US20020187344A1 - Dimensionally stable polyester yarn for high tenacity treated cords - Google Patents

Dimensionally stable polyester yarn for high tenacity treated cords Download PDF

Info

Publication number
US20020187344A1
US20020187344A1 US10/140,841 US14084102A US2002187344A1 US 20020187344 A1 US20020187344 A1 US 20020187344A1 US 14084102 A US14084102 A US 14084102A US 2002187344 A1 US2002187344 A1 US 2002187344A1
Authority
US
United States
Prior art keywords
yarn
tenacity
drawn
melting point
cord
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Abandoned
Application number
US10/140,841
Inventor
Charles Nelson
Jayendra Bheda
Peter Rim
James Turner
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Performance Fibers Inc
Original Assignee
Individual
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from US08/527,292 external-priority patent/US5646334A/en
Priority claimed from US09/571,843 external-priority patent/US6403006B1/en
Application filed by Individual filed Critical Individual
Priority to US10/140,841 priority Critical patent/US20020187344A1/en
Publication of US20020187344A1 publication Critical patent/US20020187344A1/en
Priority to US10/440,642 priority patent/US6828021B2/en
Priority to US10/980,546 priority patent/US7108818B2/en
Assigned to PERFORMANCE FIBERS, INC. reassignment PERFORMANCE FIBERS, INC. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: HONEYWELL INTERNATIONAL, INC., A CORP. OF DELAWARE
Assigned to GENERAL ELECTRIC CAPITAL CORPORATION reassignment GENERAL ELECTRIC CAPITAL CORPORATION SECURITY INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: PERFORMANCE FIBERS ENTERPRISES, INC., PERFORMANCE FIBERS HOLDINGS, INC., PERFORMANCE FIBERS, INC.
Assigned to PERFORMANCE FIBERS, INC., PERFORMANCE FIBERS HOLDINGS, INC., PERFORMANCE FIBERS ENTERPRISES, INC. reassignment PERFORMANCE FIBERS, INC. RELEASE BY SECURED PARTY (SEE DOCUMENT FOR DETAILS). Assignors: GENERAL ELECTRIC CAPITAL CORPORATION
Abandoned legal-status Critical Current

Links

Images

Classifications

    • GPHYSICS
    • G01MEASURING; TESTING
    • G01NINVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
    • G01N1/00Sampling; Preparing specimens for investigation
    • G01N1/02Devices for withdrawing samples
    • G01N1/22Devices for withdrawing samples in the gaseous state
    • G01N1/26Devices for withdrawing samples in the gaseous state with provision for intake from several spaces
    • DTEXTILES; PAPER
    • D01NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01DMECHANICAL METHODS OR APPARATUS IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS
    • D01D5/00Formation of filaments, threads, or the like
    • D01D5/12Stretch-spinning methods
    • DTEXTILES; PAPER
    • D01NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01FCHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
    • D01F6/00Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof
    • D01F6/58Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from homopolycondensation products
    • D01F6/62Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from homopolycondensation products from polyesters
    • GPHYSICS
    • G01MEASURING; TESTING
    • G01NINVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
    • G01N1/00Sampling; Preparing specimens for investigation
    • G01N1/02Devices for withdrawing samples
    • G01N1/22Devices for withdrawing samples in the gaseous state
    • G01N1/2226Sampling from a closed space, e.g. food package, head space
    • G01N2001/2229Headspace sampling, i.e. vapour over liquid
    • GPHYSICS
    • G01MEASURING; TESTING
    • G01NINVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
    • G01N7/00Analysing materials by measuring the pressure or volume of a gas or vapour
    • G01N7/14Analysing materials by measuring the pressure or volume of a gas or vapour by allowing the material to emit a gas or vapour, e.g. water vapour, and measuring a pressure or volume difference
    • YGENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10TTECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00Stock material or miscellaneous articles
    • Y10T428/29Coated or structually defined flake, particle, cell, strand, strand portion, rod, filament, macroscopic fiber or mass thereof
    • Y10T428/2913Rod, strand, filament or fiber
    • YGENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10TTECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00Stock material or miscellaneous articles
    • Y10T428/29Coated or structually defined flake, particle, cell, strand, strand portion, rod, filament, macroscopic fiber or mass thereof
    • Y10T428/2913Rod, strand, filament or fiber
    • Y10T428/2929Bicomponent, conjugate, composite or collateral fibers or filaments [i.e., coextruded sheath-core or side-by-side type]

