POLY(LACTIC ACID) FIBER, NON-WOVEN WEFT, ABSORBENT ARTICLE, AND METHODS FOR THE FORMATION OF A POLY(

专利摘要:
poly(lactic acid) fiber and method of forming the same The present invention provides poly(lactic acid) fibers formed from a thermoplastic composition, which contains poly(lactic acid) and a polymeric stiffening additive. the present inventors have found that the specific nature of the components and the process by which they are combined can be carefully controlled to achieve a composition having desirable morphological characteristics. more particularly, the stiffening additive can be dispersed as discrete physical domains within a continuous phase of the poly(lactic acid). these domains have a particular size, shape and distribution, such that, when the fibers are drawn, they absorb energy and become elongated. this allows the resulting composition to exhibit more malleable and softer behavior than otherwise rigid poly(lactic acid). through selective control over the components and method employed, the present inventors have found that the resulting fibers can thus exhibit good mechanical properties both during and after melt spinning.
公开号:BR112013003178B1
申请号:R112013003178-6
申请日:2011-07-06
公开日:2021-08-03
发明作者:Vasily A. Topolkaraev；Peiguang Zhou；Gregory J. Wideman；Tom Eby；Ryan J. Mceneany
申请人:Kimberly-Clark Worldwide, Inc；
IPC主号:

专利说明:

HISTORY OF THE INVENTION
[001] Several attempts have been made to form nonwoven webs from biodegradable polymers. Although fibers prepared from biodegradable polymers are known, problems with their use have been encountered. For example, poly(lactic acid) ("PLA") is one of the most common biodegradable and sustainable (renewable) polymers used to form nonwoven webs. Unfortunately, PLA nonwoven webs, in general, have low bonding flexibility and high roughness due to the high glass transition temperature and low crystallization rate of poly(lactic acid). In turn, thermally bonded PLA nonwoven webs often exhibit small elongations, which are not acceptable in certain applications, such as in an absorbent article. Also, although poly(lactic acid) can withstand high draw ratios, it requires high levels of draw energy to achieve the crystallization needed to overcome thermal shrinkage. In response to these difficulties, plasticizers have been employed in an attempt to reduce the glass transition temperature and to improve bonding and softness. A common plasticizer is poly(ethylene glycol). Unfortunately, poly(ethylene glycol) tends to phase separation from poly(lactic acid) during aging, especially in a high humidity and high temperature environment, which deteriorates the mechanical properties of the resulting fibers over time. The addition of plasticizers also causes other problems, such as degradation in melt spinning and a reduction in melt strength and drawability.
[002] As such, there is currently a demand for poly(lactic acid) fibers that exhibit good elongation properties while remaining strong. SUMMARY OF THE INVENTION
[003] According to an embodiment of the present invention, a poly(lactic acid) fiber that extends in a longitudinal direction and has an average diameter of about 2 to about 25 micrometers is described. The fiber comprises a thermoplastic composition, which contains a plurality of discrete domains dispersed within a continuous phase, the discrete domains containing a polymeric stiffening additive, and the continuous phase containing poly(lactic acid). At least one of the discrete domains is elongated in the longitudinal direction of the fiber and has a length of about 5 to about 400 micrometers. The fiber exhibits a peak elongation of about 25% or more and a tenacity of about 7.35 to about 58.84 mN (about 0.75 to about 6 grams-force) per denier.
[004] According to another embodiment of the present invention, a method for forming a poly(lactic acid) fiber is described. The method comprises combining a poly(lactic acid) with a polymeric stiffening additive to form a thermoplastic composition, the composition comprising a plurality of discrete domains dispersed within a continuous phase. Discrete domains contain the polymeric stiffening additive and the continuous phase contains the poly(lactic acid). The thermoplastic composition is extruded through a mold and drawn to form a fiber. The drawn fiber domains are elongated in a longitudinal direction of the fiber so that the length of the elongated domains is greater than the length of the domains before drawing.
[005] Other features and aspects of the present invention are discussed in greater detail below. BRIEF DESCRIPTION OF THE DRAWINGS
[006] A complete and enabling description of the present invention, including its best mode, addressed to a person skilled in the art, is shown more particularly in the remainder of the descriptive report, which makes reference to the attached figures, in which: Figure 1 is is a schematic illustration of a process that can be used in an embodiment of the present invention to form fibers; Figure 2 is a schematic illustration of the formation of discrete domains of the stiffening additive when drawing the fibers, wherein Figure 2A shows the domains before drawing the fibers and Figure 2B shows the domains after drawing the fibers; Figure 3 is an SEM photograph (7KV, 3000X) of a cross section of a polymer blend (Sample 2) from Example 1; Figure 4 is an SEM photograph (7 KV, 10,000X) of a cross section of a polymer blend (Sample 2) from Example 1; Figure 5 is an SEM photograph (7 KV, 9,000X) of a section cross-section of a fiber (Sample 2 ) from Example 2; Figure 6 is an SEM photograph (7 KV, 10,000X) of a cross section of a fiber (Sample 2) from Example 2; Figure 7 is an SEM photograph (7 KV, 7,500X) the axial dimension of a fiber (Sample 2) from Example 2; e Figure 8 is an SEM photograph (7 KV, 5,000X) of the axial dimension of a fiber (Sample 2) from Example 2.
[007] The repeated use of reference characters in this descriptive report and in the drawings is intended to represent the same or analogous features or elements of the invention. DETAILED DESCRIPTION OF REPRESENTATIVE MODALITIES
[008] Reference will now be made in detail to various embodiments of the invention, one or more examples of which are shown below. Each example is provided by way of explaining the invention, not limiting the invention. Indeed, it will be evident to those skilled in the art that various modifications and variations can be made to the present invention without departing from the scope or spirit of the invention. For example, features illustrated or described as part of one modality can be used in another modality to obtain yet another modality. Therefore, it is intended that the present invention cover such modifications and variations as they fall within the scope of the appended claims and their equivalents. Definitions
[009] As used herein, the terms "biodegradable" or "biodegradable polymer" in general refer to a material that degrades from the action of naturally occurring microorganisms, such as bacteria, fungi and algae; of ambient heat; moisture or other environmental factors. The biodegradability of a material can be determined using ASTM Test Method 5338.92.
[0010] As used herein, the term "fibers" refers to elongated extrudates formed by passing a polymer through a forming hole, such as a mold. Unless otherwise noted, the term "fibers" includes both staple fibers having a defined length and substantially continuous filaments. Substantially continuous filaments can, for example, 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.
[0011] As used herein, the term "monocomponent" refers to fibers formed from a polymer. Obviously, this does not exclude fibers to which additives have been added for color, antistatic properties, lubricity, hydrophilicity, liquid repellency, etc.
[0012] As used herein, the term "multicomponent" refers to fibers formed from at least two polymers (eg bicomponent fibers) that are extruded from separate extruders. The polymers are disposed in distinct zones positioned substantially constant along the cross section of the fibers. The components can be arranged in any desired configuration, such as wrap-core, side-by-side, segmented pie, island in the sea, and so on. Various methods for forming multicomponent fibers are described in U.S. Patent Nos. 4,789,592 to Taniguchi, et al. and 5,336,552 from Strack, et al., 5,108,820 from Kaneko, et al., 4,795,668 from Kruege, et al., 5,382,400 from Pike, et al., 5,336,552 from Strack, et al. , and 6,200,669 to Marmon, et al., which are incorporated herein in their entirety by reference thereto for all purposes. Multi-component fibers having various irregular shapes can also be formed, as described in U.S. Patent Nos. 5,277,976 to Hogle, et al., 5,162,074 to Hills, 5,466,410 to Hills, 5,069,970 to Largman, et al., and 5,057,368 to Largman, et al., which are incorporated herein into their wholes, by reference to them, for all purposes.
[0013] As used herein, the term "non-woven weft" refers to a weft having a structure of individual fibers that are interwoven randomly, not in an identifiable manner, as in a knitted fabric. Non-woven wefts include, for example, meltblown wefts, spunbond wefts, carded wefts, wet dispersed wefts, air dispersed wefts, coform wefts, hydraulically entangled wefts, etc. The grammage of the non-woven fabric, in general, can vary, but typically it is from about 5 grams per square meter (g/m2) to 200 g/m2, in some embodiments, from about 10 g/m2 to about 150 g/m2 and, in some embodiments, from about 15 g/m2 to about 100 g/m2.
[0014] As used herein, the term "meltblown" web or layer generally refers to a non-woven web that is formed by a process in which a molten thermoplastic material is extruded through a plurality of capillaries of fine molds, usually circular, as fused fibers into converging, high velocity gas (e.g. air) streams which attenuate the fused thermoplastic material fibers to reduce their diameter, which may be up to the microfiber diameter . Thereafter, the meltblown fibers are carried by the high velocity gas stream and are deposited onto a collecting surface to form a web of randomly arranged meltblown fibers. Such a process is described, for example, in U.S. Patent Nos. 3,849,241, by Butin et, al.; 4,307,143, by Meitner, et al.; and 4,707,398, by Wisneski, et al.; which are incorporated herein, in their entirety, by reference thereto, for all purposes. Meltblown fibers can be substantially continuous or discontinuous, and are generally tacky when deposited onto a collecting surface.
[0015] As used herein, the term "spunbond" web or layer generally refers to a non-woven web containing substantially continuous filaments of small diameter. The filaments are formed by extrusion of a molten thermoplastic material, from a plurality of thin, usually circular, capillaries of a spinner with the diameter of the extruded filaments, then being rapidly reduced as, for example, by extractive drawing and/or other well-known spunbonding mechanisms. The production of spunbond webs is described and illustrated, for example, in U.S. Patents Nos. 4,340,563 to Appel, et al.; 3,692,618 by Dorschner, et al.; 3,802,817 to Matsuki, et al.; 3,338,992 to Kinney; 3,341,394 to Kinney; 3,502,763 to Hartman; 3,502,538 from Levy; 3,542,615 by Dobo, et al. and 5,382,400 to Pike, et al., which are incorporated herein in their entirety by reference thereto for all purposes. Spunbond filaments are generally non-sticky when they are deposited onto a collecting surface. Spunbond filaments can sometimes be smaller than about 40 micrometers in diameter, and are often between about 5 and about 20 micrometers. Test Methods Melting Mass Flow Rate:
[0016] The melt flow rate ("MFR") is the weight of a polymer (in grams) forced through an extrusion rheometer hole (0.0825 inches in diameter or 0.2096 cm), when subjected to a load of 2,160 grams in 10 minutes, typically at 190°C or 230°C. Unless otherwise noted, the melt flow rate is measured in accordance with ASTM Test Method D1239 with a Tinius Olsen Extrusion Plastometer. Thermal Properties:
[0017] The melting temperature and the glass transition temperature can be determined by differential scanning calorimetry (DSC). The differential scanning calorimeter could be a DSC Q100 Differential Scanning Calorimeter, which was equipped with a liquid nitrogen cooling accessory and a UNIVERSAL ANALYSIS 2000 analysis computer program (version 4.6.6), both of which are available from TA Instruments Inc., of New Castle, Delaware, USA. To avoid direct handling of the samples, special tweezers or other tools were used. The samples are placed in an aluminum pan and weighed to an accuracy of 0.01 milligram on an analytical balance. A lid is folded over the material sample over the pan. Typically, resin pellets are placed directly into the weigh pan, and the fibers are cut to accommodate placement over the weigh pan and cover by the lid.
[0018] The differential scanning calorimeter is calibrated using an indium metal standard and a baseline correction is performed as described in the operating manual for the differential scanning calorimeter. A sample of material is placed in the test chamber of the differential scanning calorimeter for testing, and an empty pan is used as a reference. All testing takes place with a nitrogen purge (industrial grade) of 55 cubic centimeters per minute over the test chamber. For resin pellet samples, the heating and cooling program is a 2-cycle test, which started with a chamber equilibration to -30°C, followed by a first heating period at a 10° heating rate 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, the heating and cooling program is a 1-cycle test, which started with a chamber equilibration to -25°C, followed by a warm-up 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, and then a cool-down period at a cooling rate of 10°C per minute to a temperature of -30°C. All testing takes place with a nitrogen purge (industrial grade) of 55 cubic centimeters per minute over the test chamber.
[0019] The results are evaluated using the UNIVERSAL ANALYSIS 2000 analysis computer program, which identified and quantified the glass transition temperature (Tg) of inflection, the endothermic and exothermic peaks and the areas over the peaks on the DSC plots. The glass transition temperature is identified as the region on the graph line where a distinct change in slope has occurred, and the melting temperature is determined using an automatic inflection calculation. Traction Properties:
[0020] Individual fiber specimens are shortened (eg cut with scissors) to 38mm in length, and placed separately on a black velvet cloth. 10 to 15 fiber specimens are collected in this way. The fiber specimens are then mounted in a substantially straight condition in a rectangular paper frame having an outer dimension of 51mm x 51mm and an inner dimension of 25mm x 25mm. The ends of each fiber specimen are operatively secured to the frame by carefully securing the fiber ends to the sides of the frame with adhesive tape. Each fiber specimen is then measured for its relatively shorter outer fiber cross-sectional dimension using a conventional laboratory microscope, which has been properly calibrated and adjusted to 40X magnification. This fiber cross-sectional dimension is recorded as the diameter of the individual fiber specimen. The frame helps mount the ends of the sample fiber specimens to the upper and lower grips of a constant-extension-rate-type pull tester in a way that prevents excessive damage to the fiber specimens.
[0021] A constant extension rate type pull tester and an appropriate load cell are employed for testing. The load cell is chosen (eg 10N) so that the test value falls within 10-90% of the full scale load. The tensile tester (ie, MTS SYNERGY 200) and load cell are obtained from MTS Systems Corporation, of Eden Prairie, Michigan, USA. The fiber specimens in the frame assembly are then mounted between the grips of the tensile tester such that the ends of the fibers are operatively held by the grips of the tensile tester. Then, the sides of the paper frame, which extend parallel to the length of the fibers, are cut or otherwise separated so that the tensile tester applies the testing force to the fibers only. The fibers are then subjected to a tensile test at a pull rate and a grip speed of 30.48 cm (12 inches per minute). The resulting data is analyzed using a MTS Corporation TESTWORKS 4 computer program with the following test settings:

