combinations thereof. In another embodiment, the oxazoline may be selected from ricinoloxazoline maleinate, undecyl-2-oxazoline, soya-2-oxazoline, ricinus-2-oxazoline and combinations thereof, for example. In yet another embodiment, the oxazoline is selected from 2-isopropenyl-2-oxazoline, 2-isopropenyl-4,4-dimethyl-2-oxazoline and combinations thereof.
In certain embodiments of the present invention, multiple nanoinclusion additives may be employed in combination. For instance, a first nanoinclusion additive (e.g., polyepoxide) may be dispersed in the form of domains having an average cross-sectional dimension of from about 50 to about 500 nanometers, in some embodiments from about 60 to about 400 nanometers, and in some embodiments from about 80 to about 300 nanometers. A second nanoinclusion additive may also be dispersed in the form of domains that are smaller than the first nanoinclusive additive, such as those having an average cross-sectional dimension of from about 1 to about 50 nanometers, in some embodiments from about 2 to about 45 nanometers, and in some embodiments from about 5 to about 40 nanometers. When employed, the first and/or second nanoinclusion additives typically constitute from about 0.05 wt. % to about 20 wt. %, in some embodiments from about 0.1 wt. % to about 10 wt. %, and in some embodiments, from about 0.5 wt. % to about 5 wt. % of the thermoplastic composition, based on the weight of the continuous phase (matrix polymer(s)). The concentration of the first and/or second nanonclusion additives in the entire thermoplastic composition may likewise be from about 0.01 wt. % to about 15 wt. %, in some embodiments from about 0.05 wt. % to about 10 wt. %, and in some embodiments, from about 0.1 wt. % to about 8 wt. % of the thermoplastic composition.
Nanofillers may optionally be employed for the second nanoinclusion additive, examples of which may include carbon black, carbon nanotubes, carbon nanofibers, nanoclays, metal nanoparticles, nanosilica, nanoalumina, etc. Nanoclays are particularly suitable. The term “nanoclay” generally refers to nanoparticles of a clay material (a naturally occurring mineral, an organically modified mineral, or a synthetic nanomaterial), which typically have a platelet structure. Examples of nanoclays include, for instance, montmorillonite (2:1 layered smectite clay structure), bentonite (aluminium phyllosilicate formed primarily of montmorillonite), kaolinite (1:1 aluminosilicate having a platy structure and empirical formula of Al2Si2O5(OH)4), halloysite (1:1 aluminosilicate having a tubular structure and empirical formula of Al2Si2O5(OH)4), etc. An example of a suitable nanoclay is Cloisite®, which is a montmorillonite nanoclay and commercially available from Southern Clay Products, Inc. Other examples of synthethic nanoclays include but are not limited to a mixed-metal hydroxide nanoclay, layered double hydroxide nanoclay (e.g., sepiocite), laponite, hectorite, saponite, indonite, etc.
If desired, the nanoclay may contain a surface treatment to help improve compatibility with the matrix polymer (e.g., polyester). The surface treatment may be organic or inorganic. In one embodiment, an organic surface treatment is employed that is obtained by reacting an organic cation with the clay. Suitable organic cations may include, for instance, organoquaternary ammonium compounds that are capable of exchanging cations with the clay, such as dimethyl bis[hydrogenated tallow] ammonium chloride (2M2HT), methyl benzyl bis[hydrogenated tallow] ammonium chloride (MB2HT), methyl tris[hydrogenated tallow alkyl] chloride (M3HT), etc. Examples of commercially available organic nanoclays may include, for instance, Dellite® 43B (Laviosa Chimica of Livorno, Italy), which is a montmorillonite clay modified with dimethyl benzylhydrogenated tallow ammonium salt. Other examples include Cloisite® 25A and Cloisite® 30B (Southern Clay Products) and Nanofil 919 (Süd Chemie). If desired, the nanofiller can be blended with a carrier resin to form a masterbatch that enhances the compatibility of the additive with the other polymers in the composition. Particularly suitable carrier resins include, for instance, polyesters (e.g., polylactic acid, polyethylene terephthalate, etc.); polyolefins (e.g., ethylene polymers, propylene polymers, etc.); and so forth, as described in more detail above.
Regardless of the material employed, the nanoinclusion additive is typically selected to have a certain viscosity (or melt flow rate) to ensure that the discrete domains and resulting pores can be adequately maintained. For example, if the viscosity of the nanoinclusion additive is too low (or melt flow rate is too high), it tends to flow and disperse uncontrollably through the continuous phase. This results in lamellar, plate-like domains or co-continuous phase structures that are difficult to maintain and also likely to prematurely fracture. Conversely, if the viscosity is too high (or melt flow rate is too low), it tends to clump together and form very large elliptical domains, which are difficult to disperse during blending. This may cause uneven distribution of the nanoinclusion additive through the entirety of the continuous phase. For instance, the ratio of the melt flow rate of the polyolefin to the melt flow rate of a polymeric nanoinclusion additive, for instance, may be from about 0.2 to about 8, in some embodiments from about 0.5 to about 6, and in some embodiments, from about 1 to about 5. The nanoinclusion additive may, for example, have a melt flow rate (on a dry basis) of from about 0.1 to about 100 grams per 10 minutes, in some embodiments from about 0.5 to about 50 grams per 10 minutes, and in some embodiments, from about 5 to about 15 grams per 10 minutes, determined at a load of 2160 grams and at a temperature at least about 40° C. above the melting temperature (e.g., at 190° C.) in accordance with ASTM D1238. The polyolefin may likewise have a melt flow rate (on a dry basis) of from about 0.5 to about 80 grams per 10 minutes, in some embodiments from about 1 to about 40 grams per 10 minutes, and in some embodiments, from about 5 to about 20 grams per 10 minutes, determined at a load of 2160 grams and at a temperature at least about 40° C. above the melting temperature (e.g., at 230° C.) in accordance with ASTM D1238.
C. Beta-Nucleating Agent
The beta-nucleating agent is typically employed in an amount high enough to initiate the desired formation of beta-crystals, but not so high that the resulting properties of the composition are adversely impacted. For example, the beta-nucleating agent is typically employed in an amount of from about 0.01 wt. % to about 8 wt. %, in some embodiments from about 0.1 wt. % to about 5 wt. %, and in some embodiments, from about 0.5 wt. % to about 4 wt. %, based on the weight of the continuous phase (e.g., matrix polymer(s)). The beta-nucleating agent may also be employed in an amount of from about 0.01 wt. % to about 8 wt. %, in some embodiments from about 0.1 wt. % to about 5 wt. %, and in some embodiments, from about 0.5 wt. % to about 4 wt. %, based on the total weight of the composition.
Any of a variety of beta-nucleating agents may generally be employed in the present invention. Examples of suitable beta-nucleating agents may include, for instance, quinacridones (e.g., gamma-phase quinacridone, delta-phase quinacridone, etc.); quinacridone derivatives (e.g., quinacridonequinone, dihydroxyquinacridone, quinacridine-tetrone, etc.); dicarboxylic acids (e.g., adipic acid, suberic, pimelic, phthalic, isophthalic, terephthalic acid, etc.), as well as oxide, hydroxides, diamides, or metal salts thereof; anthraquinones, anthraquinone derivatives, or anthraquinone salts (e.g., an aluminum salt of quinizarin sulphonic acid); ditriazines (e.g., triphenenol ditriazine); aromatic carboxamides (e.g., N,N-dicyclohexyl-2.6-naphtalene dicarboxamide); and so forth, as well as combinations thereof. In one embodiment, for instance, the beta-nucleating agent is quinacridone or quinacridonequinone. In some embodiments, the beta-nucleating agent is formed by mixing an organic dicarboxylic acid (e.g., pimelic acid, azelaic acid, o-phthalic acid, terephthalic acid, and isophthalic acid) and an oxide, hydroxide, or acid salt of a Group II metal (e.g., magnesium, calcium, strontium, and barium). The beta-nucleating agents may be provided in the form of a polyolefin masterbatch, such as those commercially available under the designation MPM® 2000, MPM® 1101, MPM® 1110, MPM® 1112, MPM® 1113, and MPM® 1114 from Mayzo, Inc.
D. Microinclusion Additive
Although not required, the composition of the present invention may also employ a microinclusion additive. As used herein, the term “microinclusion additive” generally refers to any material that is capable of being dispersed within the polymer matrix in the form of discrete domains of a micro-scale size. For example, prior to drawing, the domains may have an average cross-sectional dimension of from about 0.1 μm to about 25 μm, in some embodiments from about 0.5 μm to about 20 μm, and in some embodiments from about 1 μm to about 10 μm. When employed, the present inventors have discovered that the micro-scale and nano-scale phase domains are able to interact in a unique manner when subjected to a deformation and elongational strain (e.g., drawing) to create a network of pores. Namely, it is believed that elongational strain can initiate intensive localized shear zones and/or stress intensity zones (e.g., normal stresses) near the micro-scale discrete phase domains as a result of stress concentrations that arise from the incompatibility of the materials. These shear and/or stress intensity zones cause some initial debonding in the polyolefin matrix adjacent to the micro-scale domains. Notably, however, the localized shear and/or stress intensity zones created near the nano-scale discrete phase domains may overlap with the micro-scale zones to cause even further debonding to occur in the polymer matrix, thereby creating a substantial number of nanopores adjacent to the nano-scale domains and/or micro-scale domains.