Definitions

  • This invention relates to polyester multifilament yarn with high modulus and low shrinkage particularly useful for the textile reinforcement of tires.
  • the yarn of the invention provides high treated cord tenacity while maintaining or increasing treated cord dimensional stability when compared to prior art yarns.
  • a process for production of the multifilament polyester yarn is an aspect of the invention.
  • Polyethylene terephthalate filaments of high strength are well known in the art and are commonly utilized in industrial applications including tire cord for rubber reinforcement, conveyor belts, seat belts, V-belts and hosing.
  • Polyethylene terephthalate yarn can be prepared by spinning under high stress conditions in the transition region between oriented-amorphous and oriented-crystalline undrawn yarns.
  • the invention is accomplished by selection of process parameters to form an undrawn yarn that is a crystalline, partially oriented yarn with a crystallinity of 3 to 15 percent and a melting point elevation of 2 to 10° C.
  • the spun yarn is then hot drawn to a total draw ratio between 1.5/l and 2.5/l with the resulting unique combination of properties: (A) a terminal modulus of at least 20 g/d, (B) a dimensional stability defined by E 4.5 +FS ⁇ 13.5 percent, (C) a tena-city of at least 7 grams per denier, (D) a melting point elevation of 9 to 14° C., and (E) an amorphous orientation function of less than 0.75.
  • the drawn yarn is twisted and plied to produce tire cord and then treated with resorcinol-formaldehyde-latex.
  • the resulting treated tire cord unexpectedly provides high tenacity in combination with improved dimensional stability.
  • FIG. 1 represents treated cord dimensional stability as judged by plots of LASE-5 versus free shrinkage for the yarns prepared in Example I.
  • FIG. 2 represents a comparison of treated cord tenacities at a given free shrinkage for the yarns of Example I.
  • FIG. 3 represents treated cord dimensional stability as judged by plots of LASE-5 versus free shrinkage for the yarns prepared in Example II.
  • FIG. 4 represents a comparison of treated cord tenacities at a given free shrinkage for the yarns of Example II.
  • FIG. 5 represents a plot of LASE-5 versus free shrinkage of drawn yarns from Example II.
  • FIG. 6 plots treated cord tenacity versus LASE-5 at a given free shrinkage (4 percent) and demonstrates the unexpected increase in treated cord tenacity obtained by the yarns of this invention. (Example II).
  • FIG. 7 represents the percent crystallinity and melting point elevation for the undrawn yarns for Example II.
  • FIG. 8 gives the range of spinning speeds wherein prior art U.S. Pat. No. 4,491,657 teaches that different undrawn birefringences can be achieved.
  • FIG. 9 gives the DSC traces for drawn yarns from Example II.
  • FIG. 10 represents a plot of the shrinkage force vs. free shrinkage of drawn yarns from Example II.
  • the high strength polyester multifilament yarn of the present invention provides improved dimensional stability together with improved treated cord tenacity when incorporated as fibrous reinforcement into rubber composites such as tires.
  • modulus at elevated temperature (up to 120° C.) is the ‘true’ parameter governing performance. Due to the highly crystalline nature of treated cords based on conventional or dimensionally stable yarns, the modulus retention (in percent) at elevated tire temperatures is essentially similar for all current commercial treated cords and for those of this invention. Thus, room temperature measurement of LASE-5 is sufficient to establish meaningful differences in cord dimensional stability.
  • the polyester yarn contains at least 90 mol percent polyethylene terephthalate (PET).
  • PET polyethylene terephthalate
  • the polyester is substantially all polyethylene terephthalate.
  • the polyester may incorporate as copolymer units minor amounts of units derived from one or more ester-forming ingredients other than ethylene glycol and terephthalic acid or its derivatives.
  • ester-forming ingredients which may be copolymerized with the polyethylene terephthalate units include glycols such as diethylene glycol, trimethylene glycol, tetramethylene glycol, hexamethylene glycol, etc., and dicarboxylic acids such as isophthalic acid, hexahydroterephthalic acid, bibenzoic acid, adipic acid, sebacic acid, azelaic acid, etc.
  • glycols such as diethylene glycol, trimethylene glycol, tetramethylene glycol, hexamethylene glycol, etc.
  • dicarboxylic acids such as isophthalic acid, hexahydroterephthalic acid, bibenzoic acid, adipic acid, sebacic acid, azelaic acid, etc.
  • the multifilament yarn of the present invention commonly possesses a denier per filament of about 1 to 20 (e.g. about 3 to 10), and commonly consists of about 6 to 600 continuous filaments (e.g. about 20 to 400 continuous filaments).
  • the denier per filament and the number of continuous filaments present in the yarn may be varied widely as will be apparent to those skilled in the art.
  • the multifilament yarn is particularly suited for use in industrial applications wherein high strength polyester fibers have been utilized in the prior art.
  • the yarn of this invention is particularly suitable for use as tire cord for the reinforcment of tires and for the fiber reinforcement of rubber articles and other composite structures.
  • the fibers are particularly suited for use in environments where elevated temperatures (e.g. 80° C. to 180° C.) are encountered. Not only does the filamentary material undergo a relatively low degree of shrinkage for a high strength fibrous material, but it provides enhanced translational efficiency for tenacity when the yarn is translated into treated cord.
  • the characterization parameters referred to herein may conveniently be determined by testing the multifilament yarn which consists of substantially parallel filaments.
  • Birefringence was determined using a polarizing light microscope equipped with a Berek compensator and the fraction crystallinity was determined by conventional density measurements.
  • the amorphous orientation function was determined from the following relationship (see R. J. Samuels, Structured Polymer Properties, New York, John Wiley & Sons).
  • n Xf c ⁇ n c +(1 ⁇ X ) f a ⁇ n a + ⁇ n f
  • ⁇ n c intrinsic birefringence of crystal (0.220 for polyethylene terephthalate)
  • ⁇ n a intrinsic birefringence of amorphous (0.275 for polyethylene terephthalate)
  • ⁇ c theoretical density of 100% crystalline phase (1.529 gm/cm 3 )
  • Melting points were determined with a Perkin-Elmer Differential Scanning Calorimeter (DSC) from the maxima of the endotherm resulting from scanning a 2 mg sample at 20° C. per minute. As shown in FIG. 9, M.P. is taken to be the temperature of the highest temperature peak of the DSC trace. Melting point elevations cited are defined as the difference between the specimen melting point (M.P.) and the melting point (M.P.Q.) of a specimen after subsequent rapid liquid nitrogen quenching of an encapsulated DSC sample from the melt. The melting point of this re-crystallized sample is due to crystals which have cold-crystallized during the melting point test procedure.
  • DSC Perkin-Elmer Differential Scanning Calorimeter
  • Z melting point characteristic
  • the Z parameter is an important characteristic for drawn yarns which have not received a significant thermal treatment. Such drawn yarns have a percent crystallinity from density measurements of 28% or less. Application of an effective heat treatment to the yarn results in an increase in the measured Z value and crystallinity. However, this additional heat treatment does not significantly influence the ultimate properties of the final treated cord. Thus, the measured Z value can be higher than an intrinsic value Z* which reflects inherent differences in the subsequently treated cords. This intrinsic Z* can be estimated from the measured Z and density for drawn yarns receiving a thermal treatment by the following empirical relation:
  • the tenacity values (i.e. at least 7 grams per denier), compare favorably with these particular parameters exhibited by commercially available polyethylene terephthalate tire cord yarns.
  • the tensile properties referred to herein were determined on yarns conditioned for two hours through the utilization of an Instron tensile tester (Model TM) using a 10-inch gauge length and a strain rate of 120 percent per minute in accordance with ASTM D885. All tensile measurements were made at room temperature.
  • the high strength multifilament yarn of the present invention possesses an internal morphology which, for a LASE-5 of 4.5 grams per denier or greater, manifests an unusually low free shrinkage propensity of less than 8 percent, and preferably less than 6 percent when measured in air at 177° C.
  • filaments of commercially available dimensionally stable tire cord yarns based on polyethylene terephthalate commonly shrink about 6 to 10 percent when tested in air at 177° C.
  • Free shrinkage (FS) values were determined in accordance with ASTM D885 with the exception that the testing load was 9.3 grams. Such improved dimensional stability is of particular importance if the product serves as fibrous reinforcement in a radial tire.
  • Elongation at the specified load of 4.5 g/d (E 4.5 ) is an alternate indicator of modulus. It is particularly useful in that the sum E 4.5 +FS is a good indicator of dimensional stability for yarns processed under different relaxation levels. Lower sums (E 4.5 +FS) indicate better dimensional stability.
  • N network chains or crosslinks/cc
  • the classical method for determining crosslink density is to measure shrinkage force and shrinkage for samples which have been drawn (or relaxed) to different extents.
  • the constraining force corresponds to the shrinkage force.
  • the shrinkage value needed for the effective crosslink calculation is the difference between the shrinkage measured at a given constraining force and the shrinkage measured at a minimal constraining force of 5 grams. Note that since curvature is exhibited at high shrinkage forces only data up to a shrinkage force of 0.08 g/d should be used for the above computation. For industrial applications, a temperature of 177° C. was employed.
  • the melt-spinnable polyester is supplied to an extrusion spinnerette at a temperature above its melting point and below the temperature at which the polymer degrades substantially.
  • the residence time at this stage is kept to a minimum and the temperature should not rise above 315° C., preferably 310° C.
  • the flow curve of molten PET in terms of melt viscosity versus shear rate has been shown to be important for steady-state melt spinning giving uniform individual multifilaments.
  • R radius of the capillary in meters.
  • the extruded filaments then traverse a conventional yarn solidification zone where quench air impinges on the spun yarn thereby freezing in desirable internal structural features and preventing the filaments from fusing to one another.
  • the solidification zone comprises (a) a retarded cooling zone, preferably comprising a gaseous atmosphere heated at a temperature of 150 to 450° C., and (b) a cooling zone adjacent said retarded cooling zone wherein said yarn is rapidly cooled and solidified in a blown air atmosphere.
  • the key to the current process is to utilize extruding polymer with IV greater than 0.80 and adjust processing conditions to achieve a crystalline, partially oriented yarn with a crystallinity of 3 to 15 percent and a melting point elevation of 2 to 10° C.
  • One skilled in the art can achieve this by adjusting the following conditions: length and temperature of an annealing zone adjacent to the spinnerette, diameter of the spinnerette holes, method of blowing the quench, quench air velocity, and drawdown in the quench column.
  • the speed of withdrawal of the yarn from the solidification zone is an important parameter affecting the stress on the spun fiber, and should be adjusted to yield the desired characteristics. It is preferred that the melting point elevation be 2 to 5° C. and that ⁇ 1 ⁇ 2 is at least 26°.
  • the spun yarn was then drawn between rolls at temperatures above the glass transition temperature (80° C.) to within 85 percent of the maximum draw ratio.
  • This drawing process involves multiple drawing and conditioning steps to achieve a tenacity above 7 grams per denier, a LASE-5 above 3.7 grams per denier and a shrinkage less than 8 percent.
  • the effective crosslink density (N) be between 10 ⁇ 10 21 and 20 ⁇ 10 21 crosslinks per cubic centimeter.
  • the high viscosity polymer spun as above can be drawn in known ways such as that disclosed in U.S. Pat. No. 4,195,052 to Davis et al. and in U.S. Pat. No. 4,251,481 to Hamlyn.
  • the yarn can be drawn off-line. However, for economic reasons it is preferred to draw the yarn in a continuous integrated spin-draw process.
  • the drawn yarns are usually twisted into a cord and then dipped into one or more conventional adhesive coatings, referred to as cord dips and then subjected to various stretch/relax sequences at elevated temperature to 5 achieve the optimum combination of tenacity, shrinkage, LASE-5. Again this technology is well-known to those skilled in the art who adjust twist and treating conditions for specific end-uses. Details for the treating conditions employed are given in the examples.
  • Treated cords prepared in such manner from the yarn of this invention have been shown to have the following treated cord properties:
  • FIGS. 1 - 4 Graphs of LASE-5 and tenacity versus free shrinkage were constructed as shown in FIGS. 1 - 4 . Comparison between different starting yarns can be made at the interpolated values at 4% free shrinkage.
  • a 1000 denier PET yarn was produced by extruding 300 individual filaments at 62.5 lbs/hr into a heated sleeve (220-300° C. Temp) and then solidifying in an air quenching column. Yarns were then taken-up at varying winder speeds. The residence times in the heated sleeve and quench columns were 0.02 to 0.03 and 0.2 seconds, respectively. The Godet speed at the bottom of the spinning column and the winder speed were adjusted to give different undrawn birefringences and crystallinity levels. In all cases the same shear rate in the spinnerette holes was employed. Yarn intrinsic viscosity was 0.88.
  • the measured Z is much lower than those for Example I, which have higher crystallinity due to lower viscosity and slower drawing stages. Due to the high drawing speeds and modest roll temperatures, none of the samples in this example received an effective heat treatment. The maximum crystallinity without heat treatment is 27-28% with 27.2% representing the average.
  • FIG. 5 gives such a plot for drawn yarns prepared similar to II-AD and II-ED, but then relaxed to various degrees in the final zone.
  • the solid lines in FIG. 5 represent the data for the relaxation series where ( ⁇ ) and ( ⁇ ) represent points for yarns similar to II-AD and II-ED, respectively.
  • the individual data points from Table IV are also plotted as encircled sample designations from Table IV. One would expect a family of linear lines with increasing slope. On this basis, the products of this invention would be defined by