[0022] Toughness values are expressed in terms of gram-force per denier. Peak elongation (% tensile at break) is also measured. Moisture Content:
[0023] Moisture content may be determined using an Arizona Instruments Computrac Vapor Pro Moisture Analyzer (Model No. 3100), in substantial accordance with ASTM D7191-05, which is incorporated herein in its entirety by reference to he, for all purposes. The test temperature (§X2.1.2) can be 130°C, the sample size (§X2.1.1) can be 2 to 4 grams, and the vial purge time (§X2.1.4) can be 30 seconds. In addition, the termination criteria (§X2.1.3) can be defined as a “prediction” mode, which means that the test is terminated when the built-in programmed criteria (which mathematically calculate the endpoint moisture content) are satisfied. Detailed Description
Generally speaking, the present invention is directed to poly(lactic acid) fibers formed from a thermoplastic composition, which contains poly(lactic acid) and a polymeric stiffening additive. The present inventors have found that the specific nature of the components and the process by which they are combined can be carefully controlled to achieve a composition having desirable morphological characteristics. More particularly, the stiffening additive can be dispersed as physical domains dispersed within a continuous phase of the poly(lactic acid). These domains have a particular particle size, shape and distribution, such that, when the fibers are drawn, they absorb energy and become elongated. This allows the resulting composition to exhibit a more malleable and softer behavior than the otherwise rigid poly(lactic acid). Through selective control over the components and method employed, the present inventors have found that the resulting fibers can thus exhibit good mechanical properties both during and after melt spinning.
[0025] Various embodiments of the present invention will now be described in greater detail. I. Thermoplastic Composition A. Poly(lactic acid)
[0026] In general, poly(lactic acid) can be obtained from monomer units of any lactic acid isomer, such as levorotatory lactic acid ("L-lactic acid"), dextorrotatory lactic acid ("D-acid" lactic"), meso-lactic acid or mixtures thereof. Monomer units can also be formed from anhydrides of any lactic acid isomer, 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 process, such as polycondensation or ring-opening polymerization, can be used to polymerize lactic acid. A small amount of a chain extending agent (eg, a diisocyanate compound, an epoxide compound, or an acid anhydride) may also be employed. The poly(lactic acid) can be a homopolymer or a copolymer, such as one containing monomer units obtained from L-lactic acid and monomer units obtained from D-lactic acid. Although not necessary, the content ratio in one of the monomer unit obtained from L-lactic acid and the monomer unit obtained from D-lactic acid is preferably about 85% by mol or more. in some embodiments, about 90% mole or more, and, in some embodiments, about 95% mole or more. Multiple poly(lactic acids), each having a different ratio between the monomer unit obtained from L-lactic acid and the monomer unit obtained from D-lactic acid, can be combined at an arbitrary percentage. Obviously, poly(lactic acid) can also be combined with other types of polymers (eg polyolefins, polyesters, etc.) to provide a variety of different benefits such as processing, fiber formation, etc.
[0027] In a particular modality, poly(lactic acid) has the following general structure:

A specific example of a suitable poly(lactic acid) polymer, which can be used in the present invention, is commercially available from Biomer, Inc., of Krailling, Germany) under the name BIOMER™ L9000. Other suitable poly(lactic acid) polymers are commercially available from Natureworks LLC, of Minnetonka, Minnesota (NATUREWORKS®) or from Mitsui Chemical (LACEATM). Still other suitable poly(lactic acids) can be described in U.S. Patent 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.
[0029] Poly(lactic acid) typically has a melting point of from about 140°C to about 260°C, in some embodiments from about 150°C to about 250°C, and in some in some embodiments, from about 160°C to about 220°C. Such poly(lactic acids) are useful in that they biodegrade at a rapid rate. The glass transition temperature ("Tg") of poly(lactic acid) can be relatively high, such as from about 40°C to about 80°C, in some embodiments, from about 50°C to about 80 °C, and, in some embodiments, from about 55°C to about 65°C. As discussed in greater detail above, the melting temperature and the glass transition temperature can all be determined using differential scanning calorimetry (“DSC”) in accordance with ASTM D-3417.
[0030] Poly(lactic acid) typically has a number average molecular weight ("Mn") ranging from about 40,000 to about 160,000 grams per mole, in some embodiments, from about 50,000 to about 140,000 grams per mol, and, in some embodiments, from about 80,000 to about 120,000 grams per mol. Likewise, the polymer typically also has a weight average molecular weight ("Mw") ranging from about 80,000 to about 200,000 grams per mole, in some embodiments, from about 100,000 to about 180,000 grams per mole, and, in some embodiments, from about 110,000 to about 160,000 grams per mol. 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. Weight and number average molecular weights can be determined by methods known to those skilled in the art.
Poly(lactic acid) can also have an apparent viscosity of from about 50 to about 600 Pascal.seconds (Pa.s), in some embodiments, from about 100 to about 500 Pa.s, and in some embodiments some modalities, from about 200 to about 400 Pa.s, as determined at a temperature of 190°C and a shear stress of 1000 s-1. The melt flow rate of poly(lactic acid) (on a dry basis) can also range from about 0.1 to about 40 grams per 10 minutes, in some embodiments from about 0.5 to about 20 grams per 10 minutes, and in some modes from about 5 to about 15 grams per 10 minutes, determined at a load of 2,160 grams and at 190°C. B. Polymeric Hardening Additive
[0032] The thermoplastic composition of the present invention also contains a polymeric stiffening additive. Due to its polymeric nature, the stiffening additive has a relatively high molecular weight, which can help to improve the melt strength and stability of the thermoplastic composition. It is typically desired that the polymeric stiffening additive be generally immiscible with poly(lactic acid). In this way, the stiffening additive can become dispersed as discrete phase domains within a continuous poly(lactic acid) phase. Discrete domains are capable of absorbing energy, which arises from the tension imparted during the stretching of the composition during the drawing of the fibers, which increases the overall stiffness and strength of the resulting fibers. Although polymers are generally immiscible, the stiffening additive can nevertheless be selected to have a solubility parameter that is relatively similar to that of poly(lactic acid). This generally improves interfacial adhesion and physical interaction of discrete and continuous phase boundaries, and thus reduces the likelihood that the composition will fracture on stretch. In that regard, the ratio of the solubility parameter for the poly(lactic acid) to that of the stiffening additive is typically from about 0.5 to about 1.5, and, in some embodiments, from about 0. 8 to about 1.2. For example, the polymeric stiffening additive can have a solubility parameter from about 15 to about 30 MJoules1/2/m3/2, and, in some embodiments, from about 18 to about 22 MJoules1/2/m3/ 2, while poly(lactic acid) can have a solubility parameter of about 20.5 MJoules1/2/m3/2. The term “solubility parameter”, as used here, refers to the “Hildebrand Solubility Parameter”, which is the square root of the cohesive energy density and is calculated according to the following equation:
in which:ΔHv = heat of vaporizationR = Constant of Ideal GasesT = TemperatureVm = Molecular Volume
[0033] Hildebrand solubility parameters for many polymers are also available from Wyeych's Solubility Handbook of Plastics (2004), which is incorporated herein by reference.
[0034] The polymeric hardening additive is also selected to exhibit a certain melt flow rate (or viscosity), to ensure that the discrete domains can be properly maintained. For example, if the melt flow rate of the hardening additive is too high, it tends to flow and disperse uncontrollably through the continuous phase. This results in lamellar or plate-like domains, which are difficult to maintain and also likely to fracture prematurely during fiber drawing. Conversely, if the melt flow rate of the hardening additive is too low, it tends to clump together and form very large elliptical domains, which are difficult to disperse during blending. This can cause uneven distribution of the stiffening additive over the entire continuous phase. In this regard, the present inventors have found that the ratio of the melt mass flow rate of the stiffening additive to the melt mass flow rate of the poly(lactic acid) is typically 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 polymeric stiffening additive may, for example, have a flow rate of melt 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 for 10 minutes, determined at a load of 2,160 grams and at 190°C.
[0035] In addition to the properties noted above, the mechanical characteristics of the polymeric stiffening additive are also, in general, selected to achieve the desired increase in fiber stiffness. For example, when a combination of the poly(lactic acid) and the stiffening additive is stretched during drawing the fibers, shear and/or plastic yield zones can be initiated in and around the discrete phase domains, as a result stress concentrations that originate from a difference in the elastic modulus of the stiffening additive and the poly(lactic acid). Higher stress concentrations promote more intensive localized plastic flow in the domains, which allows them to become significantly elongated during fiber drawing. These elongated domains allow the composition to exhibit more pliable and softer behavior than otherwise rigid poly(lactic acid) resin. To enhance stress concentrations, the stiffening additive is selected to have a relatively low Young's modulus of elasticity compared to poly(lactic acid). For example, the ratio of the modulus of elasticity of poly(lactic acid) to that of the stiffening additive is typically from about 1 to 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 stiffening additive can, for example, range from about 2 to about 500 MegaPascal (MPa), in some embodiments, from about 5 to about 300 MPa, and, in some embodiments, from about 10 to about 200 MPa. In contrast, the modulus of elasticity of poly(lactic acid) is typically from about 800 MPa to about 2000 MPa.
[0036] To provide the desired increase in stiffness, the polymeric stiffening additive may also exhibit a peak elongation (i.e., the percent elongation of the polymer at its peak load) greater than that of poly(lactic acid). For example, the polymeric stiffening additive of the present invention can exhibit a peak elongation of about 50% or more, in some embodiments, from about 100% or more, in some embodiments, from about 100% to about 2,000 %, and, in some modalities, from around 250% to around 1,500%.
[0037] While a variety of polymeric additives may be employed that exhibit the properties identified above, particularly suitable examples of such polymers may include, for example, polyolefins (eg, polyethylene, polypropylene, polybutylene, etc.); polytetrafluoroethylenes; polyesters (eg recycled polyester, poly(ethylene terephthalate), etc.); poly(vinyl acetates) (for example, poly(ethylene-vinyl acetate), poly(vinyl acetate chloride), etc.); poly(vinyl alcohols) (e.g. poly(vinyl alcohol), poly(ethylene-vinyl alcohol), etc.); poly(vinyl butyrals); acrylic resins (for example, polyacrylate, poly(methyl acrylate), poly(methyl methacrylate), etc.); polyamides (for example nylon); poly(vinyl chlorides); poly(vinylidene chlorides); polystyrenes, polyurethanes; etc. Suitable polyolefins may, for example, include ethylene polymers (eg, low density polyethylene ("LDPE"), high density polyethylene ("HDPE"), linear low density polyethylene ("LLDPE"), etc.), propylene homopolymers (eg syndiotactic, atactic, isotactic, etc.), propylene copolymer, and so on.
[0038] In a particular embodiment, the polymer is a propylene polymer, such as homopolypropylene or a copolymer of propylene. The propylene polymer can, for example, be formed of a substantially isotactic polypropylene homopolymer or a copolymer containing equal to or less than about 10% by weight of another monomer, i.e. at least 90% by weight by weight of propylene. Such homopolymers can have a melting point of about 160°C to about 170°C.
[0039] In yet another embodiment, 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; 1-decene substituted with ethyl, methyl or dimethyl; 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 can be from about 60 mol% to about 99 mol%, in other embodiments, from about 80 mol% to about 98.5% mol, and, in still other embodiments, from about 87 mol% to about 97.5% mol. The α-olefin content can also range from about 1 mol% to about 40 mol%, in some embodiments, from about 1.5% mol to about 15 mol%, and in some embodiments , from about 2.5% by mol to about 13% by mol.
Exemplary olefin copolymers for use in the present invention include ethylene-based copolymers available under the EXACTTM designation from ExxonMobil Chemical Company of Houston, Texas, USA. Other suitable polyethylene copolymers are available under the designations ENGAGETM, AFFINITYTM, DOWLEXTM (LLDPE) and ATTANETM (ULDPE) from Dow Chemical Company, of Midland, Michigan, USA. Other suitable ethylene polymers are described in U.S. Patent Nos. 4,937,299 to Ewen, et al.; 5,218,071 to Tsutsui, et al.; 5,272,236 of Lai, et al.; and 5,278,272 to Lai, et al., which are incorporated herein in their entirety by reference thereto for all purposes. Suitable propylene copolymers are also commercially available under the designations VISTAMAXXTM from ExxonMobil Chemical Co., of Houston, Texas, USA; FINA™ (eg 8573) from Atofina Chemicals of Feluy, Belgium; TAFMERTM available from Mitsui Petrochemical Industries; and VERSIFYTM available from Dow Chemical Company of Midland, Michigan, USA. Other examples of suitable propylene polymers are described in U.S. Patent Nos. 6,500,563 to Datta, et al.; 5,539,056 to Yang, et al.; and 5,596,052 to Resconi, et al., which are incorporated herein in their entirety by reference thereto for all purposes.
[0041] Any of a variety of generally known techniques can be employed to form olefin copolymers. For example, olefin polymers can be formed using a free radical catalyst or a coordination catalyst (eg, 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 evenly distributed across the different molecular weight fractions. Metallocene-catalyzed polyolefins are described, for example, in U.S. Patent Nos. 5,571,619 of McAlpin, et al.; 5,322,728 to Davis, et al.; 5,472,775 to Obijeski, et al.; 5,272,236 of Lai, et al.; and 6,090,325 to Wheat, et al., which are incorporated herein in their entirety by reference thereto for all purposes. Examples of metallocene catalysts include bis(n-butyl-cyclopentadienyl) titanium dichloride, bis(n-butyl-cyclopentadienyl) zirconium dichloride, bis(cyclopentadienyl) scandium chloride, bis(indenyl) zirconium dichloride, bis(dichloride) methyl-cyclopentadienyl) titanium, bis(methyl-cyclopentadienyl) zirconium dichloride, cobaltocene, cyclopentadienyl-titanium trichloride, ferrocene, hafnocene dichloride, isopropyl (cyclopentadienyl,-1-fluorenyl) zirconium dichloride, diniquelocene dichloride of niobiocene, rutenocene, titanocene dichloride, zirconocene chloride hydride, zirconocene dichloride, and so on. Polymers prepared using metallocene catalysts typically have a narrow range of molecular weights. For example, metallocene-catalyzed polymers may have polydispersity indices (Mw/Mn) below 4, controlled short chain branch distribution, and controlled isotacticity.
[0042] Regardless of the materials employed, the relative percentage of the polymeric stiffening additive in the thermoplastic composition is selected to achieve the desired properties without significantly impacting the biodegradability of the resulting composition. For example, the stiffening additive is typically employed in an amount of from about 0.1% by weight to about 30% by weight, in some embodiments, from about 0.5% by weight to about 20% by weight. , and, in some embodiments, from about 2% by weight to about 12% by weight of the thermoplastic composition, based on the weight of the poly(lactic acid) employed in the composition. Depending on what other components are employed, the actual composition of the stiffening additive in the entire thermoplastic composition may be equal to or less than the ranges mentioned above. In certain embodiments, for example, the stiffening additive is from about 1% by weight to about 30% by weight, in some embodiments from about 2% by weight to about 25% by weight, and in some embodiments, from about 5% by weight to about 20% by weight of the thermoplastic composition. Also, the poly(lactic acid) can constitute from about 70% by weight to about 99% by weight, in some embodiments, from about 75% by weight to about 98% by weight, and, in some embodiments, from about 80% by weight to about 95% by weight of the composition. C. Compatibilizer
[0043] As indicated above, the polymeric stiffening agent, in general, is selected so that it presents a solubility parameter relatively close to that of poly(lactic acid). Among other things, this can enhance phase adhesion and improve the global distribution of discrete domains within the continuous phase. However, in certain domains, optionally, a compatibilizer can be employed to further enhance the compatibility between the poly(lactic acid) and the polymeric stiffening additive. This may be particularly desirable when the polymeric stiffening additive has a polar portion, such as polyurethanes, acrylic resins, etc. When employed, compatibilizers typically comprise from about 1% by weight to about 20% by weight, in some embodiments, from about 2% by weight to about 15% by weight, and, in some embodiments, from about 4% by weight to about 10% by weight of the thermoplastic composition. An example of a suitable compatibilizer is a functionalized polyolefin, which has a polar component provided by one or more functional groups, which are compatible with the water-soluble polymer and a non-polar component provided by an olefin, which is compatible with the olefinic elastomer . The polar component can, for example, be provided by one or more functional groups and the non-polar component can be provided by an olefin. The olefin component of the compatibilizer, in general, can be formed from any linear or branched α-olefin monomer, oligomer or polymer (including copolymers) derived from an olefin monomer as described above.
[0044] The functional group of the compatibilizer can be any group that provides a polar segment to the molecule. 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 EI Du Pont de Nemours and Company, under the name Fusabond®, such as 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 (ethylene-propylene, ethylene-propylene diene monomer
[0045] ("EPDM") or chemically modified ethylene-octene). Alternatively, maleated polyolefins are also available from Chemtura Corporation, under the designation Polybond®, and from Eastman Chemical Company, under the designation Eastman G series. D. Other Components
[0046] A beneficial aspect of the present invention is that good mechanical properties (eg elongation) can be provided without the need for conventional plasticizers such as alkylene glycols (eg poly(ethylene glycols) such as those available from Dow Chemical under the trade name CarbowaxTM), alkane diols and alkylene oxides, which have one or more hydroxyl groups, which attack the poly(lactic acid) ester bonds and result in hydrolytic degradation. Other examples of such plasticizers are described in U.S. Patent No. 2010/0048082 to Topolkaraev, et al., which is incorporated herein in its entirety by reference thereto for all purposes. The thermoplastic composition of the present invention can therefore be substantially free of such plasticizers. However, it should be understood that plasticizers can be used in certain embodiments of the present invention. When used, however, plasticizers typically are present in an amount of less than about 10% by weight, in some embodiments, from about 0.1% by weight to about 5% by weight, and in some embodiments. in some embodiments, from about 0.2% by weight to about 2% by weight of the thermoplastic composition.
[0047] Obviously, other ingredients can be used for a variety of different reasons. For example, materials that can be used include, without limitation, catalysts, pigments, antioxidants, stabilizers, surfactants, waxes, flow promoters, solid solvents, nucleating agents (e.g., titanium dioxide, calcium carbonate, etc.) , particulates, and other materials added to enhance the processability of the thermoplastic composition. When used, it is usually desired that the amounts of these additional ingredients be minimized to ensure optimal compatibility and cost-effectiveness. Therefore, for example, it is normally desired that such ingredients constitute less than about 10% by weight, in some embodiments, less than about 8% by weight, and, in some embodiments, less than about 5% by weight. weight of thermoplastic composition.