The particular nature of the microinclusion additive is not critical, and may include liquids, semi-solids, or solids (e.g., amorphous, crystalline, or semi-crystalline). In certain embodiments, the microinclusion additive is polymeric in nature and possesses a relatively high molecular weight to help improve the melt strength and stability of the thermoplastic composition. Typically, the microinclusion additive polymer may be generally incompatible with the matrix polymer. In this manner, the additive can better become dispersed as discrete phase domains within a continuous phase of the matrix polymer. The discrete domains are capable of absorbing energy that arises from an external force, which increases the overall toughness and strength of the resulting material. The domains may have a variety of different shapes, such as elliptical, spherical, cylindrical, plate-like, tubular, etc. In one embodiment, for example, the domains have a substantially elliptical shape. The physical dimension of an individual domain is typically small enough to minimize the propagation of cracks through the polymeric material upon the application of an external stress, but large enough to initiate microscopic plastic deformation and allow for shear zones at and around particle inclusions.
The microinclusion additive may have a certain melt flow rate (or viscosity) to ensure that the discrete domains and resulting pores can be adequately maintained. For example, if the melt flow rate of the additive is too high, it tends to flow and disperse uncontrollably through the continuous phase. This results in lamellar, plate-like domains or co-continuous phase structures that are difficult to maintain and also likely to prematurely fracture. Conversely, if the melt flow rate of the additive is too low, it tends to clump together and form very large elliptical domains, which are difficult to disperse during blending. This may cause uneven distribution of the additive through the entirety of the continuous phase. In this regard, the present inventors have discovered that the ratio of the melt flow rate of the microinclusion additive to the melt flow rate of the matrix polymer is typically from about 0.5 to about 10, in some embodiments from about 1 to about 8, and in some embodiments, from about 2 to about 6. The microinclusion additive may, for example, have a melt flow rate of from about 5 to about 200 grams per 10 minutes, in some embodiments from about 20 to about 150 grams per 10 minutes, and in some embodiments, from about 40 to about 100 grams per 10 minutes, determined at a load of 2160 grams and at a temperature at least about 40° C. above its melting temperature (e.g., 210° C.).
In addition to the properties noted above, the mechanical characteristics of the microinclusion additive may also be selected to achieve the desired porous network. For example, applied with an external force, stress concentrations (e.g., including normal or shear stresses) and shear and/or plastic yielding zones may be initiated at and around the discrete phase domains as a result of stress concentrations that arise from a difference in the elastic modulus of the additive and matrix polymer. Larger stress concentrations promote more intensive localized plastic flow at the domains, which allows them to become significantly elongated when stresses are imparted. These elongated domains can allow the composition to exhibit a more pliable and softer behavior. To enhance the stress concentrations, the microinclusion additive may be selected to have a relatively high Young's modulus of elasticity in comparison to the polyolefin matrix. For example, the ratio of the modulus of elasticity of the additive to that of polyolefin matrix is typically from about 1 to about 250, in some embodiments from about 2 to about 100, and in some embodiments, from about 2 to about 50. The modulus of elasticity of the microinclusion additive may, for instance, range from about 200 to about 3,500 Megapascals (MPa), in some embodiments from about 300 to about 2,000 MPa, and in some embodiments, from about 400 to about 1,500 MPa. To the contrary, the modulus of elasticity of the polyolefin may, for instance, range from about 100 to about 1,500 MPa, and in some embodiments, from about 200 to about 1000 MPa. Alternatively, the modulus of elasticity of microinclusion additive can be lower than the modulus of elasticity of polyolefin matrix. The modulus of elasticity may, for example, range from about 10 MPa to about 100 MPa, and optionally from about 20 MPA to about 80 MPa.
While a wide variety of microinclusion additives may be employed that have the properties identified above, particularly suitable examples of such additives may include styrenic copolymers (e.g., styrene-butadiene-styrene, styrene-isoprene-styrene, styrene-ethylene-propylene-styrene, styrene-ethylene-butadiene-styrene, etc.); fluoropolymers, such as polyvinyl chloride (PVC), polytetrafluoroethylene (PTFE), polychlorotrifluoroethylene (PCTFE), etc.; polyvinyl alcohols; polyvinyl acetates; polyesters, such as aliphatic polyesters, such as polycaprolactone, polyesteramides, polylactic acid (PLA) and its copolymers, polyglycolic acid, polyalkylene carbonates (e.g., polyethylene carbonate), poly-3-hydroxybutyrate (PHB), poly-3-hydroxyvalerate (PHV), poly-3-hydroxybutyrate-co-4-hydroybutyrate, poly-3-hydroxybutyrate-co-3-hydroxyvalerate copolymers (PHBV), poly-3-hydroxybutyrate-co-3-hydroxyhexanoate, poly-3-hydroxybutyrate-co-3-hydroxyoctanoate, poly-3-hydroxybutyrate-co-3-hydroxydecanoate, poly-3-hydroxybutyrate-co-3-hydroxyoctadecanoate, and succinate-based aliphatic polymers (e.g., polybutylene succinate, polybutylene succinate adipate, polyethylene succinate, etc.), aliphatic-aromatic copolyesters (e.g., polybutylene adipate terephthalate, polyethylene adipate terephthalate, polyethylene adipate isophthalate, polybutylene adipate isophthalate, etc.), aromatic polyesters (e.g., polyethylene terephthalate, polybutylene terephthalate, etc.); and so forth.
Particularly suitable are microinclusion additives that are generally rigid in nature to the extent that they have a relatively high glass transition temperature. For example, the glass transition temperature (“Tg”) may be about 0° C. or more, in some embodiments from about 5° C. to about 100° C., in some embodiments from about 30° C. to about 80° C., and in some embodiments, from about 50° C. to about 75° C. The glass transition temperature may be determined by dynamic mechanical analysis in accordance with ASTM E1640-13.
One particularly suitable rigid polyester is polylactic acid, which may generally be derived from monomer units of any isomer of lactic acid, such as levorotory-lactic acid (“L-lactic acid”), dextrorotatory-lactic acid (“D-lactic acid”), meso-lactic acid, or mixtures thereof. Monomer units may also be formed from anhydrides of any isomer of lactic acid, including L-lactide, D-lactide, meso-lactide, or mixtures thereof. Cyclic dimers of such lactic acids and/or lactides may also be employed. Any known polymerization method, such as polycondensation or ring-opening polymerization, may be used to polymerize lactic acid. A small amount of a chain-extending agent (e.g., a diisocyanate compound, an epoxy compound or an acid anhydride) may also be employed. The polylactic acid may be a homopolymer or a copolymer, such as one that contains monomer units derived from L-lactic acid and monomer units derived from D-lactic acid. Although not required, the rate of content of one of the monomer unit derived from L-lactic acid and the monomer unit derived from D-lactic acid is preferably about 85 mole % or more, in some embodiments about 90 mole % or more, and in some embodiments, about 95 mole % or more. Multiple polylactic acids, each having a different ratio between the monomer unit derived from L-lactic acid and the monomer unit derived from D-lactic acid, may be blended at an arbitrary percentage. Of course, polylactic acid may also be blended with other types of polymers (e.g., polyolefins, polyesters, etc.).
In one particular embodiment, the polylactic acid has the following general structure:
One specific example of a suitable polylactic acid polymer that may be used in the present invention is commercially available from Biomer, Inc. of Krailling, Germany) under the name BIOMER™ L9000. Other suitable polylactic acid polymers are commercially available from Natureworks LLC of Minnetonka, Minn. (NATUREWORKS®) or Mitsui Chemical (LACEA™). Still other suitable polylactic acids may be described in U.S. Pat. Nos. 4,797,468; 5,470,944; 5,770,682; 5,821,327; 5,880,254; and 6,326,458, which are incorporated herein in their entirety by reference thereto for all purposes.
The polylactic acid typically has a number average molecular weight (“Mn”) ranging from about 40,000 to about 180,000 grams per mole, in some embodiments from about 50,000 to about 160,000 grams per mole, and in some embodiments, from about 80,000 to about 120,000 grams per mole. Likewise, the polymer also typically has a weight average molecular weight (“Mw”) ranging from about 80,000 to about 250,000 grams per mole, in some embodiments from about 100,000 to about 200,000 grams per mole, and in some embodiments, from about 110,000 to about 160,000 grams per mole. The ratio of the weight average molecular weight to the number average molecular weight (“Mw/Mn”), i.e., the “polydispersity index”, is also relatively low. For example, the polydispersity index typically ranges from about 1.0 to about 3.0, in some embodiments from about 1.1 to about 2.0, and in some embodiments, from about 1.2 to about 1.8. The weight and number average molecular weights may be determined by methods known to those skilled in the art.
Some types of neat polyesters (e.g., polylactic acid) can absorb water from the ambient environment such that it has a moisture content of about 500 to 600 parts per million (“ppm”), or even greater, based on the dry weight of the starting polylactic acid. Moisture content may be determined in a variety of ways as is known in the art, such as in accordance with ASTM D 7191-05, such as described below. Because the presence of water during melt processing can hydrolytically degrade the polyester and reduce its molecular weight, it is sometimes desired to dry the polyester prior to blending. In most embodiments, for example, it is desired that the renewable polyester have a moisture content of about 300 parts per million (“ppm”) or less, in some embodiments about 200 ppm or less, in some embodiments from about 1 to about 100 ppm prior to blending with the microinclusion additive. Drying of the polyester may occur, for instance, at a temperature of from about 50° C. to about 100° C., and in some embodiments, from about 70° C. to about 80° C.