Landscapes

  • Engineering & Computer Science (AREA)
  • Health & Medical Sciences (AREA)
  • Chemical & Material Sciences (AREA)
  • Life Sciences & Earth Sciences (AREA)
  • Textile Engineering (AREA)
  • Biomedical Technology (AREA)
  • Mechanical Engineering (AREA)
  • General Chemical & Material Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Molecular Biology (AREA)
  • Physics & Mathematics (AREA)
  • Analytical Chemistry (AREA)
  • Biochemistry (AREA)
  • General Health & Medical Sciences (AREA)
  • General Physics & Mathematics (AREA)
  • Immunology (AREA)
  • Pathology (AREA)
  • Artificial Filaments (AREA)

Abstract

Polyethylene terephthalate yarn is prepared by spinning under high stress conditions in the transition region between oriented-amorphous and oriented-crystalline undrawn yarns by selection of process parameters to form an undrawn yarn that is a crystalline, partially oriented yarn with a crystallinity of 3 to 15 percent and a melting point elevation of 2 to 10° C. The spun yarn is then hot drawn to a total draw ratio between 1.5/1 and 2.5/1 with the resulting properties: (A) a terminal modulus of at least 20 g/d, (B) a dimensional stability defined by E4.5+FS<13.5 percent, (C) a tenacity of at least 7 grams per denier, (D) a melting point elevation of 9 to 14° C., and (E) an amorphous orientation function of less than 0.75. The resulting treated tire cord provides high tenacity in combination with improved dimensional stability.