[0048] It should also be understood that other components may be included in the thermoplastic composition. One such component that can be employed is an additional biodegradable polyester, including aliphatic polyesters such as polycaprolactone, polyesteramides, modified poly(ethylene terephthalate), poly(lactic acid) (PLA) and its copolymers, poly(acid based terpolymers) lactic), poly(glycolic acid), poly(alkylene carbonates) (eg poly(ethylene carbonate), poly(3-hydroxy-butyrate) (PHB), poly(3-hydroxy-valerate) (PHV), poly(3-hydroxy-butyrate-co-4-hydroxy-butyrate), poly(3-hydroxy-butyrate-co-3-hydroxy-valerate) (PHBV) copolymers, poly(3-hydroxy-butyrate-co-3) -hydroxyhexanoate), poly(3-hydroxy-butyrate-co-3-hydroxy-octanoate), poly(3-hydroxy-butyrate-co-3-hydroxy-decanoate), poly(3-hydroxy-butyrate-co- 3-hydroxy-octadecanoate), and aliphatic succinate-based polymers (eg, poly(butylene succinate), poly(butylene adipate succinate), and poly(ethylene succinate), etc.); aliphatic-aromatic copolyesters ( for example, poly(terephthalate adipate butylene act), poly(ethylene terephthalate adipate), poly(ethylene isophthalate adipate), poly(butylene isophthalate adipate), etc.) and so on. II. Combination
[0049] In general, pure poly(lactic acid) absorbs water from the environment, such that it has a moisture content of about 500 to 600 parts per million ("ppm"), or even higher, based on the dry weight of the starting poly(lactic acid). Moisture content can be determined in a variety of ways, as is known in the art, such as in accordance with ASTM D 7191-05, as described above. Because the presence of water during melt processing can hydrolytically degrade the poly(lactic acid) and reduce its molecular weight, it is sometimes desirable to dry the poly(lactic acid) prior to blending. In most embodiments, for example, it is desired that the poly(lactic acid) have a moisture content of about 300 parts per million ("ppm") or less, in some embodiments about 200 ppm or less, in in some embodiments, from about 1 to about 100 ppm, prior to combination with the stiffening additive. Drying of the poly(lactic acid) can occur, for example, at a temperature of from about 50°C to about 100°C, and, in some embodiments, from about 70°C to about 80°C.
[0050] Once optionally dried, the poly(lactic acid) and stiffening agent can be combined using any of a variety of techniques. In one embodiment, for example, raw materials (eg poly(lactic acid) and stiffening additive) can be supplied separately or in combination. For example, the raw materials can first be dry blended together to form an essentially homogeneous mixture. The raw materials can also be fed, either simultaneously or sequentially, to a melt mass processing device, which combines the materials in a dispersive manner. Batch and/or continuous melt melt processing techniques can be employed. For example, a mixer/kneader, a Banbury mixer, a Farrel continuous mixer, a single screw extruder, a twin screw extruder, a roller mill, etc. can be used to blend and melt the materials. Particularly suitable melt mass processing devices can be a twin screw extruder, which spin together (for example, a ZSK-30 extruder available from Werner and Pfleiderer Corporation, of Ramsey, New Jersey, USA, or a Thermo Prism™ extruder USALAB 16 available from Thermo Electron Corp., Stone, England). Such extruders can include feed and pressure relief ports and provide high intensity distributive and dispersive mixing. For example, the poly(lactic acid) and stiffening agent can be fed to the same or different twin screw extruder feed ports and combined as a melt to form a substantially homogeneous molten mixture. If desired, other additives can also be injected into the polymer melt and/or fed separately into the extruder at a different point along its length. Alternatively, the additives can be combined in advance with the poly(lactic acid) and/or the stiffening agent.
[0051] Regardless of the particular processing technique chosen, the raw materials are combined under sufficient shear/pressure and heat to ensure sufficient dispersion, but not as high as to adversely reduce the size of the discrete domains so that they are unable to achieve the desired stiffness and elongation of the fibers. For example, blending typically occurs at a temperature of from about 170°C to 230°C, in some embodiments from about 175°C to about 220°C, and in some embodiments from about 180°C at about 210°C. Also, the apparent shear rate during melt processing can 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 is equal to 4Q/πR3, where Q is the volumetric flow ("m3/s") of the polymer melt and R is the radius ("m") of the capillary (eg mold of the extruder) through which the molten polymer flows. Obviously, other variables, such as the residence time during melt processing, which is inversely proportional to the throughput rate, can be controlled to achieve the desired degree of homogeneity.
[0052] To achieve the desired shear conditions (for example, speed, residence time, shear rate, melt processing temperature, etc.), the speed of the screw(s) of the extruder can be selected within a certain range. In general, a product temperature rise is observed with increasing screw speed due to additional mechanical energy entering the system. For example, screw speed can range from about 50 to about 300 revolutions per minute ("rpm"), in some embodiments from about 70 to about 250 rpm, and in some embodiments from about 100 at about 200 rpm. This can result in a temperature that is high enough to disperse the hardening additive without adversely impacting the size of the resulting domains. The melt shear rate and, in turn, the degree to which the polymers are dispersed, can also be increased through the use of one or more distributive and/or dispersive mixing elements within the mixing section of the extruder. Suitable dispensing mixers for single screw extruders may include, for example, Saxon, Dulmage, Cavity Transfer mixers, etc. Also, suitable dispersive mixers may include blister ring, Leroy/Maddock, CRD, etc. mixers. As is well known in the art, blending can be further improved by using barrel pins that create a bending and reorientation of the polymer melt mass, such as those used in Buss Kneader Extruders, Cavity Transfer blends and Vortex Interlocking Pin (VIP) mixers.
[0053] As a result of the molten mass combination, a plurality of discrete phase domains are formed and distributed throughout the continuous poly(lactic acid) matrix. Domains can have a variety of different shapes, such as elliptical, spherical, cylindrical, etc. In one embodiment, for example, the domains are substantially elliptical in shape after polymers are combined. Referring to Figure 2A, for example, a schematic representation of such elliptical domains 100 is shown within a primary polymer matrix 110. The physical dimension of an individual domain, after blending, is typically small enough to minimize propagation of fractures through the polymer material when stretching, but large enough to initiate microscopic plastic deformation and provide shear zones in and around particle inclusions. For example, the axial dimension of a domain (eg, length) typically ranges from about 0.05 µm to about 30 µm, in some embodiments from about 0.1 µm to about 25 µm, in in some embodiments from about 0.5 µm to about 20 µm, and in some embodiments from about 1 µm to about 10 µm. Another morphological characteristic is related to the volume content of the domains within the thermoplastic composition. The volume content refers to the average percent volume occupied by the dispersed domains of a given volume unit of the composition, which can be set to be 1 cubic centimeter (cm3). To provide enhanced stiffening, the average volume content of the domains typically is from about 3% to about 20% per cm3, in some embodiments, from about 5% to about 15%, and, in some embodiments, from about 6% to about 12% per cubic centimeter of the composition.
[0054] The melt flow rate, glass transition temperature and melt temperature of the resulting thermoplastic composition may still be somewhat similar to those of poly(lactic acid). For example, the melt flow rate of the composition (on a dry basis) can be from about 0.1 to about 40 grams per 10 minutes, in some embodiments from about 0.5 to about 20 grams per 10 minutes, and in some modes from about 5 to about 15 grams per 10 minutes, determined at a load of 2,160 grams and at a temperature of 190°C. Also, the thermoplastic composition can have a Tg of from about 50°C to about 80°C, and, in some embodiments, from about 55°C to about 65°C, and a melting point of about 150 °C to about 250°C, and, in some embodiments, from about 160°C to about 220°C. III. Fiber Formation
[0055] Fibers formed from the combined thermoplastic composition, in general, can have any desired configuration, including single-component and multi-component (for example, wrap-core configuration, side-by-side configuration, segmented cake configuration, island-at-sea configuration, and so on). In some embodiments, the fibers can contain one or more additional polymers as a component (eg, bicomponents) or constituent (eg, bicomponents) to further enhance strength and other mechanical properties. For example, the thermoplastic composition can form a wrap component of a wrap/core bicomponent fiber, while an additional polymer can form the core component, or vice versa. The additional polymer can be a thermoplastic polymer that is generally not considered biodegradable, such as polyolefins, for example, polyethylene, polypropylene, polybutylene, and so on; polytetrafluoroethylene; polyesters, for example, poly(ethylene terephthalate), and so on; poly(vinyl acetate); poly(vinyl chloride acetate); poly(vinyl butyral); acrylic resins, for example, polyacrylate, poly(methyl acrylate), poly(methyl methacrylate), and so on; polyamides, for example nylon; polyvinyl chloride); poly(vinylidene chloride); polystyrene; poly(vinyl alcohol); and polyurethanes. More desirably, however, the additional polymer is biodegradable, such as aliphatic polyesters such as polyesteramides, modified poly(ethylene terephthalate), poly(glycolic acid), poly(alkylene carbonates) (such as poly(ethylene carbonate) , polyhydroxy-alkanoates (PHA), polyhydroxy-butyrates (PHB), polyhydroxy-valerates (PHV), poly(hydroxy-butyrate-hydroxy-valerate) (PHBV) copolymers, and polycaprolactone, and aliphatic polymers succinate-based (e.g., poly(butylene succinate), poly(butylene adipate succinate), and poly(ethylene succinate)); aromatic polyesters; or other aliphatic-aromatic copolyesters.
[0056] Any of a variety of processes can be used to form fibers in accordance with the present invention. For example, the thermoplastic composition described above can be extruded through a spinneret, subjected to a thermal shock and drawn into the vertical passage of a fiber take-up unit. Once formed, the fibers can then be cut to form staple fibers having an average fiber length in the range of 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 can then be incorporated into a non-woven web as is known in the art, such as bonded carded wefts, air-bonded wefts, etc. Fibers can also be deposited onto a foraminous surface to form a non-woven web.
[0057] Referring to Figure 1, for example, an embodiment of a method for forming fibers is shown in more detail. In this particular embodiment, the poly(lactic acid)/stiffening additive combination is fed into an extruder 12 from a hopper 14. The combination can be fed to hopper 14 using any conventional technique. Regardless, in general, it is desired that the combination have a low moisture content, to minimize hydrolytic degradation of the poly(lactic acid), such as about 300 parts per million ("ppm") or less, in some embodiments, from about 200 ppm or less, in some embodiments, from about 1 to about 100 ppm. Such moisture contents can be achieved by drying, such as at a temperature of from about 50°C to about 100°C, and, in some embodiments, from about 70°C to about 80°C.
[0058] The extruder 12 is heated to a temperature sufficient to extrude the molten polymer. The extruded composition is then passed through a polymer conduit 16 to a spinner 18. For example, the spinner 18 may include a housing containing a stack of spinners having a plurality of plates stacked on top of one another and having a pattern of openings arranged to create flow paths to direct the polymer components. Spinner 18 also has openings arranged in one or more rows. The openings form a curtain of filaments, which are extruded in a downward direction when polymers are extruded through them. Process 10 also employs a quench blower 20 positioned adjacent to the curtain of fibers extending from spinner 18. Air from quenching air blower 20 performs a thermal shock on the fibers, extending from spinner 18. Thermal shock air can be directed from one side of the fiber curtain as shown in Figure 1 or from both sides of the fiber curtain.
[0059] After thermal shock, the fibers are drawn into the vertical passage of a fiber drawing unit 22. Fiber drawing units or vacuums, for use in melt spinning polymers, are well known in the art. Suitable fiber take-up units for use in the process of the present invention include a linear fiber vacuum cleaner of the type shown in U.S. Patent Nos. 3,802,817 and 3,423,255, which are incorporated herein in their entirety by reference thereto for all relevant purposes. The fiber take-up unit 22 generally includes an elongated vertical passage through which fibers are drawn by suction air entering from the sides of the passage and flowing downwardly through the passage. A heater or blower 24 supplies suction air to the fiber take-up unit 22. The suction air draws the fibers and ambient air through the fiber take-up unit 22. attenuate, which increases the molecular orientation or crystallinity of the polymers that make up the fibers. Fibers are deposited through the output opening of the fiber take-up unit 22 and onto a godet roll 42.
[0060] Due to the increased stiffness of the fibers of the present invention, high draw ratios can be employed in the present invention without resulting in fracture. The draw ratio is the linear speed of the fibers after the draw (eg speed of roller 42 or a foraminous surface (not shown), divided by the linear speed of the fibers after extrusion. For example, the draw ratio can be calculated in certain embodiments as follows: Draw Ratio = A/B where: A is the linear speed of the fiber after the draw (ie, roller speed) and is measured directly; eB is the linear speed of the extruded fibers and can be calculated as follows: Linear velocity of extruder fibers = C/(25*π*D*E2) where:C is the throughput through a single hole (grams per minute);D is the bulk density in polymer melt (grams per cubic centimeter); eE is the diameter of the hole (in centimeters) through which the fiber is extruded. In certain embodiments of the present invention, the draw ratio can be from about 200:1 to about 8,500:1, in some embodiments, from about 500:1 to about 7,500:1, and in al in some modes, from about 1,000:1 to about 6,000:1. If desired, the fibers collected on the roller 42, optionally, can be subjected to in-line processing and/or additional conversion steps (not shown) as will be appreciated by those skilled in the art. For example, staple fibers can be formed by "cold drawing" the collected fibers at a temperature below their softening temperature to the desired diameter, and thereafter crimping, texturing and/or cutting the fibers to the length of desired fiber.
Regardless of the particular manner in which they are formed, the present inventors have found that fiber draw significantly increases the axial dimension of the dispersed discrete domains so that they have an elongated, generally linear, shape. As shown in Figure 2B, for example, draw domains 120 have an elongated shape in which the axial dimension is substantially larger than that of the elliptical domains (Figure 2A). For example, the elongated domains can have an axial dimension that is about 10% or more, in some embodiments from about 50% to about 1,000%, and in some embodiments from about 100% to about 500 % greater than the axial dimension of the domains before drawing the fibers. The axial dimension after drawing the fibers, for example, can range from about 5 µm to about 400 µm, in some embodiments from about 10 µm to about 350 µm, and in some embodiments from about 20 µm to about 250 µm. Domains can also be relatively thin and therefore have a small dimension in a direction orthogonal to the axial dimension (ie, cross-sectional dimension). For example, the cross-sectional dimension can be from about 0.02 to about 75 micrometers, in some embodiments from about 0.1 to about 40 micrometers, and in some embodiments from about 0.4 to about 20 micrometers long. This can result in an aspect ratio for the domains (the ratio of axial dimension to cross-sectional dimension) of from about 3 to about 200, in some modalities from about 5 to about 100, and, in some modalities, from about 5 to about 50.
[0062] The presence of these elongated domains is indicative of the ability of the thermoplastic composition to absorb energy conferred during the drawing of fibers. In this way, the composition is not as brittle as the pure polymer and thus can release it when stress is applied, rather than fracturing. By stress release, the polymer can continue to function as a load-bearing member even after the fiber has exhibited substantial elongation. In that regard, the fibers of the present invention are capable of exhibiting improved "peak elongation" properties, i.e., the percent elongation of the fiber at its peak load. For example, the fibers of the present invention can exhibit a peak elongation of about 25% or more, in some embodiments, from about 30% or more, in some embodiments, from about 40% to about 350%, and , in some modalities, from about 50% to about 250%. Such elongations can be achieved by fibers having a wide variety of average diameters, such as those ranging from about 0.1 to about 50 micrometers, in some embodiments, from about 1 to about 40 micrometers, in some embodiments, from from about 2 to about 25 micrometers, and, in some embodiments, from about 5 to about 15 micrometers.