Regardless of the materials employed, the relative percentage of the microinclusion additive in the thermoplastic composition is selected to achieve the desired properties without significantly impacting the resulting composition. For example, the microinclusion additive is typically employed in an amount of from about 1 wt. % to about 30 wt. %, in some embodiments from about 2 wt. % to about 25 wt. %, and in some embodiments, from about 5 wt. % to about 20 wt. % of the thermoplastic composition, based on the weight of the continuous phase (e.g., matrix polymer(s)). The concentration of the microinclusion additive in the entire thermoplastic composition may likewise constitute from about 0.1 wt. % to about 30 wt. %, in some embodiments from about 0.5 wt. % to about 25 wt. %, and in some embodiments, from about 1 wt. % to about 20 wt. %.
E. Other Components
A wide variety of ingredients may be employed in the composition for a variety of different reasons. For instance, in one particular embodiment, an interphase modifier may be employed in the thermoplastic composition to help reduce the degree of friction and connectivity between the nanoinclusion and/or microinclusion additives and polyolefin matrix, and thus enhance the degree and uniformity of debonding. In this manner, the pores can become distributed in a more homogeneous fashion throughout the composition. The modifier may be in a liquid or semi-solid form at room temperature (e.g., 25° C.) so that it possesses a relatively low viscosity, allowing it to be more readily incorporated into the thermoplastic composition and to easily migrate to the polymer surfaces. By reducing physical forces at the interfaces of the polyolefin matrix and the additive, it is believed that the low viscosity, hydrophobic nature of the modifier can help facilitate debonding. As used herein, the term “hydrophobic” typically refers to a material having a contact angle of water in air of about 40° or more, and in some cases, about 60° or more. In contrast, the term “hydrophilic” typically refers to a material having a contact angle of water in air of less than about 40° . One suitable test for measuring the contact angle is ASTM D5725-99 (2008).
Although not required, the interphase modifier may be particularly suitable in embodiments in which a microinclusion additive is employed and in which the nanoinclusion additive is a solid (e.g., polymeric material). Suitable hydrophobic, low viscosity interphase modifiers may include, for instance, the liquids and/or semi-solids referenced above. One particularly suitable interphase modifier is polyether polyol, such as commercially available under the trade name PLURIOL® WI from BASF Corp. Another suitable modifier is a partially renewable ester, such as commercially available under the trade name HALLGREEN® IM from Hallstar.
When employed, the interphase modifier may constitute from about 0.1 wt. % to about 20 wt. %, in some embodiments from about 0.5 wt. % to about 15 wt. %, and in some embodiments, from about 1 wt. % to about 10 wt. % of the thermoplastic composition, based on the weight of the continuous phase. The concentration of the interphase modifier in the entire thermoplastic composition may likewise constitute from about 0.05 wt. % to about 20 wt. %, in some embodiments from about 0.1 wt. % to about 15 wt. %, and in some embodiments, from about 0.5 wt. % to about 10 wt. %. In the amounts noted above, the interphase modifier has a character that enables it to readily migrate to the interfacial surface of the polymers and facilitate debonding without disrupting the overall melt properties of the thermoplastic composition. For example, the melt flow rate of the thermoplastic composition may also be similar to that of the polyolefin matrix. For example, the melt flow rate of the composition (on a dry basis) may be from about 0.1 to about 250 grams per 10 minutes, in some embodiments from about 0.5 to about 200 grams per 10 minutes, and in some embodiments, from about 5 to about 150 grams per 10 minutes, determined at a load of 2160 grams and at 190° C. in accordance with ASTM D1238.
Compatibilizers may also be employed that improve interfacial adhesion and reduce the interfacial tension between the domain and the matrix, thus allowing the formation of smaller domains during mixing. Examples of suitable compatibilizers may include, for instance, copolymers functionalized with epoxy or maleic anhydride chemical moieties. An example of a maleic anhydride compatibilizer is polypropylene-grafted-maleic anhydride, which is commercially available from Arkema under the trade names Orevac™ 18750 and Orevac™ CA 100. When employed, compatibilizers may constitute from about 0.05 wt. % to about 10 wt. %, in some embodiments from about 0.1 wt. % to about 8 wt. %, and in some embodiments, from about 0.5 wt. % to about 5 wt. % of the thermoplastic composition, based on the weight of the continuous phase.
If desired, a butene polymer (homopolymer or copolymer) may also be employed that can act as a plasticizer of the polyolefin matrix, thereby improving its fluidity and ductility, and in turn, its ability to be processed at relatively high speeds without a substantial degree of breakage. When employed, such butene polymers typically constitute from about 0.01 wt. % to about 15 wt. %, in some embodiments from about 0.1 wt. % to about 12 wt. %, and in some embodiments, from about 0.5 wt. % to about 10 wt. %, based on the weight of the continuous phase (e.g., matrix polymer(s)). The butene polymers may also be employed in an amount of from about 0.01 wt. % to about 15 wt. %, in some embodiments from about 0.1 wt. % to about 12 wt. %, and in some embodiments, from about 0.5 wt. % to about 10 wt. %, based on the total weight of the composition.
The term “butene polymer” generally refers to a homo- or co-polymer of an alkene monomer having four carbon atoms, including 1-butene (α-butylene), 2-butene (cis-β-butylene or trans-β-butylene), 2-methylpropene (isobutylene), cyclobutene, as well as combinations thereof. The butene polymer may also contain other monomers, such as propene. In one embodiment, for example, the butene polymer may be a homopolymer of butene-1 (referred to as “polybutylene”). Other suitable polymers may include homopolymers of isobutylene (referred to as “polyisobutylene”) and copolymers of 1-butene, 2-butene and/or isobutylene (referred to as “polybutene”). In one particular embodiment, for instance, the butene polymer may be polybutylene (also known as poly-1-butene). Polybutylene can be made through a Ziegler-Natta low-pressure polymerization of 1-butene, such as by polymerizing 1-butene with catalysts of TiCl3, TiCl3AlCl3, and/or Al(C2H5)2Cl. While the molecular weight of the butene polymer may vary based on the type of polymer and degree of polymerization, it is typically desired that the butene polymer has a relatively low molecular weight, such as a number average molecular weight of about 10,000 grams per mole or less, in some embodiments about 5,000 grams per mole or less, in some embodiments about 2,000 grams per mole or less, and in some embodiments, from about 100 to about 1,000 grams per mole. Of course, it should be understood that higher molecular weight polymers may also be employed, such as those having a number average molecular weight of from about 10,000 to about 250,000 grams per mole. The density of the butene polymer is also typically about 0.910 grams per cubic centimeter or less, in some embodiments about 0.900 grams per cubic centimeter or less, and in some embodiments, from about 0.810 to about 0.890 grams per cubic centimeter, as determined in accordance with ASTM D4052-11. The kinematic viscosity of the butene polymer may likewise range from about 50 to about 2,000 centistokes (“cs”), in some embodiments from about 100 to about 1,500 cs, and in some embodiments, from about 200 to about 1,000 cs as determined at a temperature of 40° C. in accordance with ASTM D445-14e2.
Other suitable materials that may also be used in the thermoplastic composition, such as catalysts, antioxidants, stabilizers, surfactants, waxes, solid solvents, particulates, nanofillers, and other materials added to enhance the processability and mechanical properties of the thermoplastic composition. Nevertheless, one beneficial aspect of the present invention is that good properties may be provided without the need for various conventional additives, such as blowing agents (e.g., chlorofluorocarbons, hydrochlorofluorocarbons, hydrocarbons, carbon dioxide, supercritical carbon dioxide, nitrogen, etc.) and pore-initiating inorganic oxide fillers (e.g., calcium carbonate). In fact, the thermoplastic composition may be generally free of blowing agents and/or pore-initiating inorganic oxide fillers. For example, such blowing agents and/or fillers may be present in an amount of no more than about 1 wt. %, in some embodiments no more than about 0.5 wt. %, and in some embodiments, from about 0.001 wt. % to about 0.2 wt. % of the thermoplastic composition. Further, due to its stress whitening properties, as described in more detail below, the resulting composition may achieve an opaque color (e.g., white) without the need for conventional pigments, such as titanium dioxide. In certain embodiments, for example, pigments may be present in an amount of no more than about 1 wt. %, in some embodiments no more than about 0.5 wt. %, and in some embodiments, from about 0.001 wt. % to about 0.2 wt. % of the thermoplastic composition.
The polyolefin material of the present invention may generally be formed by drawing the thermoplastic composition. To form the initial thermoplastic composition, the components are typically blended together using any of a variety of known techniques. In one embodiment, for example, the components may be supplied separately or in combination. For instance, the components may first be dry mixed together to form an essentially homogeneous dry mixture, and they may likewise be supplied either simultaneously or in sequence to a melt processing device that dispersively blends the materials. Batch and/or continuous melt processing techniques may be employed. For example, a mixer/kneader, Banbury mixer, Farrel continuous mixer, single-screw extruder, twin-screw extruder, roll mill, etc., may be utilized to blend and melt process the materials. Particularly suitable melt processing devices may be a co-rotating, twin-screw extruder (e.g., ZSK-30 extruder available from Werner & Pfleiderer Corporation of Ramsey, New Jersey or a Thermo Prism™ USALAB 16 extruder available from Thermo Electron Corp., Stone, England). Such extruders may include feeding and venting ports and provide high intensity distributive and dispersive mixing. For example, the components may be fed to the same or different feeding ports of the twin-screw extruder and melt blended to form a substantially homogeneous melted mixture. If desired, other additives may also be injected into the polymer melt and/or separately fed into the extruder at a different point along its length.