Description

  • This is a continuation-in-part application of copending U.S. application Ser. No. 215, 178 filed July 5, 1988.[0001]
  • BACKGROUND OF THE INVENTION
  • 1. Field of the Invention [0002]
  • This invention relates to polyester multifilament yarn with high modulus and low shrinkage particularly useful for the textile reinforcement of tires. The yarn of the invention provides high treated cord tenacity while maintaining or increasing treated cord dimensional stability when compared to prior art yarns. A process for production of the multifilament polyester yarn is an aspect of the invention. [0003]
  • 2. Description of the Prior Art [0004]
  • Polyethylene terephthalate filaments of high strength are well known in the art and are commonly utilized in industrial applications including tire cord for rubber reinforcement, conveyor belts, seat belts, V-belts and hosing. [0005]
  • Continued improvement in high strength industrial yarns particularly suited for use as fibrous reinforcement in rubber tires is an ongoing need in the industry. In particular, the improvement of treated cord tenacity and dimensional stability are desired objectives. U.S. Pat. No. 4,101,525 to Davis et al. provides an industrial strength multifilament polyester yarn with high initial modulus and low shrinkage. Although Davis et al. does not provide treated cord data, it is commonly known that compared to conventional tire cords such yarn provides a reduced tenacity when the yarn is converted to the treated tire cord. Additionally, rapid cooling of the filament immediately after emerging from the spinneret can result in excessive filament breakage and thus yield yarn with poor mechanical quality. U.S. Pat. No. 4,491,657 to Saito et al. discloses high modulus, low shrinkage polyester yarn, but requires a low terminal modulus to achieve good yarn to treated cord conversion efficiency for such dimensionally stable yarns. The low terminal modulus is carried over into the treated cord and results in a lower tenacity than the high terminal modulus cords of the present invention. Also, as shown in FIG. 8 the process of Saito et al. requires high spinning speeds, which makes it difficult to process on-panel, i.e. a continuous spin-draw process. [0006]
  • SUMMARY OF THE INVENTION
  • Polyethylene terephthalate yarn can be prepared by spinning under high stress conditions in the transition region between oriented-amorphous and oriented-crystalline undrawn yarns. The invention is accomplished by selection of process parameters to form an undrawn yarn that is a crystalline, partially oriented yarn with a crystallinity of 3 to 15 percent and a melting point elevation of 2 to 10° C. The spun yarn is then hot drawn to a total draw ratio between 1.5/l and 2.5/l with the resulting unique combination of properties: (A) a terminal modulus of at least 20 g/d, (B) a dimensional stability defined by E[0007] 4.5+FS<13.5 percent, (C) a tena-city of at least 7 grams per denier, (D) a melting point elevation of 9 to 14° C., and (E) an amorphous orientation function of less than 0.75. The drawn yarn is twisted and plied to produce tire cord and then treated with resorcinol-formaldehyde-latex. The resulting treated tire cord unexpectedly provides high tenacity in combination with improved dimensional stability.
  • BRIEF DESCRIPTION OF THE DRAWINGS
  • FIG. 1 represents treated cord dimensional stability as judged by plots of LASE-5 versus free shrinkage for the yarns prepared in Example I. [0008]
  • FIG. 2 represents a comparison of treated cord tenacities at a given free shrinkage for the yarns of Example I. [0009]
  • FIG. 3 represents treated cord dimensional stability as judged by plots of LASE-5 versus free shrinkage for the yarns prepared in Example II. [0010]
  • FIG. 4 represents a comparison of treated cord tenacities at a given free shrinkage for the yarns of Example II. [0011]
  • FIG. 5 represents a plot of LASE-5 versus free shrinkage of drawn yarns from Example II. [0012]
  • FIG. 6 plots treated cord tenacity versus LASE-5 at a given free shrinkage (4 percent) and demonstrates the unexpected increase in treated cord tenacity obtained by the yarns of this invention. (Example II). [0013]
  • FIG. 7 represents the percent crystallinity and melting point elevation for the undrawn yarns for Example II. [0014]
  • FIG. 8 gives the range of spinning speeds wherein prior art U.S. Pat. No. 4,491,657 teaches that different undrawn birefringences can be achieved. [0015]
  • FIG. 9 gives the DSC traces for drawn yarns from Example II. [0016]
  • FIG. 10 represents a plot of the shrinkage force vs. free shrinkage of drawn yarns from Example II.[0017]
  • DESCRIPTION OF THE PREFERRED EMBODIMENT
  • The high strength polyester multifilament yarn of the present invention provides improved dimensional stability together with improved treated cord tenacity when incorporated as fibrous reinforcement into rubber composites such as tires. [0018]
  • With the current emphasis on the monoply radial passenger tire, the demand for ever increasing dimensionally stable cords continues to be high. Dimensional stability is defined as high modulus at a given shrinkage and directly relates to tire sidewall indentations (SWI) and tire handling. While the modulus of the cord in the tire is the primary variable governing both SWI and handling, shrinkage is important in two ways. First, excessive cord shrinkage during tire curing can significantly reduce the modulus from that of the starting treated cord. Second, cord shrinkage is a potential source of tire non-uniformity. Thus, comparison of modulus and tenacity at a given shrinkage is a meaningful comparison for tire cords. Since tire cords experience deformations of a few percent during service, a good practical measure of modulus is LASE-5 (load at 5 percent elongation). Alternatively, E[0019] 4.5 (elongation at 4.5 g/d load) can be used as a practical measure of compliance.
  • For both tire SWI and handling, modulus at elevated temperature (up to 120° C.) is the ‘true’ parameter governing performance. Due to the highly crystalline nature of treated cords based on conventional or dimensionally stable yarns, the modulus retention (in percent) at elevated tire temperatures is essentially similar for all current commercial treated cords and for those of this invention. Thus, room temperature measurement of LASE-5 is sufficient to establish meaningful differences in cord dimensional stability. [0020]
  • The polyester yarn contains at least 90 mol percent polyethylene terephthalate (PET). In a preferred embodiment, the polyester is substantially all polyethylene terephthalate. Alternatively, the polyester may incorporate as copolymer units minor amounts of units derived from one or more ester-forming ingredients other than ethylene glycol and terephthalic acid or its derivatives. Illustrative examples of other ester-forming ingredients which may be copolymerized with the polyethylene terephthalate units include glycols such as diethylene glycol, trimethylene glycol, tetramethylene glycol, hexamethylene glycol, etc., and dicarboxylic acids such as isophthalic acid, hexahydroterephthalic acid, bibenzoic acid, adipic acid, sebacic acid, azelaic acid, etc. [0021]
  • The multifilament yarn of the present invention commonly possesses a denier per filament of about 1 to 20 (e.g. about 3 to 10), and commonly consists of about 6 to 600 continuous filaments (e.g. about 20 to 400 continuous filaments). The denier per filament and the number of continuous filaments present in the yarn may be varied widely as will be apparent to those skilled in the art. [0022]
  • The multifilament yarn is particularly suited for use in industrial applications wherein high strength polyester fibers have been utilized in the prior art. The yarn of this invention is particularly suitable for use as tire cord for the reinforcment of tires and for the fiber reinforcement of rubber articles and other composite structures. The fibers are particularly suited for use in environments where elevated temperatures (e.g. 80° C. to 180° C.) are encountered. Not only does the filamentary material undergo a relatively low degree of shrinkage for a high strength fibrous material, but it provides enhanced translational efficiency for tenacity when the yarn is translated into treated cord. [0023]
  • The unexpected combination of tenacity and dimensional stability seems to originate from the emergence of a two-phase structure (crystal plus amorphous) during spinning. As a threshold amorphous orientation is achieved there is a simultaneous crystallization of the more oriented amorphous regions. [0024]