[0063] While having the ability to stretch under tension, the fibers of the present invention can also remain relatively strong. One parameter that is indicative of the relative strength of the fibers of the present invention is "tenacity", which indicates the tensile strength of a fiber expressed as strength per unit linear density. For example, the fibers of the present invention can have a tenacity of from about 7.35 to about 58.84 mN (about 0.75 to about 6.0 grams-strength ("gf")) per denier, in in some embodiments from about 9.80 to about 44.13 mN (from about 1.0 to about 4.5 gf) per denier, and in some embodiments from about 14.71 to about 39 .23 mN (from about 1.5 to about 4.0 gf) per denier. Fiber denier may vary depending on the desired application. Typically, fibers are shaped to have a denier per filament (i.e., the unit of linear density equal to the mass in grams per 9,000 meters of fiber) of less than about 6, in some embodiments, of less than about 3, and, in some embodiments, from about 0.5 to about 3.
[0064] If desired, the fibers of the present invention can also be formed into a coherent weft structure by randomly deposition of the fibers onto a forming surface (optionally with the aid of a vacuum) and then by binding the resulting web using any known technique. For example, an endless foraminous forming surface can be positioned below the fiber take-up unit and receive fibers from an outlet opening. A vacuum can be positioned below the forming surface to draw the filaments and consolidate the unbonded nonwoven web. Once formed, the non-woven web can then be bonded using any conventional technique, such as with an adhesive or in an autogenous manner (e.g. fusing and/or self-adhesive fibers without an external adhesive applied). Autogenous bonding, for example, can be achieved by contacting the fibers while they are semi-fused or sticky, or simply by combining an adhesive resin and/or solvent with the polylactic acid(s) )) used to form the fibers. Suitable autogenous bonding techniques can include ultrasonic bonding, thermal bonding, air bonding, calender bonding, and so on. For example, the web can be further bonded or embossed with a pattern by a thermomechanical process, in which the web is passed between a heated smooth anvil roll and a heated pattern roll. The pattern roll can have any embossed pattern that provides the desired weft properties or appearance. Desirably, the pattern roll defines an embossed pattern that defines a plurality of bonding sites that define a bonding area between about 2% and 30% of the total roll area. Exemplary binding patterns include, for example, those described in U.S. Patent Nos. 3,855,046 to Hansen et al., 5,620,779 to Levy et al., 5,962,112 to Haynes et al., 6,093,665 to Sayovitz et al., as well as U.S. Industrial Design Patent Nos. 428,267 by Romano et al.; 390,708 from Brown; 418,305 to Zander, et al.; 384,508 by Zander, et al.; 384,819 of Zander, et al.; 358,035 of Zander, et al. and 315,990 to Blenke, et al., all of which are incorporated herein, in their entirety by reference thereto, for all purposes. The pressure between the rollers and the temperature of the rollers are balanced to obtain can be from about 876 to about 350,254 N/m (from about 5 to about 2000 pounds per linear inch). The pressure between the rolls and the temperature of the rolls are balanced to obtain the desired properties or web appearance, while maintaining the farm-like properties. As is well known to those of skill in the art, the temperature and pressure required may vary depending on many factors, including, but not limited to, pattern bonding area, polymer properties, fiber properties, and properties of the nonwoven.
[0065] In addition to spunbond webs, a variety of other non-woven webs can also be formed from the thermoplastic composition according to the present invention, such as meltblown webs, bonded and carded webs, wet dispersed webs, webs air-dispersed, coform wefts, hydraulically entangled wefts, etc. For example, the thermoplastic composition can be extruded through a plurality of thin mold capillaries into converging high velocity gas (e.g. air) streams, which attenuate the fibers to reduce their diameters. Thereafter, the meltblown fibers are carried by the high velocity gas stream and are deposited onto a collection surface to form a web of randomly dispersed meltblown fibers. Alternatively, the polymer can be formed into a carded web, by placing fiber bales, formed from the thermoplastic composition, in a collector, which separates the fibers. Next, the fibers are sent through a blending or carding unit, which additionally breaks apart and aligns the fibers in the machine direction, so as to form a fibrous non-woven web oriented in the machine direction. Once formed, the nonwoven web typically is stabilized by one or more known binding techniques.
[0066] If desired, the non-woven web can also be a composite that contains a combination of the fibers of the thermoplastic composition and other types of fibers (eg staple fibers, filaments, etc.). For example, additional synthetic fibers can be used, such as those formed from polyolefins, for example, polyethylene, polypropylene, polybutylene, and so on; polytetrafluoroethylene; polyesters, for example, poly(ethylene terephthalate), and so on; poly(vinyl acetate); poly(vinyl chloride acetate); poly(vinyl butyral); acrylic resins, for example, polyacrylate, poly(methyl acrylate), poly(methyl methacrylate), and so on; polyamides, for example nylon; polyvinyl chloride); poly(vinylidene chloride); polystyrene; poly(vinyl alcohol); and polyurethanes; poly(lactic acid); etc. If desired, biodegradable polymers such as poly(glycolic acid) (PGA), poly(lactic acid) (PLA), poly(e-malic acid) (PMLA), poly(ε-caprolactone) (PCL), poly(p -dioxanone) (PDS), poly(butylene succinate) (PBS) and poly(3-hydroxybutyrate) (PHB) may also be employed. Some examples of known synthetic fibers include core-wrap bicomponent fibers available from KoSa Inc., of Charlotte, North Carolina, under the designations T-255 and T-256, both of which use a polyolefin wrap, or T-254 , which features a low melting point copolyester wrap. Still other known bicomponent fibers that can be used include those available from Chisso Corporation, of Moriyama, Japan, or Fibervisions LLC, of Wilmington, Delaware, USA. Poly(lactic acid) staple fibers may also be employed, such as those commercially available from Far Eastern Textile, Ltd., of Taiwan.
[0067] The composite may also contain pulp fibers such as pulp with high average length fibers, pulp with low average length fibers, or mixtures thereof. An example of suitable high average length fluff pulp fibers include softwood kraft pulp fibers. Softwood kraft pulp fibers are derived from coniferous trees and include pulp fibers such as, but not limited to, northern, western and southern softwood species, including redwood, red cedar, Canadian pine , Douglas fir, spruce, pine (southern pine), common spruce (eg spruce), bamboo, their combinations, and so on. Northern softwood kraft pulp fibers can be used in the present invention. An example of commercially available southern softwood kraft pulp fibers suitable for use in the present invention include those available from Weyerhaeuser Company, with offices in Federal Way, Washington, under the tradename "NF-405". Another pulp suitable for use in the present invention is a bleached sulfate wood pulp, primarily containing softwood fibers, which is available from Bowater Corp., with offices in Greenville, South Carolina, under the trade name Pulp CoosAbsorb S. Fibers of low medium length can also be used in the present invention. An example of suitable low medium length pulp fibers are hardwood kraft pulp fibers. Hardwood kraft pulp fibers are derived from deciduous trees and include pulp fibers such as, but not limited to, eucalyptus, maple, birch, poplar, etc. Eucalyptus kraft pulp fibers may be particularly desired to increase softness, enhance clarity, increase opacity and change the pore structure of the sheet to increase its capillary action capability. Bamboo or cotton fibers can also be used.
[0068] Nonwoven composites can be formed using a variety of known techniques. For example, the non-woven composite can be a "coform material" which contains a stabilized blend or matrix of the fibers of the thermoplastic composition and an absorbent material. As an example, coform materials can be produced by a process in which at least one meltblown mold head is disposed close to a chute through which absorbent materials are added to the web while it is in formation. Such absorbent materials can include, but are not limited to, pulp fibers, superabsorbent particles, inorganic and/or organic absorbent materials, treated polymer staple fibers, and so forth. The relative percentages of the absorbent material can vary over a wide range depending on the desired characteristics of the non-woven composite. For example, the non-woven composite may contain from about 1% by weight to about 60% by weight, in some embodiments, from about 5% by weight to about 50% by weight, and, in some embodiments, from about 10% by weight and about 40% by weight of fibers of the thermoplastic composition. The non-woven composite may also contain from about 40% by weight to about 99%, in some embodiments, from 50% by weight to about 95% by weight, and, in some embodiments, from about 60% by weight. to about 90% by weight of absorbent material. Some examples of such coform materials are described in U.S. Patent Nos. 4,100,324 to Anderson, et al.; 5,284,703 to Everhart, et al.; and 5,350,624 to Georger et al., which are incorporated herein in their entirety by reference thereto for all purposes.
[0069] Non-woven laminates can also be formed in the present invention, in which one or more layers are formed from the thermoplastic composition. For example, the non-woven web of one layer may be a spunbond, which contains the thermoplastic composition, while the non-woven web of the other layer contains the thermoplastic composition, other biodegradable polymer(s) and/or any other polymer (eg polyolefins). In one embodiment, the non-woven laminate contains a layer of meltblown positioned between two layers of spunbond to form a spunbond/meltblown/spunbond (“SMS”) laminate. If desired, the spunbond layer(s) may be formed from the thermoplastic composition. The meltblown layer can be formed from the thermoplastic composition, other biodegradable polymer(s) and/or any other polymer (eg polyolefins). Various techniques for forming SMS laminates are described in U.S. Patent Nos. 4,041,203 to Brock et al.; 5,213,881 to Timmons, et al.; 5,464,688 to Timmons, et al.; 4,374,888 to Bornslaeger; 5,169,706 of Collier, et al. and 4,766,029 to Brock et al., as well as US Patent Application Publication No. 2004/0002273 to Fitting, et al., all of which are incorporated herein in their entirety by reference thereto for all purposes . Obviously, the non-woven laminate can be of another configuration and have any desired number of meltblown and spunbond layers, such as spunbond/meltblown/meltblown/spunbond ("SMMS"), spunbond/meltblown ("SM") laminates, etc. Although the grammage of the non-woven laminate can be tailored to the desired application, it generally ranges from about 10 to about 300 grams per square meter ("g/m2"), in some embodiments from about 25 to about 200 g/m2 and, in some embodiments, from about 40 to about 150 g/m2.
[0070] If desired, the non-woven web or laminate can be applied with various treatments to impart desirable characteristics. For example, the web can be treated with liquid repellent additives, antistatic agents, surfactants, dyes, anti-mist agents, blood and alcohol repellants, fluorochemicals, lubricants and/or antimicrobial agents. In addition, the web can be subjected to an electrical treatment, which imparts an electrostatic charge to improve filtration efficiency. The charge can include layers of positive and negative charge trapped on or near the polymer surface, or clouds of charge stored in the polymer bulk. The charge can also include polarizing charges that are frozen in alignment with the dipoles of the molecules. Techniques for subjecting a fabric to an electrical treatment are well known to those skilled in the art. Examples of such techniques include, but are not limited to, thermal, liquid contact, electron beam, and corona discharge techniques. In a particular modality, the electrical treatment is a corona discharge technique, which involves subjecting the laminate to a pair of electrical fields that present opposite polarities. Other methods for forming an electrified material are described in U.S. Patent Nos. 4,215,682 to Kubik, et al.; 4,375,718 to Wadsworth; 4,592,815 from Nakao; 4,874,659 of Ando; 5,401,446 to Tsai, et al.; 5,883,026 to Reader, et al.; 5,908,598 of Rousseau, et al.; 6,365,088 to Knight, et al., which are incorporated herein in their entirety by reference thereto for all purposes. IV. Articles
[0071] The non-woven weft can be used in a wide variety of applications. For example, the weft can be incorporated into a "medical product", such as garments, surgical garments, face masks, general caps, surgical caps, slippers, sterilization wraps, heating blankets, heating pads, and so on. . Of course, the non-woven weft can also be used in a number of other articles. For example, the non-woven web can 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, absorbent personal care articles, such as diapers, training pants, absorbent underwear, incontinence articles, feminine hygiene products (eg, sanitary napkins), swimwear , baby wipes, glove scarf, and so on; medical absorbent articles such as garments, fenestration materials, linings, bed pillows, bandages, absorbent pads and medical wipes; handkerchiefs for food services; articles of clothing; pockets, and so on. Suitable materials and processes for forming such articles are well known to those skilled in the art. Absorbent articles, for example, typically include a substantially liquid-impermeable layer (e.g., outer covering), a liquid-permeable layer (e.g., body facing liner, sudden insult layer, etc.), and an absorbent core . In one embodiment, for example, a non-woven web formed in accordance with the present invention can be used to form an outer covering of an absorbent article. If desired, the non-woven web can be laminated to form a liquid impermeable film, which is either vapor permeable or vapor impermeable.
[0072] The present invention can be better understood with reference to the following examples. In each of the Examples below, the poly(lactic acid) was dried in a desiccant dryer at a temperature of about 77°C (to a moisture content below 300 ppm) prior to combination with the hardening additive. The resulting blend was also dried in a desiccant dryer at a temperature of 52°C to 66°C (125°F to 150°F) (to a moisture content below 300 ppm, and optionally 200 ppm) before spinning the fibers.
[0073] The following samples refer to combinations of poly(lactic acid) (PLA), which contain stiffening additives. Refer to these combinations by a sample number in Examples 1-2, as follows:
[0074] Sample 1 - 100% by weight of PLA 6021 D. PLA 6021 D is poly(lactic acid) (Natureworks) having a melt flow rate of 10 g/10 minutes at 190°C.
[0075] Sample_2 - 90% by weight PLA 6201 D and 10% by weight EscoreneTM Ultra 7720. EscoreneTM Ultra 7720 is an ethylene-vinyl acetate ("EVA") resin (Exxonmobil) having a mass flow rate in melting of 150 g/10 minutes at 190°C and a density of 0.946 g/cm3.
Sample = 92.5% by weight of PLA 6201 D and 7.5% by weight of Escorene™ Ultra 7720.
[0077] Sample_4 - 90% by weight PLA 6201 D and 10% by weight Pearlbond® 123. Pearlbond® 123 is a polycaprolactone - thermoplastic polyurethane elastomer (Merquinsa) having a melt flow rate of 70 to 90 g/10 minutes at 170°C.
[0078] Sample 5 - 90% by weight PLA 6201 D and 10% by weight AffinityTM EG 8185. AffinityTM EG 8185 is an α-olefin/ethylene (Dow Chemical) copolymer plastomer having a mass flow rate in melting of 30 g/10 minutes at 190°C and a density of 0.885 g/cm3.
[0079] Sample_6 - 90% by weight PLA 6201 D and 10% by weight AffinityTM EG 8200. AffinityTM EG 8200 is an octene/ethylene (Dow Chemical) copolymer plastomer having a melt flow rate of 5 g/10 minutes at 190°C and a density of 0.870 g/cm3.
[0080] Sample_7 - 90% by weight PLA 6201 D and 10% by weight AffinityTM GA 1950. AffinityTM GA 1950 is an octene/ethylene (Dow Chemical) copolymer plastomer having a melt flow rate of 500 g /10 minutes at 190°C and a density of 0.874 g/cm3.
[0081] Sample_8 - 90% by weight of PLA 6201 D and 10% by weight of Pearlthane™ Clear 15N80. PearlthaneTM Clear 15N80 Polyurethane elastomer based on thermoplastic polyether (Merquinsa) featuring a melt flow rate of 10 to 90 g/10 minutes at 190°C.
[0082] Sample_9 - 92.5% by weight of PLA 6201 D and 7.5% by weight of EscoreneTM Ultra LD 755.12. EscoreneTM Ultra LD 755.12 is an ethylene-vinyl acetate (“EVA”) resin (Exxonmobil) having a melt flow rate of 25 g/10min at 190°C and a density of 0.952 g/cm3.
[0083] Sample 10 - 92.5% by weight of PLA 6201 D and 7.5% by weight of AffinityTM EG 8200.
[0084] Sample 11 - 92.5% by weight of PLA 6201 D and 7.5% by weight of Pearlbond® 123.EXAMPLE 1
[0085] The ability to form a combination of poly(lactic acid) and a stiffening additive has been demonstrated. More particularly, a co-rotating twin screw extruder (ZSK-30, diameter 30 mm, length 1328 mm) was employed for composite formation, which was manufactured by Werner & Pfleiderer Corporation, of Ramsey, New Jersey. The extruder had 14 zones, consecutively numbered 1-14 from the feed hopper to the mold. The first No. 1 drum received the resins via two gravimetric feeders (one for the PLA and one for the hardening additive) at a total capacity of 9 kg (20 pounds) per hour. The mold used to extrude the resin had 3 openings (6 millimeters in diameter), which were 4 millimeters apart. The extruder was operated at a speed of 160 revolutions per minute. Upon formation, the extruded resin was cooled on a fan-cooled conveyor belt and formed into pellets by a Conair pelletizer. The composite formation conditions are shown in Table 1. Table 1: Composite Formation Conditions