Regardless of the particular processing technique chosen, the resulting melt blended composition typically contains nano-scale domains of the nanoinclusion additive and optionally micro-scale domains of the microinclusion additive. The degree of shear/pressure and heat may be controlled to ensure sufficient dispersion, but not so high as to adversely reduce the size of the domains so that they are incapable of achieving the desired properties. For example, blending typically occurs at a temperature of from about 180° C. to about 300° C., in some embodiments from about 185° C. to about 250° C., and in some embodiments, from about 190° C. to about 240° C. Likewise, the apparent shear rate during melt processing may range from about 10 seconds−1 to about 3000 seconds−1, in some embodiments from about 50 seconds−1 to about 2000 seconds−1, and in some embodiments, from about 100 seconds−1 to about 1200 seconds−1. The apparent shear rate may be equal to 4Q/R3, where Q is the volumetric flow rate (“m3/s”) of the polymer melt and R is the radius (“m”) of the capillary (e.g., extruder die) through which the melted polymer flows. Of course, other variables, such as the residence time during melt processing, which is inversely proportional to throughput rate, may also be controlled to achieve the desired degree of homogeneity.
To achieve the desired shear conditions (e.g., rate, residence time, shear rate, melt processing temperature, etc.), the speed of the extruder screw(s) may be selected with a certain range. Generally, an increase in product temperature is observed with increasing screw speed due to the additional mechanical energy input into the system. For example, the screw speed may range from about 50 to about 600 revolutions per minute (“rpm”), in some embodiments from about 70 to about 500 rpm, and in some embodiments, from about 100 to about 300 rpm. This may result in a temperature that is sufficiently high to disperse the nanoinclusion additive without adversely impacting the size of the resulting domains. The melt shear rate, and in turn the degree to which the additives are dispersed, may also be increased through the use of one or more distributive and/or dispersive mixing elements within the mixing section of the extruder. Suitable distributive mixers for single screw extruders may include, for instance, Saxon, Dulmage, Cavity Transfer mixers, etc. Likewise, suitable dispersive mixers may include Blister ring, Leroy/Maddock, CRD mixers, etc. As is well known in the art, the mixing may be further improved by using pins in the barrel that create a folding and reorientation of the polymer melt, such as those used in Buss Kneader extruders, Cavity Transfer mixers, and Vortex Intermeshing Pin (VIP) mixers.
Regardless of the particular manner in which it is formed, the composition may be drawn in the longitudinal direction (e.g., machine direction), transverse direction (e.g., cross-machine direction), etc., as well as combinations thereof, to form a porous network. If desired, the composition may be drawn in-line as it is being formed in to a film, fiber, etc. Alternatively, the composition may be drawn in its solid state after being formed into a film, fiber, etc., before and/or after lamination to any optional materials. By “solid state” drawing, it is generally meant that the composition is kept at a temperature below the melting temperature of the polyolefin matrix polymer. Among other things, this helps to ensure that the polymer chains are not altered to such an extent that the porous network becomes unstable. For example, the composition may be drawn at a temperature of from about −50° C. to about 120° C., in some embodiments from about −40° C. to about 110° C., in some embodiments, from about −20° C. to about 100° C., and in some embodiments, from about 0° C. to about 50° C. In certain cases, the drawing temperature may optionally be at least about 10° C., in some embodiments at least about 20° C., and in some embodiments, at least about 30° C. below the glass transition temperature of the component having the highest glass transition temperature (e.g., microinclusion additive). In such embodiments, the composition may be drawn at a temperature of from about 0° C. to about 50° C., in some embodiments from about 15° C. to about 40° C., and in some embodiments, from about 20° C. to about 30° C.
To perform the desired drawing, the thermoplastic composition may be formed into a precursor shape, drawn, and thereafter converted into the desired material (e.g., film, fiber, molded article, etc.). In one embodiment, the precursor shape may be a film having a thickness of from about 1 to about 5000 micrometers, in some embodiments from about 2 to about 4000 micrometers, in some embodiments from about 5 to about 2500 micrometers, and in some embodiments, from about 10 to about 500 micrometers. As an alternative to forming a precursor shape, the thermoplastic composition may also be drawn in situ as it is being shaped into the desired form for the polyolefin material. In one embodiment, for example, the thermoplastic composition may be drawn as it is being formed into a film or fiber.
Regardless, various drawing techniques may be employed, such as aspiration (e.g., fiber draw units), tensile frame drawing, biaxial drawing, multi-axial drawing, profile drawing, vacuum drawing, etc. In one embodiment, for example, the composition may be in the form of a film that is drawn with a machine direction orienter (“MDO”), such as commercially available from Marshall and Willams, Co. of Providence, R.I. MDO units typically have a plurality of drawing rolls (e.g., from 5 to 8) which progressively draw and thin the film in the machine direction. The composition may be drawn in either single or multiple discrete drawing operations. It should be noted that some of the rolls in an MDO apparatus may not be operating at progressively higher speeds. To draw the composition in the manner described above, it is typically desired that the rolls of the MDO are not heated. Nevertheless, if desired, one or more rolls may be heated to a slight extent to facilitate the drawing process so long as the temperature of the composition remains below the ranges noted above.
In other embodiments, the composition may be in the form of a fiber that is drawn to form the desired porous network. As used herein, the term “fiber” generally refers to an elongated extrudate formed by passing a polymer through a forming orifice, such as a die. Unless noted otherwise, the term “fiber” includes both discontinuous fibers having a definite length and substantially continuous filaments. Substantially filaments may, for instance, have a length much greater than their diameter, such as a length to diameter ratio (“aspect ratio”) greater than about 15,000 to 1, and in some cases, greater than about 50,000 to 1.
Fibers formed from the thermoplastic composition may generally have any desired configuration, including monocomponent and multicomponent (e.g., sheath-core configuration, side-by-side configuration, segmented pie configuration, island-in-the-sea configuration, and so forth). Hollow fibers (monocomponent and/or multicomponent) may also be employed, such as described in U.S. Pat. No. 6,642,429 to Carter, et al. In some embodiments, the fibers may contain one or more additional polymers as a component (e.g., bicomponent) or constituent (e.g., biconstituent) to further enhance strength, processibility, and/or other properties. For instance, the thermoplastic composition may form a core component of a sheath/core bicomponent fiber, while an additional polymer may form the sheath component, or vice versa. The additional polymer may be any polymer desired, such as polyesters, e.g., polylactic acid, polyethylene terephthalate, etc.; polyolefins, e.g., polyethylene, polypropylene, polybutylene, and so forth; polytetrafluoroethylene; polyvinyl acetate; polyvinyl chloride acetate; polyvinyl butyral; acrylic resins, e.g., polyacrylate, polymethylacrylate, polymethylmethacrylate, and so forth; polyamides, e.g., nylon; polyvinyl chloride; polyvinylidene chloride; polystyrene; polyvinyl alcohol; and polyurethanes.
Any of a variety of processes may be used to form the fibers. For example, the thermoplastic composition described above may be extruded through a spinneret and quenched. Referring to
The extruder 12 is heated to a temperature sufficient to extrude the melted polymer. The extruded composition is then passed through a polymer conduit 16 to a spinneret 18. For example, the spinneret 18 may include a housing containing a spin pack having a plurality of plates stacked one on top of each other and having a pattern of openings arranged to create flow paths for directing polymer components. The spinneret 18 also has openings arranged in one or more rows. The openings form a downwardly extruding curtain of filaments when the polymers are extruded therethrough. The process 10 also employs a quench blower 20 positioned adjacent the curtain of fibers extending from the spinneret 18. Air from the quench air blower 20 quenches the fibers extending from the spinneret 18. The quench air may be directed from one side of the fiber curtain as shown in
To form a fiber with the desired length, the quenched fibers are generally melt drawn, such as using a fiber draw unit 22 as shown in
Draw Down Ratio=A/B
wherein,
A is the linear speed of the fiber after melt drawing (e.g., godet speed) and is directly measured; and
B is the linear speed of the extruded fiber and can be calculated as follows:
Extruder linear fiber speed=C/(25*π*D*E2)
wherein,
C is the throughput through a single hole (grams per minute);
D is the melt density of the polymer (grams per cubic centimeter); and
E is the diameter of the orifice (in centimeters) through which the fiber is extruded. In certain embodiments, the draw down ratio may be from about 20:1 to about 4000:1, in some embodiments from about 25:1 to about 2000:1, and in some embodiments, from about 50:1 to about 1000:1 and in some embodiments from about 75:1 to about 800:1.
Once formed, the fibers may be deposited through the outlet opening of the fiber draw unit 22 and onto a godet roll 42. If desired, the fibers collected on the godet roll 42 may optionally be subjected to additional in line processing and/or converting steps (not shown) as will be understood by those skilled in the art. For example, fibers may be collected and thereafter crimped, texturized, and/or and cut to an average fiber length in the range of from about 3 to about 80 millimeters, in some embodiments from about 4 to about 65 millimeters, and in some embodiments, from about 5 to about 50 millimeters. The staple fibers may then be incorporated into a nonwoven web as is known in the art, such as bonded carded webs, through-air bonded webs, etc. Once formed, the resulting fibers may be drawn in their solid state to form the desired porous network. If desired, the fibers may be drawn in-line as the fibers are being formed. Alternatively, the fibers may be drawn in their solid state after they are formed.
The degree of drawing depends in part of the nature of the material being drawn (e.g., fiber, film, etc.). The composition is typically drawn (e.g., in the machine direction) to a draw ratio of from about 1.1 to about 3.5, in some embodiments from about 1.2 to about 3.0, and in some embodiments, from about 1.3 to about 2.5. The draw ratio may be determined by dividing the length of the drawn material by its length before drawing. The draw rate may also vary to help achieve the desired properties, such as within the range of from about 5% to about 1500% per minute of deformation, in some embodiments from about 20% to about 1000% per minute of deformation, and in some embodiments, from about 25% to about 850% per minute of deformation. Although the composition is typically drawn without the application of external heat (e.g., heated rolls), such heat might be optionally employed to improve processability, reduce draw force, increase draw rates, and improve fiber uniformity.