  • In the conventional PET yarn process, crystallization occurs mainly in the drawing step since orientation in the spinning column is low. In current commercial dimensionally stable yarn processes, there is significant amorphous orientation during spinning but crystallization essentially occurs only in the drawing step. In the present invention, the amorphous orientation in spinning is sufficient to result in modest levels of oriented crystalline nuclei (with a degree of 3 to 15 percent). The consequence of this crystalline nucleation is to remove the high end of amorphous-orientation distribution leaving behind the less oriented amorphous regions. Thus, while the overall orientation increases with increased spinning stress, the amorphous orientation decreases immediately following the onset of crystallization in the spin-line. Further increasing the spin-line stress results in more net orientation and more separation of the more oriented amorphous regions via crystallization. The net result is further increased amorphous orientation at very high spinning stresses. In such a process amorphous orientation first increases with spinning stress prior to threshold values where crystallization occurs, then decreases as modest spun crystallinity is achieved, and finally again increases at very high stress levels. The theoretical analysis of the consequence of crystallization on amorphous-orientation distribution has been discussed by Desai and Abhiraman [J. Polym. Sci., Polym. Letters Edition, 23, 213-217 (1985)]. [0025]
  • The characterization parameters referred to herein may conveniently be determined by testing the multifilament yarn which consists of substantially parallel filaments. [0026]
  • Birefringence was determined using a polarizing light microscope equipped with a Berek compensator and the fraction crystallinity was determined by conventional density measurements. The amorphous orientation function was determined from the following relationship (see R. J. Samuels, Structured Polymer Properties, New York, John Wiley & Sons). [0027]
  • Δn=Xf c Δn c+(1−X)f a Δn a +Δn f
  • where [0028]
  • Δn=birefringence [0029]
  • X=fraction crystalline [0030]
  • f[0031] c=crystalline orientation function
  • Δn[0032] c=intrinsic birefringence of crystal (0.220 for polyethylene terephthalate)
  • f[0033] a=amorphous orientation function
  • Δn[0034] a=intrinsic birefringence of amorphous (0.275 for polyethylene terephthalate)
  • Δn[0035] f=form birefringence (negligable for this system)
  • Crystal orientations were determined with Herman's orientation function employing the average angular azimuthal breadth of the (010) and (100) reflections of the wide angle x-ray diffraction pattern: [0036]
  • fc=½(3 cos2φ−1)
  • where, [0037]
  • f[0038] c=crystal orientation function
  • φ=average orientation angle [0039]
  • Density of the undrawn and drawn yarn is a convenient measure of percent crystallinity. Densities of undrawn and drawn yarns were determined in n-heptane/carbon tetrachloride density gradient column at 23° C. The gradient column was prepared and calibrated according to ASTM D1505-68 with density ranging from 1.30-1.43 g/cm[0040] 3. Percent crystallinity was then calculated from XTAL % = ( ρ s - ρ a ) ( ρ c - ρ a ) × 100
    Figure US20020187344A1-20021212-M00001
  • ρs—measured density of sample in gm/cm[0041] 3
  • ρa—theoretical density of 100% amorphous phase (1.335 gm/cm[0042] 3)
  • ρc—theoretical density of 100% crystalline phase (1.529 gm/cm[0043] 3)
  • While birefringence and crystallinity measurements are effective for characterizing the amorphous orientation of drawn yarns, undrawn yarn produced near the transition between oriented-amorphous and oriented-crystalline structures demands a more direct method of evaluating degree of orientation in the amorphous phase. For this, wide angle X-Ray diffraction patterns were obtained in the transmission geometry on a Philips diffractometer with Cu radiation and diffracted beam monochromator. Several radial scans were obtained at various azimuthal angles between the equator and the meridian. These scans were resolved into crystalline and amorphous components through a DuPont curve resolver (Gaussian lineshape). The azimuthal half-width at half-height (φ½) for the intensity distribution of amorphous halo was determined by plotting the height of amorphous peak as a function of azimuthal angle. [0044]
  • Melting points (M.P.) were determined with a Perkin-Elmer Differential Scanning Calorimeter (DSC) from the maxima of the endotherm resulting from scanning a 2 mg sample at 20° C. per minute. As shown in FIG. 9, M.P. is taken to be the temperature of the highest temperature peak of the DSC trace. Melting point elevations cited are defined as the difference between the specimen melting point (M.P.) and the melting point (M.P.Q.) of a specimen after subsequent rapid liquid nitrogen quenching of an encapsulated DSC sample from the melt. The melting point of this re-crystallized sample is due to crystals which have cold-crystallized during the melting point test procedure. An alternate measure of melting point characteristic (Z) which is a more sensitive parameter than M.P. for many samples of this invention, is defined as the height (H[0045] 9) of the trace at M.P.Q.+9° C. divided by the sum of the heights at M.P.Q.+40C (H4) and at M.P.Q+19° C. (H19): Z = H 9 H 4 + H 19
    Figure US20020187344A1-20021212-M00002
  • The Z parameter is an important characteristic for drawn yarns which have not received a significant thermal treatment. Such drawn yarns have a percent crystallinity from density measurements of 28% or less. Application of an effective heat treatment to the yarn results in an increase in the measured Z value and crystallinity. However, this additional heat treatment does not significantly influence the ultimate properties of the final treated cord. Thus, the measured Z value can be higher than an intrinsic value Z* which reflects inherent differences in the subsequently treated cords. This intrinsic Z* can be estimated from the measured Z and density for drawn yarns receiving a thermal treatment by the following empirical relation: [0046]
  • log Z/Z* =0.033(XTAL %−27.2)2
  • No correction is made for yarns with 27.2% or less crystallinity. Thus, a drawn yarn with Z=1.8 and crystallinity of 29.5% would have Z*=1.3, which would be the value of Z if the measurement were made prior to the thermal treatment step. Drawn yarns of the present invention have been found to have Z* greater than or equal to 1.3. Effective heat treatment of such yarns have produced dimensionally stable yarns with Z greater than or equal to 1.7. [0047]
  • Regardless of which melting point characteristic is used, the differences in thermal response provide a direct quantitative measure of differences in internal morphological structure. It is felt that this unique morphological structure rather than [0048] melting point 20 elevation per se gives rise to the desired improved performance.
  • Intrinsic viscosity (IV) of the polymer and yarn is a convenient measure of the degree of polymerization and molecular weight. IV is determined by measurement of relative solution viscosity (η[0049] r) of PET sample in a mixture of phenol and tetrachloroethane (60/40 by weight) solvents. The relative solution viscosity (ηr) is the ratio of the flow time of a PET/solvent solution to the flow time of pure solvent through a standard capillary. Billmeyer approximation (J. Polym. Sci. 4, 83-86 (1949)) is used to calculate IV according to I V = 1 / 4 ( η r - 1 ) C + 3 / 4 ln η r C
    Figure US20020187344A1-20021212-M00003
  • where C is concentration in gm/100 ml. [0050]
  • The tenacity values (i.e. at least 7 grams per denier), compare favorably with these particular parameters exhibited by commercially available polyethylene terephthalate tire cord yarns. The tensile properties referred to herein were determined on yarns conditioned for two hours through the utilization of an Instron tensile tester (Model TM) using a 10-inch gauge length and a strain rate of 120 percent per minute in accordance with ASTM D885. All tensile measurements were made at room temperature. [0051]
  • The high strength multifilament yarn of the present invention possesses an internal morphology which, for a LASE-5 of 4.5 grams per denier or greater, manifests an unusually low free shrinkage propensity of less than 8 percent, and preferably less than 6 percent when measured in air at 177° C. For instance, filaments of commercially available dimensionally stable tire cord yarns based on polyethylene terephthalate commonly shrink about 6 to 10 percent when tested in air at 177° C. Free shrinkage (FS) values were determined in accordance with ASTM D885 with the exception that the testing load was 9.3 grams. Such improved dimensional stability is of particular importance if the product serves as fibrous reinforcement in a radial tire. Elongation at the specified load of 4.5 g/d (E[0052] 4.5) is an alternate indicator of modulus. It is particularly useful in that the sum E4.5+FS is a good indicator of dimensional stability for yarns processed under different relaxation levels. Lower sums (E4.5+FS) indicate better dimensional stability.
  • The Kinetic Theory of Rubber Elasticity allows computation of an effective number of crosslinks in a yarn. These crosslink values are imagined to be a measure of the ability of the crystals to tie together the amorphous regions, either via tie chains or crystal proximity. The relationship of interest is: [0053]
  • σ=NkT(A 2−1/A)
  • where, [0054]
  • σ=shrinkage force [0055]
  • k=Boltzman constant [0056]
  • T=temperature [0057]
  • A=extension ratio=1/(1-shrinkage) [0058]
  • N=network chains or crosslinks/cc [0059]