[0086] The melt flow rate and moisture content of various resulting thermoplastic combinations were then determined. The results are shown below.Table 2: MFR and Moisture Content

[0087] As indicated, the moisture content was greater than 100% PLA (typically < 100 ppm), lower than the moisture content typically seen when conventional plasticizers (eg, poly(ethylene glycol)) are used - that is, 300-500 ppm.
[0088] SEM photographs were also taken of a cross section of Sample 2, after being annealed for 10 minutes at about 85°C. The results are shown in Figures 3-4. As shown, the composition contained a plurality of generally spherical domains of the polymeric stiffening additive. The domains had an axial dimension from about 1 µm to about 3 µm.EXAMPLE 2
[0089] The ability to form fibers from a combination of poly(lactic acid) and a stiffening additive has been demonstrated. More particularly, several of the combinations from Example 1 (Samples 2, 3, 4 and 5) were fed into a co-rotating twin screw extruder (ZSK-30, diameter 30mm, length 1,328mm) which was used for the composite formation, which was manufactured by Werner & Pfleiderer Corporation, of Ramsey, New Jersey, USA. The extruder had 14 zones, consecutively numbered 1-14 from the feed hopper to the mold. The first No. 1 drum received the resins via two gravimetric feeders, at a total capacity of 9 kg (20 pounds) per hour. The mold used to extrude the resin had 3 openings (6 millimeters in diameter), which were 4 millimeters apart. Upon formation, the extruded resin was cooled on a fan-cooled conveyor belt and formed into pellets by a Conair pelletizer. The screw speed was 160 revolutions per minute (“rpm”). Upon formation, the extruded resin was cooled on a fan-cooled conveyor belt and formed into pellets. The pellets were then fed to an extruder heated to a temperature of 240°C. The molten mass was extruded through a single-component spinning stack (16 holes, 0.600 mm hole size), at a rate of 0.23 grams per hole per minute, to form continuous fibers, which were then subjected to a thermal shock using forced air supplied by a blower at a temperature of 25°C. The continuous fibers were then mechanically removed and collected on a roller, the speed of which was increased until the fibers were broken. In processing the blends to form fibers, heated thermal shock was not used because heated thermal shock led to an inability to collect fibers.
Unlike the PLA blends, the PLA Control (Sample 1) was dried at 74°C (165°F) for approximately one week, before being spun to form a fiber. The following table shows the parameters for fiber spinning.Table 3: Fiber Spinning Conditions