Drawing may occur in one or multiple stages. In
Drawing in the manner described above can result in the formation of pores that have a “nano-scale” cross-sectional dimension (“nanopores”), such as about 800 nanometers or less, in some embodiments from about 5 to about 700 nanometers, and in some embodiments, from about 10 to about 500 nanometers. The nanopores may also have an average axial dimension (e.g., length) of from about 100 to about 5000 nanometers, in some embodiments from about 50 to about 2000 nanometers, and in some embodiments, from about 100 to about 1000 nanometers. Micropores may also be formed during drawing that have an average cross-sectional dimension of about 0.2 micrometers or more, in some embodiments about 0.5 micrometers or more, and in some embodiments, from about 0.5 micrometers to about 5 micrometers. In certain cases, the axial dimension of the micropores and/or nanopores may be larger than the cross-sectional dimension so that the aspect ratio (the ratio of the axial dimension to the cross-sectional dimension) is from about 1 to about 30, in some embodiments from about 1.1 to about 15, and in some embodiments, from about 1.2 to about 5. For example, the axial dimension of the micropores may be 1 micrometer or more, in some embodiments about 1.5 micrometers or more, and in some embodiments, from about 2 to about 30 micrometers.
Regardless of their particular size, the present inventors have discovered that the pores (e.g., nanopores, micropores, or both) can be distributed in a substantially homogeneous fashion throughout the material. For example, the pores may be distributed in columns that are oriented in a direction generally perpendicular to the direction in which a stress is applied. These columns may be generally parallel to each other across the width of the material. Without intending to be limited by theory, it is believed that the presence of such a homogeneously distributed porous network can result in a high thermal resistance as well as good mechanical properties (e.g., energy dissipation under load and impact strength). This is in stark contrast to conventional techniques for creating pores that involve the use of blowing agents, which tend to result in an uncontrolled pore distribution and poor mechanical properties.
In addition to forming a porous network, drawing can also significantly increase the axial dimension of certain of the discrete domains so that they have a generally linear, elongated shape. For example, the elongated micro-scale domains may have an average axial dimension that is about 10% or more, in some embodiments from about 20% to about 500%, and in some embodiments, from about 50% to about 250% greater than the axial dimension of the domains prior to drawing. The axial dimension (e.g., length) after drawing may, for instance, range from about 1 μm to about 400 μm, in some embodiments from about 5 μm to about 200 μm, and in some embodiments from about 10 μm to about 150 μm. The micro-scale domains may also be relatively thin and thus have a small cross-sectional dimension, such as from about 0.02 to about 20 micrometers, in some embodiments from about 0.1 to about 10 micrometers, and in some embodiments, from 0.4 to about 5 micrometers. This may result in an aspect ratio for the domains (the ratio of the axial dimension to a dimension orthogonal to the axial dimension) of from about 2 to about 150, in some embodiments from about 3 to about 100, and in some embodiments, from about 4 to about 50. Due to their small size, the nano-scale domains are not typically elongated in the same manner as the micro-scale domains. Thus, the nano-scale domains may retain an average axial dimension (e.g., length) of from about 1 to about 1000 nanometers, in some embodiments from about 5 to about 800 nanometers, in some embodiments from about 10 to about 500 nanometers, and in some embodiments from about 20 to about 200 nanometers.
Although by no means required, the polyolefin material may be converted into a different form before being employed in a final article or product. When fibers are formed, for instance, they may be subsequently formed into a nonwoven web structure by randomly depositing the fibers onto a forming surface (optionally with the aid of a vacuum) and then bonding the resulting web using any known technique. The nonwoven web may be formed before or after the fibers are drawn. In certain embodiments, for instance, it may be desired to form a nonwoven web from a plurality of fibers, and thereafter draw the fibers by stretching the nonwoven web to the extent desired to form the porous network. In an alternative embodiment, an endless forming surface may simply be positioned below a fiber aspiration unit that draws the fibers to the desired extent before the web is formed.
Once formed, the nonwoven web may then be bonded using any conventional technique, such as with an adhesive or autogenously (e.g., fusion and/or self-adhesion of the fibers without an applied external adhesive). Autogenous bonding, for instance, may be achieved through contact of the fibers while they are semi-molten or tacky, or simply by blending a tackifying resin and/or solvent with the polymer used to form the fibers. Suitable autogenous bonding techniques may include ultrasonic bonding, thermal bonding, through-air bonding, calendar bonding, and so forth. For example, the web may be further bonded or embossed with a pattern by a thermo-mechanical process in which the web is passed between a heated smooth anvil roll and a heated pattern roll. The pattern roll may have any raised pattern which provides the desired web properties or appearance. Desirably, the pattern roll defines a raised pattern which defines a plurality of bond locations which define a bond area between about 2% and 30% of the total area of the roll. Exemplary bond patterns include, for instance, those described in U.S. Pat. No. 3,855,046 to Hansen et al., U.S. Pat. No. 5,620,779 to Levy et al., U.S. Pat. No. 5,962,112 to Haynes et al., U.S. Pat. No. 6,093,665 to Sayovitz et al., as well as U.S. Design Pat. Nos. 428,267 to Romano et al.; 390,708 to Brown; 418,305 to Zander, et al.; 384,508 to Zander, et al.; 384,819 to Zander, et al.; 358,035 to Zander, et al.; and 315,990 to Blenke, et al. The pressure between the rolls may be from about 5 to about 2000 pounds per lineal inch. The pressure between the rolls and the temperature of the rolls is balanced to obtain desired web properties or appearance while maintaining cloth like properties. As is well known to those skilled in the art, the temperature and pressure required may vary depending upon many factors including but not limited to, pattern bond area, polymer properties, fiber properties and nonwoven properties.
In addition to spunbond webs, a variety of other nonwoven webs may also be formed from the thermoplastic composition in accordance with the present invention, such as meltblown webs, bonded carded webs, wet-laid webs, airlaid webs, coform webs, hydraulically entangled webs, etc. For example, the thermoplastic composition may be extruded through a plurality of fine die capillaries into a converging high velocity gas (e.g., air) streams that attenuate the fibers to reduce their diameter. Thereafter, the meltblown fibers are carried by the high velocity gas stream and are deposited on a collecting surface to form a web of randomly dispersed meltblown fibers. Alternatively, the polymer may be formed into a carded web by placing bales of fibers formed from the thermoplastic composition into a picker that separates the fibers. Next, the fibers are sent through a combing or carding unit that further breaks apart and aligns the fibers in the machine direction so as to form a machine direction-oriented fibrous nonwoven web. Once formed, the nonwoven web is typically stabilized by one or more known bonding techniques as described above to form a bonded carded web. Composites and/or laminates may also be formed from the fibers.
Due to its unique and beneficial properties, the resulting polyolefin material of the present invention is well suited for use in a variety of different types of articles, such as an absorbent article, packaging film, barrier film, medical product (e.g., gown, surgical drape, facemask, head covering, surgical cap, shoe covering, sterilization wrap, warming blanket, heating pad, etc.), and so forth. For example, the polyolefin material may be incorporated into an “absorbent article” that is capable of absorbing water or other fluids. Examples of some absorbent articles include, but are not limited to, personal care absorbent articles, such as diapers, training pants, absorbent underpants, incontinence articles, feminine hygiene products (e.g., sanitary napkins), swim wear, baby wipes, mitt wipe, and so forth; medical absorbent articles, such as garments, fenestration materials, underpads, bedpads, bandages, absorbent drapes, and medical wipes; food service wipers; clothing articles; pouches, and so forth. Materials and processes suitable for forming such articles are well known to those skilled in the art. Absorbent articles, for instance, typically include a substantially liquid-impermeable layer (e.g., outer cover), a liquid-permeable layer (e.g., bodyside liner, surge layer, etc.), and an absorbent core. In one embodiment, for example, the polyolefin material may be in the form of a fibrous material (e.g., nonwoven web) and used to form an outer cover of an absorbent article. If desired, the nonwoven web may be laminated to a liquid-impermeable film that is either vapor-permeable or vapor-impermeable. The polyolefin material may likewise be in the form of a film that is used in an absorbent article, such as a liquid-impermeable film of the outer cover, which is either vapor-permeable or vapor-impermeable.
Absorbent articles, for instance, generally include an absorbent member (e.g., core layer, surge layer, transfer delay layer, wrapsheet, ventilation layer, etc.) positioned between a backsheet and a topsheet. The absorbent article may also contain other components as is known in the art, such as side panels, containment flaps, ears, waist or leg bands, etc. Generally speaking, the polyolefin material of the present invention may be employed in any layer or component of the absorbent article, such as the topsheet, backsheet, and/or absorbent member. When employed in certain layers or components (e.g., backsheet), it may be desirable to laminate the polyolefin material of the present invention to another layer (e.g., film).