  • The classical method for determining crosslink density is to measure shrinkage force and shrinkage for samples which have been drawn (or relaxed) to different extents. For simplicity, we have developed a method which allows one to determine analogous data by measuring the shrinkage at a variety of constraining forces. For this modified technique, the constraining force corresponds to the shrinkage force. The shrinkage value needed for the effective crosslink calculation is the difference between the shrinkage measured at a given constraining force and the shrinkage measured at a minimal constraining force of 5 grams. Note that since curvature is exhibited at high shrinkage forces only data up to a shrinkage force of 0.08 g/d should be used for the above computation. For industrial applications, a temperature of 177° C. was employed. [0060]
  • Identified hereafter is a description of a process which has been found to be capable of forming the improved yarn of the present invention. The yarn product claimed hereafter is not to be limited by the parameters of the process which follows. [0061]
  • The melt-spinnable polyester is supplied to an extrusion spinnerette at a temperature above its melting point and below the temperature at which the polymer degrades substantially. The residence time at this stage is kept to a minimum and the temperature should not rise above 315° C., preferably 310° C. The flow curve of molten PET in terms of melt viscosity versus shear rate has been shown to be important for steady-state melt spinning giving uniform individual multifilaments. For a circular spinnerette hole where flow is steady and end-effects are negligible, the apparent shear rate [0062]
    Figure US20020187344A1-20021212-P00900
    at the wall of the capillary is given by γ . = 4 Q Π R 3
    Figure US20020187344A1-20021212-M00004
  • where [0063]
  • Q=flow rate through the capillary in m[0064] 3/sec (calculate using melt density of 1.30 g/cc)
  • R=radius of the capillary in meters. [0065]
  • The extruded filaments then traverse a conventional yarn solidification zone where quench air impinges on the spun yarn thereby freezing in desirable internal structural features and preventing the filaments from fusing to one another. The solidification zone comprises (a) a retarded cooling zone, preferably comprising a gaseous atmosphere heated at a temperature of 150 to 450° C., and (b) a cooling zone adjacent said retarded cooling zone wherein said yarn is rapidly cooled and solidified in a blown air atmosphere. The key to the current process is to utilize extruding polymer with IV greater than 0.80 and adjust processing conditions to achieve a crystalline, partially oriented yarn with a crystallinity of 3 to 15 percent and a melting point elevation of 2 to 10° C. One skilled in the art can achieve this by adjusting the following conditions: length and temperature of an annealing zone adjacent to the spinnerette, diameter of the spinnerette holes, method of blowing the quench, quench air velocity, and drawdown in the quench column. The speed of withdrawal of the yarn from the solidification zone is an important parameter affecting the stress on the spun fiber, and should be adjusted to yield the desired characteristics. It is preferred that the melting point elevation be 2 to 5° C. and that φ½ is at least 26°. [0066]
  • The spun yarn was then drawn between rolls at temperatures above the glass transition temperature (80° C.) to within 85 percent of the maximum draw ratio. This drawing process involves multiple drawing and conditioning steps to achieve a tenacity above 7 grams per denier, a LASE-5 above 3.7 grams per denier and a shrinkage less than 8 percent. It is preferred that the effective crosslink density (N) be between 10×10[0067] 21 and 20×1021 crosslinks per cubic centimeter.
  • It will be appreciated by those of skill in the art that the high viscosity polymer spun as above can be drawn in known ways such as that disclosed in U.S. Pat. No. 4,195,052 to Davis et al. and in U.S. Pat. No. 4,251,481 to Hamlyn. The yarn can be drawn off-line. However, for economic reasons it is preferred to draw the yarn in a continuous integrated spin-draw process. [0068]
  • The drawn yarns are usually twisted into a cord and then dipped into one or more conventional adhesive coatings, referred to as cord dips and then subjected to various stretch/relax sequences at elevated temperature to 5 achieve the optimum combination of tenacity, shrinkage, LASE-5. Again this technology is well-known to those skilled in the art who adjust twist and treating conditions for specific end-uses. Details for the treating conditions employed are given in the examples. [0069]
  • In evaluating the potential of tire yarns as treated cords, one may use a “standard” twist and cord treatment for comparative purposes. In this “standard” procedure, 1000 denier yarns are twisted to 8 turns per inch and then three ply cords are prepared again using 8 turns per inch. The cords are then dipped in an aqueous blocked diisocyanate (6% solids) just prior to passage through a hot air oven at 440° F. for 40 seconds where the cord was stretched 6% or 8%. The emerging cord then passes through an RFL dip (20% solids) and finally through a second oven at 440° F. for 60 seconds where the cord was relaxed to varying degrees to cover the range where 4% free shrinkage is achieved. For less dimensionally stable cord controls, some extrapolation to 4% shrinkage may be necessary. The cord is wound on a bobbin for further testing. A single-end Litzler Computreater was used. [0070]
  • Treated cords prepared in such manner from the yarn of this invention have been shown to have the following treated cord properties: [0071]
  • (a) a dimensional stability defined by LASE-5 of at least 2.3 grams per denier at 4 percent free shrinkage, and [0072]
  • (b) a tenacity of at least 7.0 grams per denier at 4 percent free shrinkage (preferred at least 7.4 grams per denier), said dimensional stability and said tenacity being determined by interpolation of LASE-5 versus free shrinkage data to 4 percent free shrinkage. [0073]
  • Graphs of LASE-5 and tenacity versus free shrinkage were constructed as shown in FIGS. [0074] 1-4. Comparison between different starting yarns can be made at the interpolated values at 4% free shrinkage.
  • EXAMPLE I
  • A 1000 denier PET yarn was produced by extruding 300 individual filaments at 62.5 lbs/hr into a heated sleeve (220-300° C. Temp) and then solidifying in an air quenching column. Yarns were then taken-up at varying winder speeds. The residence times in the heated sleeve and quench columns were 0.02 to 0.03 and 0.2 seconds, respectively. The Godet speed at the bottom of the spinning column and the winder speed were adjusted to give different undrawn birefringences and crystallinity levels. In all cases the same shear rate in the spinnerette holes was employed. Yarn intrinsic viscosity was 0.88. [0075]
  • These undrawn yarns were then drawn in three stages on a draw-winder. The first three godet rolls had temperatures of 120, 120, and 230° C., the last godet was ambient. The residence times were 0.7, 0.6-0.7, 0.3-0.6, and, 0.2-0.4 seconds. Yarn draw ratios and specific properties are given in Tables I and II. [0076]
  • The above drawn yarns were then twisted into 1000/3, 8.5×8.5 tpi cords and two-zone treated at 440° F. (227° C.) and 440° F. (227° C.) for 40 and 60 seconds. Aqueous blocked diisocyanate and RFL dips were applied prior to the two hot zones, respectively. The treated cords were prepared using +6% stretch in the first zone and various relaxations (−4, −2, and 0%) in the second zone. A stretching sequence of +8, 0% was also used. The properties of these cords are given in Table III. Treated cord dimensional stabilities, as judged by plots of LASE-5 versus free shrink (FIG. 1), increase with increasing undrawn yarn birefringence, melting point, and crystallinity. [0077]
  • Comparison of the treated cord tenacities at a given free shrinkage (FIG. 2) clearly indicates an unexpected high tenacity for the undrawn intermediate birefringence of 0.056. This higher treated cord tenacity is equal to that for standard tire yarn processed at very low undrawn birefringence. While drawn yarn tenacitites alone are not necessarily a good barometer for treated cord tenacity, the combination of yarn tenacity and dimensional stability (E[0078] 4.5+FS) does give a good indication, provided similar thermal histories are experienced during drawing. For the samples representing this invention (I-BD and I-CD), E4.5+FS is 10.2% and 10.1% respectively, indicating highly dimensionally stable yarns. These sums would have been slightly higher (2-3%) if the yarn 10 was drawn at higher speeds where residence times on heated rolls were lower. Note the melting points (258° C. and 259° C.) lies betwen that for comparative examples I-AD and I-DD. Note that the spinning speed required to achieve the 0.056 undrawn birefringence is less than that for the prior art in FIG. 8. The yarns of this invention, I-BD and -CD, have high measured values of Z. Their cord dimensional stabilities are similar as are their calculated Z* values, which take differences in crystallinities into account.