[0091] Sample 2 (PLA with 10% EVA 7720) was difficult to process due to fluctuation in extruder pressure, which caused the screw speed to vary from 36-44 rpm. As such, samples could only be collected at 1,800 mpm (descending stretch ratio 2,789) before the break. Similarly, Sample 4 (PLA with 10% PB 123) also increased the screw rotation speed. During processing, screw speeds reached about 60 rpm, to maintain the extruder control pressure of 600 psi, and fibers could only be collected at 1,500 mpm (down draw ratio of 2,324).
[0092] Sample 3 (PLA with 7.5% EVA 7720) was more stable and could be collected at 2300 mpm. Sample 5 (PLA with 10% Affinitty EG8185) had the highest outlet pressure, but was stable and was able to be collected at 2300 mpm (down stretch ratio 3.563).
[0093] After all fibers were spun, ten (10) fibers from each of the samples were tested for various purposes. Fiber samples were measured three times and the diameter averaged. The table below shows the results from fiber testing and also includes productivity, roller speed and draw ratio for the fibers. Table 4: Mechanical Properties of Fibers

[0094] As indicated, the toughness values for the blends (Samples 2-5) were not significantly less than that of PLA at 100% by weight and fell only around 3% to 5%. Although all combinations showed an increase in peak elongation compared to PLA at 100% (Sample 1), they also showed a high level of variability. Sample 2 had the highest peak elongation in that it achieved 2-3 times the 100% PLA elongation. Sample 4 had the second highest level of elongation, but this sample also had the largest fibers. Samples 3 and 5 showed similar elongation levels.
[0095] The thermal properties of the fibers were also tested. The results are shown below.Table 5: Thermal Properties of Fibers

[0096] As indicated, the glass transition temperature of the poly(lactic acid) (Sample 1) was not significantly decreased with the addition of the hardening additive.
[0097] SEM photographs were also taken of the fibers from Sample 2, both in cross-section and along the length of the fibers. The cross-sectional photographs were taken after the sample was treated with an oxygen plasma etching at 30°C. Cross-sectional images are shown in Figures 5-6. As shown, the polymeric stiffening additive formed a nanocylindrical dispersed phase within the poly(lactic acid), where the diameter or cross-sectional dimension of the domains was from about 0.25 to about 0.3 micrometers. Figures 7-8 also show the fibers along the axial dimension. As shown, the dispersed stiffening additive domains are highly elongated and result in an aspect ratio of 10 or more.
The ability to form fibers from a combination of 90% by weight of poly(lactic acid) (PLA 6201D, Natureworks®) and 10% by weight of a stiffening additive has been demonstrated.
[0099] The hardening additive was VistamaxxTM 2120 (Exxonmobil), which is a polyolefin copolymer/elastomer with a melt flow rate of 29 g/10 minutes (190°C, 2,160 g) and a density of 0.866 g/cm3. Polymers were fed into a co-rotating twin screw extruder (ZSK-30, diameter 30 mm, length 1328 mm) for composite formation, which was manufactured by Werner & Pfleiderer Corporation, of Ramsey, New Jersey, USA. The extruder had 14 zones, consecutively numbered 1-14 from the feed hopper to the mold. The first No. 1 drum received the resins via a gravimetric feeder, at a total capacity of 5 kg (11 pounds) per hour. The mold used to extrude the resin had 3 openings (6 millimeters in diameter), which were 4 millimeters apart. Upon formation, the extruded resin was cooled on a fan-cooled conveyor belt and formed into pellets by a Conair pelletizer. The screw speed was 100 revolutions per minute (“rpm”). Upon formation, the extruded resin was cooled on a fan-cooled conveyor belt and formed into pellets. The pellets were then passed through the twin screw extruder for a second pass at a rate of 7 kg/h (15 lb/h), at a melt temperature of 200°C and a screw speed of 200 rpm and again pelleted. The pellets were then fed to an extruder heated to a temperature of 240°C. The extruder capacity was 0.20 grams per hole per minute (in a 16 hole wiring pile). The molten mass was extruded through the spin pile to form continuous fibers, which were then subjected to a thermal shock using forced air supplied by a blower at a temperature of 25°C. The continuous fibers were then drawn through a fiber drawing unit by stretching the fibers and sent over a roller at a speed of 2800 meters per minute (“mpm”). The resulting circulation rate was therefore 4.338.EXAMPLE 4
[00100] Fibers were formed as described in Example 3, except that the stiffening additive was VistamaxxTM 2320 (Exxonmobil), which is a polyolefin copolymer/elastomer with a melt flow rate of 40 g/10 minutes ( 190°C, 2,160 g) and a density of 0.864 g/cm3.EXAMPLE 5
[00101] Fibers were formed as described in Example 3, except that 3% by weight of Fusabond® MD-353D, a maleic anhydride modified polypropylene copolymer (DuPont) was added to the mixture.
[00102] Fibers were formed as described in Example 4, except that 3% by weight of Fusabond(R) MD-353D was added to the mixture.
[00103] Fibers were formed as described in Example 3, except that 2% by weight of SCC4837 (Exxon 3155 PP/TiO2 in a 50/50 ratio) was added to the mixture.
[00104] Fibers were formed as described in Example 4, except that 2% by weight of SCC4837 was added to the mixture.
Fibers were formed as described in Example 3, except that 2% by weight of SCC4837 and 3% by weight of Fusabond® MD-353D were added to the mixture.
[00106] Fibers were formed as described in Example 4, except that 2% by weight of SCC4837 and 3% by weight of Fusabond® MD-353D (DuPont) were added to the mixture.
[00107] Ten (10) samples were prepared according to Examples 3-10 and then tested for toughness and elongation. Results (average) are shown below. Table 6: Fiber Properties for Examples 3-10
EXAMPLE 11
[00108] The ability to form fibers from a combination of 90% by weight of poly(lactic acid) (PLA 6201D, Natureworks®) and 10% by weight of a stiffening additive has been demonstrated.
[00109] The hardening additive was EscoreneTM Ultra 7720. The polymers were fed to a co-rotating twin screw extruder (ZSK-30, diameter 30 mm, length 1328 mm) for composite formation, which was manufactured by Werner & Pfleiderer Corporation, of Ramsey, New Jersey, USA. The extruder had 14 zones, consecutively numbered 1-14 from the feed hopper to the mold. The first No. 1 drum received the resins via a gravimetric feeder, at a total capacity of 5 kg (11 pounds) per hour. The mold used to extrude the resin had 3 openings (6 millimeters in diameter), which were 4 millimeters apart. Upon formation, the extruded resin was cooled on a fan-cooled conveyor belt and formed into pellets by a Conair pelletizer. The screw speed was 100 revolutions per minute (“rpm”). Upon formation, the extruded resin was cooled on a fan-cooled conveyor belt and formed into pellets. The pellets were then passed through the twin screw extruder for a second pass at a rate of 7 kg/h (15 lb/h), at a melt temperature of 200°C and a screw speed of 200 rpm and again pelleted. The pellets were then fed to an extruder heated to a temperature of 230°C. The extruder capacity was 0.20 grams per hole per minute (in a 16 hole wiring pile). The molten mass was extruded through the spin pile to form continuous fibers, which were then subjected to a thermal shock using forced air supplied by a blower at a temperature of 25°C. The continuous fibers were then drawn through a fiber drawing unit by stretching the fibers and sent over a roller at a speed of 1800 meters per minute (“mpm”). The resulting draw rate was 2,789.EXAMPLE 12
[00110] Fibers were formed as described in Example 11, except that the fibers were formed at an extrusion temperature of 210°C.
[00111] Fibers were formed as described in Example 3, except that the stiffening additive was EscoreneTM Ultra 7840E (Exxonmobil), which is an ethylene-vinyl acetate ("EVA") copolymer having a melt flow rate 43 g/10 minutes (190°C, 2,160 g) and a density of 0.955 g/cm 3 . In addition, the pellets were extruded to form fibers at a temperature of 235°C.EXAMPLE 14
[00112] Fibers were formed as described in Example 11, except that 2% by weight of SCC4837 (Exxon 3155 PP/TiO2 in a 50/50 ratio) was added to the mixture. In addition, the pellets were extruded to form fibers at a temperature of 240°C.EXAMPLE 15
[00113] Fibers were formed as described in Example 11, except that 2% by weight of SCC4837 was added to the mixture. In addition, the pellets were extruded to form fibers at a temperature of 220°C.
[00114] Ten (10) samples were prepared according to Examples 11-15 and then tested for toughness and elongation. Results (average) are shown below. Table 7: Fiber Properties for Examples 11-15
EXAMPLE 16
[00115] The ability to form fibers from a combination of 90% by weight of poly(lactic acid) (PLA 6201D, Natureworks®) and 10% by weight of a stiffening additive has been demonstrated. The stiffening additive was PP 3155 (ExxonMobil), a polypropylene homopolymer. Polymers were fed into a co-rotating twin screw extruder (ZSK-30, diameter 30 mm, length 1328 mm) for composite formation, which was manufactured by Werner & Pfleiderer Corporation, of Ramsey, New Jersey, USA. The extruder had 14 zones, consecutively numbered 1-14 from the feed hopper to the mold. The first No. 1 drum received the resins via a gravimetric feeder at a total capacity of 7 kg (15 pounds) per hour. The mold used to extrude the resin had 3 openings (6 millimeters in diameter), which were 4 millimeters apart. Upon formation, the extruded resin was cooled on a fan-cooled conveyor belt and formed into pellets by a Conair pelletizer. The screw speed was 100 revolutions per minute (“rpm”). Upon formation, the extruded resin was cooled on a fan-cooled conveyor belt and formed into pellets. The pellets were then fed to an extruder heated to a temperature of 230°C. The extruder capacity was 0.40 grams per hole per minute (in a 16 hole wiring pile). The molten mass was extruded through the spin pile to form continuous fibers, which were then subjected to a thermal shock using forced air supplied by a blower at a temperature of 25°C. The continuous fibers were then drawn through a fiber drawing unit by stretching the fibers and sent over a roller at a speed of 2000 meters per minute (“mpm”). The resulting draw rate was 3,099.EXAMPLE 17
[00116] Fibers were formed as described in Example 16, except that the fibers were formed at an extrusion temperature of 235°C. The continuous fibers were drawn over a roller at a speed of 2800 meters per minute (“mpm”). The resulting draw rate was 4,338.EXAMPLE 18
[00117] Fibers were formed as described in Example 16, except that the fibers were formed at an extrusion temperature of 240°C. The continuous fibers were drawn over a roller at a speed of 2000 meters per minute (“mpm”). The resulting draw ratio was 3,099.
[00118] Ten (10) samples were prepared according to Examples 16-18 and then tested for toughness and elongation. Results (average) are shown below. Table 8: Fiber Properties for Examples 16-18