In this regard, various exemplary embodiments of the absorbent article will be described. Referring to
As indicated above, the backsheet 217 may contain the polyolefin material of the present invention. If desired, the nonwoven web may be positioned so that it defines a garment-facing surface 333 of the absorbent article 201. The absorbent article 201 also includes a topsheet 205. The topsheet 205 is generally designed to contact the body of the user and is liquid-permeable. For example, the topsheet 205 may define a body-facing surface 218, which is typically compliant, soft feeling, and non-irritating to the wearer's skin. If desired, the topsheet 205 may contain the polyolefin material (e.g., nonwoven web) of the present invention. For example, the polyolefin material may be positioned so that it defines the body-facing surface 218 if so desired. The topsheet may surround the absorbent core layer 203 so that it completely encases the absorbent article. Alternatively, the topsheet 205 and the backsheet 217 may extend beyond the absorbent member and be peripherally joined together, either entirely or partially, using known techniques, such as by adhesive bonding, ultrasonic bonding, etc. As indicated above, the topsheet 205 may include the polyolefin material of the present invention. The topsheet 205 may also include a conventional a nonwoven web (e.g., spunbond web, meltblown web, or bonded carded web). Other exemplary topsheet constructions that contain a nonwoven web are described in U.S. Pat. Nos. 5,192,606; 5,702,377; 5,931,823; 6,060,638; and 6,150,002, as well as U.S. Patent Application Publication Nos. 2004/0102750, 2005/0054255, and 2005/0059941. The topsheet 205 may also contain a plurality of apertures formed therethrough to permit body fluid to pass more readily into the absorbent core layer 203. The apertures may be randomly or uniformly arranged throughout the topsheet 205, or they may be located only in the narrow longitudinal band or strip arranged along the longitudinal axis of the absorbent article. The apertures permit rapid penetration of body fluid down into the absorbent member. The size, shape, diameter and number of apertures may be varied to suit one's particular needs.
The absorbent article also contains an absorbent member positioned between the topsheet and the backsheet. The absorbent member may be formed from a single absorbent layer or a composite containing separate and distinct absorbent layer. It should be understood, however, that any number of absorbent layers may be utilized in the present invention. In
If desired, the absorbent member may also contain a transfer delay layer positioned vertically below the surge layer. The transfer delay layer may contain a material that is less hydrophilic than the other absorbent layers, and may generally be characterized as being substantially hydrophobic. For example, the transfer delay layer may be a polyolefin material (e.g., nonwoven web) formed according to the present invention. The fibers may be round, tri-lobal or poly-lobal in cross-sectional shape and which may be hollow or solid in structure. Typically the webs are bonded, such as by thermal bonding, over about 3% to about 30% of the web area. Other examples of suitable materials that may be used for the transfer delay layer are described in U.S. Pat. No. 4,798,603 to Meyer, et al. and U.S. Pat. No. 5,248,309 to Serbiak, et al. To adjust the performance of the invention, the transfer delay layer may also be treated with a selected amount of surfactant to increase its initial wettability.
The transfer delay layer may generally have any size, such as a length of about 150 mm to about 300 mm. Typically, the length of the transfer delay layer is approximately equal to the length of the absorbent article. The transfer delay layer may also be equal in width to the surge layer, but is typically wider. For example, the width of the transfer delay layer may be from between about 50 mm to about 75 mm, and particularly about 48 mm. The transfer delay layer typically has a basis weight less than that of the other absorbent members. For example, the basis weight of the transfer delay layer is typically less than about 150 grams per square meter (gsm), and in some embodiments, between about 10 gsm to about 100 gsm. If desired, the transfer delay layer may contain the polyolefin material (e.g., nonwoven web) of the present invention.
Besides the above-mentioned components, the absorbent article 201 may also contain various other components as is known in the art. For example, the absorbent article 201 may also contain a substantially hydrophilic wrapsheet (not illustrated) that helps maintain the integrity of the fibrous structure of the absorbent core layer 203. The wrapsheet is typically placed about the absorbent core layer 203 over at least the two major facing surfaces thereof, and composed of an absorbent cellulosic material, such as creped wadding or a high wet-strength tissue. The wrapsheet may be configured to provide a wicking layer that helps to rapidly distribute liquid over the mass of absorbent fibers of the absorbent core layer 203. The wrapsheet material on one side of the absorbent fibrous mass may be bonded to the wrapsheet located on the opposite side of the fibrous mass to effectively entrap the absorbent core layer 203. Furthermore, the absorbent article 201 may also include a ventilation layer (not shown) that is positioned between the absorbent core layer 203 and the backsheet 217. When utilized, the ventilation layer may help insulate the backsheet 217 from the absorbent core layer 203, thereby reducing dampness in the backsheet 217. Examples of such ventilation layers may include a nonwoven web laminated to a breathable film, such as described in U.S. Pat. No. 6,663,611 to Blaney, et al. If desired, the wrapsheet and/or ventilation layer may contain the polyolefin material of the present invention.
In some embodiments, the absorbent article 201 may also include a pair of ears (not shown) that extend from the side edges 232 of the absorbent article 201 into one of the waist regions. The ears may be integrally formed with a selected diaper component. For example, the ears may be integrally formed with the backsheet 217 or from the material employed to provide the top surface, which may include the polyolefin material of the present invention if so desired. In alternative configurations, the ears may be provided by members connected and assembled to the backsheet 217, the top surface, between the backsheet 217 and top surface, or in various other configurations. As noted above, the ears may contain the polyolefin material of the present invention if so desired.
As representatively illustrated in
The absorbent article 201 may include various elastic or stretchable materials, such as a pair of leg elastic members 206 affixed to the side edges 232 to further prevent leakage of body exudates and to support the absorbent core layer 203. In addition, a pair of waist elastic members 208 may be affixed to longitudinally opposed waist edges 215 of the absorbent article 201. The leg elastic members 206 and the waist elastic members 208 are generally adapted to closely fit about the legs and waist of the wearer in use to maintain a positive, contacting relationship with the wearer and to effectively reduce or eliminate the leakage of body exudates from the absorbent article 201. The absorbent article 201 may also include one or more fasteners 230. For example, two flexible fasteners 130 are illustrated in
The various regions and/or components of the absorbent article 201 may be assembled together using any known attachment mechanism, such as adhesive, ultrasonic, thermal bonds, etc. Suitable adhesives may include, for instance, hot melt adhesives, pressure-sensitive adhesives, and so forth. When utilized, the adhesive may be applied as a uniform layer, a patterned layer, a sprayed pattern, or any of separate lines, swirls or dots. In the illustrated embodiment, for example, the backsheet 217 and topsheet 205 are assembled to each other and to the absorbent core layer 203 using an adhesive. Alternatively, the absorbent core layer 203 may be connected to the backsheet 217 using conventional fasteners, such as buttons, hook and loop type fasteners, adhesive tape fasteners, and so forth. Similarly, other diaper components, such as the leg elastic members 206, waist elastic members 208 and fasteners 230, may also be assembled into the absorbent article 201 using any attachment mechanism.
Although various configurations of a diaper have been described above, it should be understood that other diaper and absorbent article configurations are also included within the scope of the present invention. In addition, the present invention is by no means limited to diapers. In fact, any other absorbent article may be formed in accordance with the present invention, including, but not limited to, other personal care absorbent articles, such as training pants, absorbent underpants, adult incontinence products, feminine hygiene products (e.g., sanitary napkins), swim wear, baby wipes, and so forth; medical absorbent articles, such as garments, fenestration materials, underpads, bandages, absorbent drapes, and medical wipes; food service wipers; clothing articles; and so forth.
The polyolefin material may also be employed in a wide variety of other types of articles. Non- limiting examples include, for instance, insulation materials for refrigeration units (e.g., refrigerators, freezers, vending machines, etc.); automotive components (e.g., front and rear seats, headrests, armrests, door panels, rear shelves/package trays, steering wheels and interior trim, dashboards, etc.); building panels and sections (e.g., roofs, wall cavities, under floors, etc.); apparel (e.g., coats, shirts, pants, gloves, aprons, coveralls, shoes, boots, headware, sock liners, etc.); furniture and bedding (e.g., sleeping bags, comforters, etc.); fluid storage/transfer systems (e.g., pipes or tankers for liquid/gas hydrocarbons, liquid nitrogen, oxygen, hydrogen, or crude oil); extreme environments (e.g., underwater or space); food and beverage products (e.g., cups, cup holders, plates, etc.); containers and bottles; and so forth. The polyolefin material may also be used in a “garment”, which is generally meant to include any article that is shaped to fit over a portion of a body. Examples of such articles include, without limitation, clothing (e.g., shirts, pants, jeans, slacks, skirts, coats, activewear, athletic, aerobic, and exercise apparel, swimwear, cycling jerseys or shorts, swimsuit/bathing suit, race suit, wetsuit, bodysuit, etc.), footwear (e.g., shoes, socks, boots, etc.), protective apparel (e.g., firefighter's coat), clothing accessories (e.g., belts, bra straps, side panels, gloves, hosiery, leggings, orthopedic braces, etc.), undergarments (e.g., underwear, t-shirts, etc.), compression garments, draped garments (e.g., kilts loincloths, togas, ponchos, cloaks, shawls, etc.), and so forth.
The present invention may be better understood with reference to the following examples.
The melt flow rate (“MFR”) is the weight of a polymer (in grams) forced through an extrusion rheometer orifice (0.0825-inch diameter) when subjected to a load of 2160 grams in 10 minutes, typically at 190° C., 210° C., or 230° C. Unless otherwise indicated, melt flow rate is measured in accordance with ASTM Test Method D1238 with a Tinius Olsen Extrusion Plastometer.
The glass transition temperature (Tg) may be determined by dynamic mechanical analysis (DMA) in accordance with ASTM E1640-13. A Q800 instrument from TA Instruments may be used. The experimental runs may be executed in tension/tension geometry, in a temperature sweep mode in the range from −120° C. to 150° C. with a heating rate of 3° C./min. The strain amplitude frequency may be kept constant (2 Hz) during the test. Three (3) independent samples may be tested to get an average glass transition temperature, which is defined by the peak value of the tan δ curve, wherein tan δ is defined as the ratio of the loss modulus to the storage modulus (tan δ=E″/E′).