  • EXAMPLE II
  • A higher viscosity yarn (IV=0.92) was spun under similar conditions as in Example I except that several spinnerette shear rates were used. Following the same procedure as in Example I, the winder speed was adjusted to provide different undrawn crystallinities. This undrawn yarn was continuously transported to the panel draw rolls. Details for the undrawn and drawn yarns are given in Tables IV and V. The residence times on the draw rolls was 0.05 to 0.1 second and the godet temperatures were 90° C., ambient, 220° C., and 150° C. For comparison, values for a conventional yarn spun to 0.002 undrawn birefringence are also given. From FIG. 7 it is readily seen that the products of this invention (II-B and II-C) are prepared in the transition region where significant crystallinity 30 occurs in the spinline. The effective number of crosslinks in Table V is calculated from the shrinkage versus shrink force curves in FIG. 10. [0079]
  • The preceeding drawn yarns were twisted into a 1000/3, 8×8 tpi cord and then treated per Example I. Again 35 treated cord dimensional stability (Table VI and FIG. 3) increased with undrawn crystallinity. However as shown in FIG. 4, the highest tenacity was achieved at intermediate LASE-5. The corresponding drawn yarns have tenacity greater than 7.3 g/d, E[0080] 4.5+FS less than 12.9%, intermediate melting points(259 and 262° C.), low amorphous orientation, and a melting trace intensity parameter (Z*) of at least 1.3. The actual DSC traces are given in FIG. 9. when slight differences in twist are taken into account, the dimensional stability of II-BD is similar to I-BD and -CD. The measured Z is much lower than those for Example I, which have higher crystallinity due to lower viscosity and slower drawing stages. Due to the high drawing speeds and modest roll temperatures, none of the samples in this example received an effective heat treatment. The maximum crystallinity without heat treatment is 27-28% with 27.2% representing the average.
  • LASE-5 versus free shrink can be used as an alternate measure of drawn yarn dimensional stability. FIG. 5 gives such a plot for drawn yarns prepared similar to II-AD and II-ED, but then relaxed to various degrees in the final zone. The solid lines in FIG. 5 represent the data for the relaxation series where (×) and (∘) represent points for yarns similar to II-AD and II-ED, respectively. The individual data points from Table IV are also plotted as encircled sample designations from Table IV. One would expect a family of linear lines with increasing slope. On this basis, the products of this invention would be defined by [0081]
  • LASE-5(g/d)>0.35 [Free Shrink (%)]+1.0.
  • The advantages of this patent are more clearly shown by FIG. 6 which plots tenacity versus LASE-5 at a given free shrinkage (4%). Based on the decrease in tenacity in-going from conventional yarn (undrawn ΔN=0.002) to prior art DSP's (undrawn ΔN=0.026), one would expect the continual decrease in treated cord tenacity with increasing LASE-5, particularly in light of the low tenacity at very high undrawn ΔN(=0.082). Instead one sees an unexpected maximum at intermediate LASE-5. Again note that the spinning speeds required are much less than those taught in U.S. Pat. No. 4,491,657. This lower speed allows preparation of fibers in a continuous spin-draw process without the need for expensive high speed equipment. [0082]
  • EXAMPLE III
  • This example shows that yarn tenacity and dimensional stability Ore not sufficient criteria to define the product of this invention. Yarns spun to 0.002 and 0.026 undrawn birefringences were then drawn in the manner described in Example II. They were then given heat treatments of either (a) 6 seconds@245° C. or (b) several hours@210° C. at constant length. Subsequently, the yarn was corded (1000/3, 8.5×8.5) and treated per Example I. The data in Table VII shows that additional parameters of melting point elevations and amorphous orientations are necessary to specify yarns of this invention. The lower amorphous orientation yarns of this invention are expected to have longer flex-life. [0083]
  • EXAMPLE IV
  • This example shows that one must focus on fundamental properties such as undrawn yarn crystallinity and melting point elevation and not on undrawn birefringence alone. A yarn series was processed under similar conditions to Example I, only the thruput was 75 lbs/hr, the heated sleeve was 400° C., and the spinnerette shear rate was 766 sec[0084] −1. At 0.058 undrawn birefringence, the drawn yarn tenacity/UE/LASE-5/FS/E4.5+FS was 8.1/9.9/4.1/8.6/14.8. At 0.081 undrawn birefringence, the drawn yarn was 8.0/9.5/4.1/7.5/11.9. The two drawn yarns had melting point elevations of 8 and 13° C., respectively. Under the standard treating conditions, the tenacity and LASE-5 values at 4% FS were 6.7 g/d and 2.2 g/d for the 0.058 undrawn birefringence compared to 7.1 g/d and 2.6 g/d for the 0.081 undrawn birefringence yarn. Only the latter product was within the scope of this invention even though the undrawn birefringence for the former was similar to that for I-BD and I-CD, which are within the scope of this invention.
    TABLE I
    UNDRAWN YARN (IV = 0.88)
    Ex- Spinning Spinnerette
    am- Speed Shear Rate, M.P., Δ Density, XTAL,
    ple m/min Sec−1 ΔN ° C. M.P. g/cm3 %
    I-A 1760 2150 0.028 250  1 1.3385  2
    I-B, 2900 2150 0.056 252  3 1.3480  4
    I-C
    I-D 3500 2150 0.088 261 12 1.3701 18
  • [0085]
    TABLE IV
    UNDRAWN YARN (IV = 0.92)
    Spinning Spinnerette
    Speed Shear Rate, M.P., Density, XTAL, φ1/2
    Example m/min Sec−1 ΔN ° C. Δm.p. g/cm3 % (deg)
    II-A 1760 2150 0.026 249  0 1.3430  3 21
    II-B 2020  910 0.055 252  3 1.3494  7 32
    II-C 2420  980 0.069 253  4 1.3603 13
    II-D 2990  640 0.082 265 16 1.3707 18 19
    II-E  480 1440 0.002 249  0 1.3385  2
  • [0086]
    TABLE II
    DRAWN YARN (IV = 0.88)
    Ter-
    Te- minal
    Draw Ratio nacity LASE-5 E4.5 Mod. UE, FS (%), E4.5, + M.P., XTAL
    Examplea 1 2 3 Denier g/d g/d % g/d % @ 177° C. FS, % ° C. ΔM.P.b Fa Z Z* %
    I-AD 1.72 1.38 1.03 1016 7.8 4.1 5.2 128 9.8 9.0 14.2 257  8 0.73 0.4 0.3 29.3
    I-BD 1.72 1.10 1.04  898 7.8 5.4 4.1 111 7.2 6.1 10.2 258  9 0.71 2.5 1.5 30.2
    I-CD 1.72 1.10 0.98  943 7.0 4.0 4.6  54 8.9 5.5 10.1 259 10 0.70 1.7 1.4 29.2
    I-DD 1.40 1.10 1.05  799 6.5 5.8 3.2  78 6.2 4.7 7.9 267 18 0.68 0.6 0.2 31.4
  • [0087]
    TABLE III
    TREATED CORD PROPERTIES (IV = 0.88)
    FS (%) Tough-
    Tenacity, LASE-5, at UE, ness,
    Examplea Stretch g/d g/d 177° C. % g/d
    I-AT + 6/−4 6.0 2.48 4.8 11.7 0.34
    +6/−2 6.0 2.62 5.4 11.5 0.34
    +6/−0 6.0 3.01 6.7 10.1 0.30
    +8/−0 6.0 2.95 7.0  9.7 0.29
    I-BT + 6/−4 6.6 2.70 4.2 13.6 0.50
    +6/−2 6.7 3.34 6.3 11.6 0.44
    +6/−0 6.7 3.46 6.7 10.6 0.38
    +8/−0 7.0 3.50 6.8 11.0 0.42
    I-CT + 6/−4 6.3 2.20 2.6 16.1 0.59
    +6/−2 6.3 2.64 3.7 14.4 0.53
    +6/−0 6.5 2.99 4.6 13.3 0.50
    +8/−0 6.4 3.08 4.8 13.3 0.51
    I-DT + 6/−4 5.8 3.77 3.3 10.2 0.36
    +6/−2 5.6 3.58 3.2 11.2 0.39
    +6/−0 5.6 3.87 3.9 10.9 0.39
    +8/−0 6.0 4.00 4.1  9.1 0.31
  • [0088]
    TABLE V
    DRAWN YARN (IV = 0.92)
    Ter-
    minal Free
    Te- Lase- Mod- Shrink,
    Draw Ratio nacity 5 ulus E4.5, EU, @ E4.5, + M.P., Δ XTAL
    Examplea 1 2 3 Denier g/d g/d g/d % % 177° C. FS, % ° C. M.P.b Z Z* Fa % Nc
    II-AD 1.73 1.46 0.98 1008 8.1 3.9  95 5.5 10.0 10.0 15.5 256  7 0.7 0.7 0.70 27.5 8.4
    II-BD 1.73 1.25 0.99 1007 8.1 4.0 128 5.5 9.9 7.4 12.9 258 10 1.5 1.5 0.66 26.6 11.6
    II-CD 1.73 1.16 1.00  982 7.3 3.9 5.7 10.0 5.8 11.5 259 10 1.3 1.3 0.64 27.6
    II-DD 1.40 1.15 1.00  924 5.8 4.1  78 6.5 16.5 4.3 10.8 269 20 0.3 0.3 0.58 28.7 26.6
    II-ED 1005 9.3 3.1 6.9 15.3 10.8 17.7 255  6 <0.1 0.87
  • [0089]
    TABLE VI
    TREATED CORD PROPERTIES (IV = 0.92)
    Fs (%) Tough-
    Tenacity, LASE-5, at UE, ness,
    Example Stretch g/d g/d 177° C. % g/d
    II-AT +1/−0 6.7 2.43 4.9 15.0 0.50
    +6/−4 6.9 2.50 5.1 13.7 0.47
    +6/−2 7.0 2.80 6.9 11.5 0.40
    +6/−0 7.3 3.08 7.5 11.1 0.41
    +8/−0 7.3 3.24 7.8 11.0 0.40
    II-BT +1/−0 7.1 2.41 3.2 16.4 0.62
    +6/−4 7.2 2.55 3.2 16.1 0.61
    +6/−2 7.6 3.20 4.7 14.9 0.60
    +6/−0 7.7 3.39 5.9 13.3 0.56
    +8/−0 7.7 3.37 6.3 12.6 0.53
    II-CT +1/−0 6.6 2.40 2.9 16.3 0.61
    +6/−4 6.8 2.73 2.9 16.1 0.62
    +6/−2 7.0 3.16 5.0 13.9 0.57
    +6/−0 7.1 3.24 5.4 13.0 0.50
    +8/−0 7.1 3.36 5.8 12.6 0.50
    II-DT +1/−0 4.9 2.50 1.8 18.9 0.66
    +6/−4 5.2 2.56 1.9 18.5 0.64
    +6/−2 5.3 3.14 3.2 16.9 0.64
    +6/−0 5.4 3.53 3.9 15.2 0.59
    +8/−0 5.6 3.60 4.0 14.1 0.53
    II-ET +1/−2 7.3 2.4 7.3 16.9 0.64
    +6/−4 7.0 2.2 6.8 17.5 0.62
    +6/−2 7.4 2.9 8.9 14.8 0.59
    +6/−0 7.4 3.3 10.2 13.2 0.54
  • [0090]
    TABLE VII
    Yarn Treated Cord
    Undrawn Yarn Heat Tenacity, E4.5 + M.P., Tenacity, g/d LASE-5, g/d
    Birefringence Treatment g/d FS, % ° C. Fa @ 4% FS @ 4% FS
    0.002 None 8.9 16.8 255 0.87 6.9 1.2
    6 sec @ 245° C. 8.9 11.0 0.83
    8 hr @ 210° C. 7.5 7.2 0.90 6.0 2.5
    0.026 None 8.0 13.8 256 0.70 6.6 2.5
    6 sec @ 245° C. 7.9 8.0 256 0.63 6.6 2.5
    2 hr @ 210° C. 8.0 7.0 254 0.67 6.3 2.8
    0.056 None 8.1 12.5 258 0.66 6.9 2.8