[00119] Although the invention has been described in detail with respect to specific embodiments thereof, it will be appreciated that those skilled in the art, when they reach an understanding of the foregoing, may readily devise changes to, variations of, and equivalents to those embodiments. Accordingly, the scope of the present invention is to be assessed as that of the appended claims and any equivalents thereto.

权利要求:
Claims (14)
[0001]
1. Poly(lactic acid) fiber, which extends in a longitudinal direction and has an average diameter of 2 to 25 micrometers, characterized by comprising a thermoplastic composition that contains a plurality of discrete domains dispersed within a continuous phase, the domains discrete domains containing a polymeric stiffening additive and the continuous phase containing poly(lactic acid), at least one of the discrete domains being elongated in the longitudinal direction of the fiber and having a length of 5 to 400 micrometers, with the fiber exhibiting elongation peak of 25% or more and a toughness of 7.35 to 58.84 mN by DENIER, in which the ratio of the Hildebrand solubility parameter for the poly(lactic acid) to the Hildebrand solubility parameter for the additive is polymeric stiffening is from 0.5 to 1.5, and wherein the polymeric stiffening additive includes a polyolefin, polyurethane, poly(vinyl acetate), poly(vinyl alcohol), polyester, polytetrafluoroethyl ene, acrylic resin, polyamide, poly(vinyl chloride), poly(vinylidene chloride), polystyrene or a combination thereof.
[0002]
2. Poly(lactic acid) fiber, according to claim 1, characterized in that the polymeric stiffening additive has a Hildebrand solubility parameter of 15 to 30 MJoules1/2/m3/2.
[0003]
3. Poly(lactic acid) fiber according to claim 1 or 2, characterized in that the ratio of the melt flow rate for the poly(lactic acid) in relation to the mass flow rate in melting of the polymeric hardening additive is 0.2 to 8, and the polymeric hardening additive having a melt flow rate of 5 to 150 grams per 10 minutes, determined at a load of 2,160 grams at one temperature 190°C, measured in accordance with ASTM D-1238.
[0004]
4. Poly(lactic acid) fiber, according to any one of the preceding claims, characterized in that the ratio of the Young's modulus of elasticity of the poly(lactic acid) in relation to the Young's modulus of elasticity of the stiffening additive polymeric is from 2 to 500, and the polymeric stiffening additive has a Young's modulus of elasticity from 10 to 200 MegaPascal.
[0005]
5. Poly(lactic acid) fiber according to any one of the preceding claims, characterized in that the stiffening additive includes a polyolefin, such as a homopolymer of propylene, copolymer of propylene/α-olefin, copolymer of ethylene /α-olefin or a combination thereof.
[0006]
6. Poly(lactic acid) fiber, according to any one of the preceding claims, characterized in that the polymeric stiffening additive constitutes from 2% by weight to 25% by weight of the thermoplastic composition, and the poly(lactic acid ) constitutes from 75% by weight to 98% by weight of the thermoplastic composition.
[0007]
7. Poly(lactic acid) fiber, according to any one of the preceding claims, characterized in that the thermoplastic composition is free of a plasticizer.
[0008]
8. Poly(lactic acid) fiber, according to any one of the preceding claims, characterized in that the discrete domain has a length of 20 micrometers to 250 micrometers and an aspect ratio from 3 to 200; and/or wherein the volume content of the domains is 3% to 20% per cubic centimeter of the composition.
[0009]
9. Poly(lactic acid) fiber according to any one of the preceding claims, characterized in that the fiber exhibits a peak elongation of 40% to 350% and a tenacity of 14.71 to 39.23 mN per DENIER.
[0010]
10. Non-woven weft, characterized in that it comprises the fiber as defined in any one of the preceding claims.
[0011]
An absorbent article, characterized in that it comprises an absorbent core positioned between a liquid permeable layer and a generally liquid impermeable layer, the absorbent article comprising the non-woven web as defined in claim 10.
[0012]
12. A method for forming a poly(lactic acid) fiber, characterized by comprising: blending a poly(lactic acid) with a polymeric stiffening additive to form a thermoplastic composition, wherein the composition contains a plurality of discrete, dispersed domains within a continuous phase, the discrete domains containing the polymeric stiffening additive and the continuous phase containing the poly(lactic acid); extruding the thermoplastic composition through a mold; and drawing the extruded composition to form a fiber, wherein the domains of the drawn fiber are elongated in a longitudinal direction of the fibers so that the length of the elongated domains is greater than the length of the domains before drawing, wherein the ratio of the Hildebrand solubility parameter for poly(lactic acid) relative to the Hildebrand solubility parameter of the polymeric stiffening additive is 0.5 to 1.5, and wherein the polymeric stiffening additive includes a polyolefin, polyurethane, poly (vinyl acetate), poly(vinyl alcohol), polyester, polytetrafluoroethylene, acrylic resin, polyamide, poly(vinyl chloride), poly(vinylidene chloride), polystyrene or a combination thereof.
[0013]
13. Method according to claim 12, characterized in that the draw ratio is from 200:1 to 8,500:1, and preferably from 1,000:1 to 6,000:1, or in which the length of the domains, before drawing, is from 0.5 to 20 micrometers and the length of the elongated domains, after drawing, is from 5 to 400 micrometers, or where the polymeric stiffening additive has a Hildebrand solubility parameter of 15 to 30 MJoules1/2/m3/2.
[0014]
A method for forming a non-woven web, characterized in that it comprises: searing fibers by the method as defined in claim 12 or 13; and randomly deposit the fibers onto a surface to form a non-woven web.

类似技术:

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公开号 | 公开日 | 专利标题

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BR112013003178B1|2021-08-03|POLY| FIBER, NON-WOVEN WEFT, ABSORBENT ARTICLE, AND METHODS FOR THE FORMATION OF A POLY| FIBER AND FOR THE FORMATION OF A NON-WOVEN WEFT

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BR112013003313B1|2020-12-22|method for forming a poly | fiber, poly | fiber, and nonwoven weft

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US20210180216A1|2021-06-17|Renewable Polyester Fibers having a Low Density

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BRPI0822434B1|2018-05-29|Nonwoven weft, absorbent article and method for forming nonwoven weft

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US20120164905A1|2012-06-28|Modified Polylactic Acid Fibers

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EP2812469B1|2016-08-31|Modified polylactic acid fibers

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BRPI0909968B1|2018-10-09|fibers formed from a mixture of a modified aliphatic-aromatic copolyester and thermoplastic starch

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RU2588235C2|2016-06-27|Modified polylactic acid fibres

同族专利:

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公开号 | 公开日

---

BR112013003178A2|2021-03-02|

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EP2603623A4|2014-01-08|

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AU2011288213A1|2013-01-31|

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MX343263B|2016-10-28|

---

CN103069059A|2013-04-24|

---

US10753023B2|2020-08-25|

---

KR20130097152A|2013-09-02|

---

EP2603623B1|2018-11-07|

---

MX2013001627A|2013-03-22|

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WO2012020336A3|2012-05-24|

---

RU2561122C2|2015-08-20|

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EP2603623A2|2013-06-19|

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US20120040185A1|2012-02-16|

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KR101810273B1|2017-12-18|

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CN103069059B|2016-01-06|

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WO2012020336A2|2012-02-16|

---

AU2011288213B2|2016-05-19|

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RU2013109177A|2014-09-20|

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法律状态:
2021-03-23| B06U| Preliminary requirement: requests with searches performed by other patent offices: procedure suspended [chapter 6.21 patent gazette]|

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2021-06-22| B09A| Decision: intention to grant [chapter 9.1 patent gazette]|

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2021-08-03| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 06/07/2011, OBSERVADAS AS CONDICOES LEGAIS. PATENTE CONCEDIDA CONFORME ADI 5.529/DF, QUE DETERMINA A ALTERACAO DO PRAZO DE CONCESSAO. |

优先权:

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申请号 | 申请日 | 专利标题

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US12/855,984|2010-08-13|

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US12/855,984|US10753023B2|2010-08-13|2010-08-13|Toughened polylactic acid fibers|

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PCT/IB2011/053010|WO2012020336A2|2010-08-13|2011-07-06|Toughened polylactic acid fibers|

---