The melting temperature may be determined by differential scanning calorimetry (DSC). The weight fraction of crystalline content may be estimated from the DSC thermograms as follows:
where ΔH is the heat of fusion of crystals determined from DSC thermogram and ΔHo is the heat of fusion for the entirely alpha crystalline material (207 J/g) or beta crystalline material (168.5 J/g).
The differential scanning calorimeter, which may be outfitted with a liquid nitrogen cooling accessory and with a UNIVERSAL ANALYSIS 2000 (version 4.6.6) analysis software program, both of which are available from T.A. Instruments Inc. of New Castle, Del. To avoid directly handling the samples, tweezers or other tools may be used. The samples may be placed into an aluminum pan and weighed to an accuracy of 0.01 milligram on an analytical balance. A lid may be crimped over the material sample onto the pan. Typically, the resin pellets may be placed directly in the weighing pan.
The differential scanning calorimeter may be calibrated using an indium metal standard and a baseline correction may be performed, as described in the operating manual for the differential scanning calorimeter. A material sample may be placed into the test chamber of the differential scanning calorimeter for testing, and an empty pan may be used as a reference. All testing may be run with a 55-cubic centimeter per minute nitrogen (industrial grade) purge on the test chamber. For resin pellet samples, the heating and cooling program is a 2-cycle test that began with an equilibration of the chamber to −30° C., followed by a first heating period at a heating rate of 10° C. per minute to a temperature of 200° C., followed by equilibration of the sample at 200° C. for 3 minutes, followed by a first cooling period at a cooling rate of 10° C. per minute to a temperature of −30° C., followed by equilibration of the sample at −30° C. for 3 minutes, and then a second heating period at a heating rate of 10° C. per minute to a temperature of 200° C. For fiber samples two heating and cooling programs may be applied. First heating and cooling program may be a 2-cycle test that begins with an equilibration of the chamber at 0° C., followed by a heating period at a heating rate of 10° C. per minute to a temperature of 200° C., followed by equilibration of the sample at 200° C. for 3 minutes, followed by the first cooling period at a cooling rate of 10° C. per minute to a temperature of −50° C., followed by equilibration of the sample at −50° C. for 3 min, and then a second heating period at a heating rate of 10° C. per minute to a temperature of 200° C. All testing may be run with a 55-cubic centimeter per minute nitrogen (industrial grade) purge on the test chamber. A second heating and cooling program may be a 2-cycle test that begins with an equilibration of the chamber at 40° C., followed by a first heating period at a heating rate of 20° C. per minute to a temperature of 100° C., followed by a heating at 10° C. per minute to a temperature of 200° C., followed by equilibration of the sample at 200° C. for 3 minutes, followed by the first cooling period at a cooling rate of 20° C. per minute to a temperature of 40° C., followed by equilibration of the sample at 40° C. for 3 minutes, and then a second heating period following the same temperature profile as a first heating period.
The results are evaluated using the UNIVERSAL ANALYSIS 2000 analysis software program, which identified and quantified the endothermic and exothermic peaks during the first and second heating cycles, and the areas under the peaks on the DSC plots. The melting temperature is determined using an automatic inflection calculation for the endothermic melting peak occurring during the second heating period.
Tensile properties of the fibers may be determined using MTS 810 hydraulic tensile frame. For example, to evaluate fibers resistance to fail during “solid state” drawing they may be mounted into MTS 200N yarn grips at gauge length of 15 mm and drawn at 27° C. to 800% elongation at 1000, 2000, 3000, 4000 and 5000 mm/min rates. After drawing, percentage of failed fibers may be determined by dividing the number of failed fibers by total number of fibers mounted into yarn grip and multiplying the result by 100.
Modulus may be determined utilizing a MTS 810 hydraulic tensile frame to pull injection molded Type I dog bones as described in ASTM D638-10 (specimens pulled at a rate of 50 mm/min or 87.7%.min deformation). The tensile frame grips may be at a nominal gage length of 115 mm. Peak stress, break stress, elongation at break, and energy per volume at break may be determined using a MTS Synergie 200 tensile frame to pull injection molded Type V dog bones at described in ASTM D638-10 (specimens may be pulled at a rate of 8.4 mm/min or 87.7%/min deformation). The tensile frame grips may be at a nominal gage length of 25.4 mm. In each test, the specimens may be conditioned at 23° C.±2° C. and 50%±10% relative humidity for not less than 40 hours. Test conditions may be at 23° C.±2° C. and 50%±10% relative humidity. Five (5) specimens may be tested for each composition. A computer program (e.g., TestWorks 4) may be used to collect data during testing and to generate a stress versus strain curve from which the average modulus, peak stress, break stress, elongation at break, and energy per volume at break may be determined.
Films may be tested for tensile properties (peak stress, modulus, strain at break, and energy per volume at break) on a MTS Synergie 200 tensile frame. The test may be performed in accordance with ASTM D638-10 (at about 23° C.). Film samples may be cut into dog bone shapes with a center width of 3.0 mm before testing. The dog-bone film samples may be held in place using grips on the MTS Synergie 200 device with a gauge length of 18.0 mm. The film samples may be stretched at a crosshead speed of 5.0 in/min until breakage occurred. Five samples may be tested for each film in both the machine direction (MD) and the cross direction (CD). A computer program (e.g., TestWorks 4) may be used to collect data during testing and to generate a stress versus strain curve from which a number of properties may be determined, including modulus, peak stress, elongation, and energy to break.
Fiber tensile properties may be determined in accordance with ASTM 638-10 at 23° C. For instance, individual fiber specimens may initially be shortened (e.g., cut with scissors) to 38 millimeters in length, and placed separately on a black velvet cloth. 10 to 15 fiber specimens may be collected in this manner. The fiber specimens may then be mounted in a substantially straight condition on a rectangular paper frame having external dimension of 51 millimeters×51 millimeters and internal dimension of 25 millimeters×25 millimeters. The ends of each fiber specimen may be operatively attached to the frame by carefully securing the fiber ends to the sides of the frame with adhesive tape. Each fiber specimen may be measured for its external, relatively shorter, cross-fiber dimension employing a conventional laboratory microscope, which may be properly calibrated and set at 40× magnification. This cross-fiber dimension may be recorded as the diameter of the individual fiber specimen. The frame helps to mount the ends of the sample fiber specimens in the upper and lower grips of a constant rate of extension type tensile tester in a manner that avoids excessive damage to the fiber specimens.
A constant rate of extension type of tensile tester and an appropriate load cell may be employed for the testing. The load cell may be chosen (e.g., 10N) so that the test value falls within 10-90% of the full scale load. The tensile tester (i.e., MTS SYNERGY 200) and load cell may be obtained from MTS Systems Corporation of Eden Prairie, Mich. The fiber specimens in the frame assembly may then be mounted between the grips of the tensile tester such that the ends of the fibers may be operatively held by the grips of the tensile tester. Then, the sides of the paper frame that extend parallel to the fiber length may be cut or otherwise separated so that the tensile tester applies the test force only to the fibers. The fibers may be subjected to a pull test at a pull rate and grip speed of 12 inches per minute. The resulting data may be analyzed using a TESTWORKS 4 software program from the MTS Corporation with the following test settings:
The tenacity values may be expressed in terms of gram-force per denier. Peak elongation (% strain at break) and peak stress may also be measured.
The peak load of a web may be determined using a 2″×6″ strip cut along the length (MD) and width direction (CD). The test may be performed in a universal tensile tester equipped with two 1″×3″rubber coated grips. The gauge length may be 76±1 mm (3±0.04″).
To determine density and percent void volume, the width (Wi) and thickness (Ti) of the specimen may be initially measured prior to drawing. The length (Li) before drawing may also be determined by measuring the distance between two markings on a surface of the specimen. Thereafter, the specimen may be drawn to initiate pore formation. The width (Wf), thickness (Tf), and length (Lf) of the specimen may then be measured to the nearest 0.01 mm utilizing Digimatic Caliper (Mitutoyo Corporation). The volume (Vi) before drawing may be calculated by Wi×Ti×Li=Vi. The volume (Vf) after drawing may also be calculated by Wf×Tf×Lf=Vf. The density (Pf) may be calculated by Pf=Pi/φ, where Pi is density of precursor material and the percent void volume (% Vv) was calculated by: % Vv=(1−1/φ)×100.
The hydrostatic pressure test is a measure of the resistance of a material to penetration by liquid water under a static pressure and is performed in accordance with AATCC Test Method 127-2008. The results for each specimen may be averaged and recorded in centimeters (cm). A higher value indicates greater resistance to water penetration.
The test used to determine the WVTR of a material may vary based on the nature of the material. One technique for measuring the WVTR value is ASTM E96/96M-12, Procedure B. Another method involves the use of INDA Test Procedure IST-70.4 (01). The INDA test procedure is summarized as follows. A dry chamber is separated from a wet chamber of known temperature and humidity by a permanent guard film and the sample material to be tested. The purpose of the guard film is to define a definite air gap and to quiet or still the air in the air gap while the air gap is characterized. The dry chamber, guard film, and the wet chamber make up a diffusion cell in which the test film is sealed. The sample holder is known as the Permatran-W Model 100K manufactured by Mocon/Modem Controls, Inc., Minneapolis, Minn. A first test is made of the WVTR of the guard film and the air gap between an evaporator assembly that generates 100% relative humidity. Water vapor diffuses through the air gap and the guard film and then mixes with a dry gas flow that is proportional to water vapor concentration. The electrical signal is routed to a computer for processing. The computer calculates the transmission rate of the air gap and the guard film and stores the value for further use.
The transmission rate of the guard film and air gap is stored in the computer as CalC. The sample material is then sealed in the test cell. Again, water vapor diffuses through the air gap to the guard film and the test material and then mixes with a dry gas flow that sweeps the test material. Also, again, this mixture is carried to the vapor sensor. The computer then calculates the transmission rate of the combination of the air gap, the guard film, and the test material. This information is then used to calculate the transmission rate at which moisture is transmitted through the test material according to the equation:
TR−1testmaterial=TR−1test material,guardfilm,airgap−TR−1guardfilm, airgap
The water vapor transmission rate (“WVTR”) is then calculated as follows:
wherein,
A precursor blend was formed from 93 wt. % of isotactic propylene homopolymer (M3661, melt flow rate of 14 g/10 at 210° C. and melting temperature of 150° C., Total Petrochemicals) and 7 wt. % of poly(ethylene-co-methyl acrylate-co-glycidyl methacrylate) (LOTADER® AX8900, Arkema) having a melt flow rate of 6 g/10 min (190° C./2160 g), a glycidyl methacrylate content of 8 wt. %, methyl acrylate content of 24 wt. %, and ethylene content of 68 wt. %. The components were compounded in a co-rotating twin-screw extruder (ZSK-26 with 26 mm screw diameter and an L/D=48). The extruder had thirteen heating zones. The temperature in the extruder ranged from 180° C. to 220° C. The polymer was fed gravimetrically to the extruder at the hoper at 15 pounds per hour. The extruder was operated at 200 revolutions per minute (RPM). The die used to extrude the resin had 4 die openings (6 mm in diameter) that were separated by 4 mm. Upon extrusion, the extrudate was air-cooled on a fan-cooled conveyor belt and pelletized using a Conair Pelletizer. The pellets were then flood fed in a 20 mm single screw extruder, melted and passed through a melt pump at a rate of 0.4 grams per hole per minute and through 0.6 mm diameter 16-hole spinneret. The temperature of the extruder ranged from 175° C. to 220° C. The fibers were quenched at 27° C. and collected in free fall (gravity only as draw force).
Fibers were made as described at Example 1, except that they were collected at take up speed of 100 m/min.
Fibers were made as described in Example 1, except that they were quenched at 95° C. Fibers were collected in free fall (gravity only as draw force).
Fibers were made as described at Example 3, except that they were collected at take up speed of 100 m/min.
Fibers were made as described in Example 1, except that the blend was composed of 91 wt. % of isotactic propylene homopolymer (M3661), 7 wt. % of LOTADER® AX8900, and 2 wt. % of a beta-nucleating masterbatch (MPM-2000, Mayzo, Inc.) having a melt flow rate of 12 g/10 min and melting temperature of 148-155° C. for the beta-crystal phase and 162-167° C. for the alpha-crystal phase. The fibers were quenched at 27° C. and collected in free fall (gravity only as draw force).
Fibers were made as described at Example 5, except that they were collected at take up speed of 100 m/min.
Fibers were made as described in Example 3, except that the blend was composed of 91 wt. % of isotactic propylene homopolymer (M3661), 7 wt. % of LOTADER® AX8900, and 2 wt. % of a beta-nucleating masterbatch (MPM-2000, Mayzo, Inc.) having a melt flow rate of 12 g/10 min and melting temperature of 148-155° C. for the beta-crystal phase and 162-167° C. for the alpha-crystal phase. The fibers were quenched at 95° C. and collected in free fall (gravity only as draw force).
Fibers were made as described at Example 7, except that they were collected at take up speed of 100 m/min.
The melting temperature (Tm), crystallinity content, and crystalline structure of the fibers of Examples 2, 4, 6, and 8 were determined by DSC. The results are shown at Table 1.
A precursor blend was formed from 93 wt. % of isotactic propylene homopolymer (M3661) and 7 wt. % of LOTADER® AX8900, Arkema. The components were compounded in a co-rotating twin-screw extruder (ZSK-26 with 26 mm screw diameter and an L/D=48). The extruder had thirteen heating zones. The temperature in the extruder ranged from 180° C. to 220° C. The polymer was fed gravimetrically to the extruder at the hoper at 15 pounds per hour. The extruder was operated at 200 revolutions per minute (RPM). The die used to extrude the resin had 4 die openings (6 mm in diameter) that were separated by 4 mm. Upon extrusion, the extrudate was air-cooled on a fan-cooled conveyor belt and pelletized using a Conair Pelletizer.
Pellets of the precursor blend and linear low density polyethylene (ASPUN™ 6835A, melt flow rate 17 g/10 min at 190° C./2160 g, melting temperature 129° C.) were separately fed into 2, 32 mm single screw extruders (pellets of precursor blend were fed into the extruder A and pellets of polyethylene were fed into the extruder B), melted and passed through separate melt pumps at rates of 0.34 and 0.14 grams per hole per minute respectively through 0.5 mm 288 hole spinneret. The temperature of the extruder A ranged from 200° C. to 220° C. The temperature of the extruder B ranged from 180° C. to 220° C. The core/sheath (70% precursor blend core and 30% polyethylene sheath) bicomponent fibers were quenched at 10° C. and collected at 100 m/min take up speed.
Fibers were made as described in Example 9, except that the blend was composed of 91 wt. % of isotactic propylene homopolymer (M3661), 7 wt. % of LOTADER® AX8900, and 2 wt. % of beta-nucleating masterbatch (MPM-2000, Mayzo, Inc.) having a melt flow rate of 12 g/10 min and melting temperature of 148-155 ° C. for the beta-crystal phase and 162-167 ° C. for the alpha-crystal phase. The core/sheath bicomponent fibers were quenched at 10° C. and collected at 100 m/min take up speed. The melting temperature (Tm), crystallinity content, and crystalline structure of the fibers of Examples 2, 4, 6, and 8 were determined by DSC. The results are shown in Table 2.
The fibers of Examples 9 and 10 were also cold drawn at 23° C. in a tensile tester machine to evaluate breakability. The results are shown at Tables 2-3.
Isotactic propylene homopolymer (M3661) pellets were flood fed in a 20 mm single screw extruder, melted and passed through a melt pump at a rate of 0.4 grams per hole per minute and through 0.6 mm diameter 16-hole spinneret. The temperature of the extruder ranged from 175° C. to 220° C. The fibers were quenched at 27° C. and collected in free fall (gravity only as draw force).
Fibers were made as described in Example 11, except that they were collected at take up speed of 100 m/min.
Fibers were made as described in Example 11, except that they were collected at take up speed of 500 m/min.
Fibers were made as described in Example 11, except they were quenched at 95° C. Fibers were collected in free fall (gravity only as draw force).
Fibers were made as described in Example 14, except that they were collected at take up speed of 500 m/min.
A beta-nucleator masterbatch was formed from 99 wt. % of isotactic propylene homopolymer powder (M3661) and 1 wt. % of quinacridonequinone (Sigma Aldrich). The mixture was compounded in a co-rotating Prizm twin-screw extruder with a 16 mm diameter screw and a L/D=40. The extruder had ten heating zones. The temperature in the extruder ranged from 170° C. to 190° C. The mixture was fed gravimetrically to the extruder at the hoper at 4 pounds per hour. The extruder was operated at 200 revolutions per minute (RPM). The die used to extrude the resin had 1 opening (4 mm in diameter). Upon extrusion, the extrudate was air-cooled on a fan-cooled conveyor belt and pelletized using a Conair Pelletizer.
The pellets of the beta-nucleator masterbatch (10 wt. %) were blended with isotactic propylene homopolymer (M3661, 90 wt. %) in a co-rotating twin-screw extruder (ZSK-26 with a screw diameter of 26 mm and a L/D=48). The extruder had thirteen heating zones. The temperature in the extruder ranged from 180° C. to 220° C. The polymer was fed gravimetrically to the extruder at the hoper at 15 pounds per hour. The extruder was operated at 200 revolutions per minute (RPM). The die used to extrude the resin had 3 die openings (6 mm in diameter) that were separated by 4 mm. Upon extrusion, the extrudate was air-cooled on a fan-cooled conveyor belt and pelletized using a Conair Pelletizer. The pellets were then flood fed in a 20 mm single screw extruder, melted and passed through a melt pump at a rate of 0.4 grams per hole per minute and through 0.6 mm diameter 16-hole spinneret. The temperature of the extruder ranged from 175° C. to 220° C. The fibers were quenched at 27° C. and collected in free fall (gravity only as draw force).
Fibers were made as described in Example 17, except that they were collected at take up speed of 100 m/min.
Fibers were made as described in Example 17, except that they were collected at take up speed of 500 m/min.
Fibers were made as described in Example 17, except they were quenched at 95° C. Fibers were collected in free fall (gravity only as draw force).
Fibers were made as described in Example 20, except that they were collected at take up speed of 100 m/min.
Fibers were made as described in Example 20, except that they were collected at take up speed of 500 m/min.
The melting temperature (Tm), crystallinity content, and crystalline structure of the fibers of Examples 12, 13, 15, 16, 18, 19, 21, and 22 were determined by DSC. The results are shown at Table 4.
While the invention has been described in detail with respect to the specific embodiments thereof, it will be appreciated that those skilled in the art, upon attaining an understanding of the foregoing, may readily conceive of alterations to, variations of, and equivalents to these embodiments. Accordingly, the scope of the present invention should be assessed as that of the appended claims and any equivalents thereto.
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/US2015/061086 | 11/17/2015 | WO | 00 |
| Number | Date | Country | |
|---|---|---|---|
| 62084721 | Nov 2014 | US |