Claims (21)

What is claimed is:
1. A process for production of a drawn polyethylene terephthalate yarn which translates to a high tenacity dimensionally stable tire cord, comprising:
(A) extruding a molten melt-spinnable polyethylene terephthalate having an intrinsic viscosity of 0.8 of greater through a shaped extrusion orifice having a plurality of openings to form a molten spun yarn,
(B) solidifying the spun yarn gradually by passing the yarn through a solidification zone which comprises (a) a retarded cooling zone and (b) a cooling zone adjacent said retarded cooling zone wherein said yarn is rapidly cooled and solidified in a blown air atmosphere,
(C) withdrawing the solidified yarn at sufficient speed to form a crystalline, partially oriented yarn with a crystallinity of 3 to 15% and a melting point elevation of 2 to 10° C., and
(D) hot drawing the yarn to a total draw ratio between 1.5/1 and 2.5/1.
2. The process of claim 1 wherein the melting point elevation is 2 to 5° C.
3. The process of claim 1 wherein φ½ is at least 26°.
4. The process of claim 1 wherein the steps A, B, C, and D are performed in a continuous integrated spin-draw process.
5. The process of claim 4 wherein the melting point elevation is 2 to 5° C.
6. The process of claim 4 wherein φ½ is at least 26°.
7. A drawn polyethylene terephthalate multifilament yarn having the following combination of properties:
(A) a terminal modulus of at least 20 g/d,
(B) a dimensional stability defined by E4.5+FS<13.5%,
(C) a tenacity of at least 7 grams/denier,
(D) a melting point elevation of 9 to 14° C., and
(E) an amorphous orientation function of less than 0.75.
8. The drawn yarn of claim 7 wherein the melting point elevation is 9-11° C.
9. The drawn yarn of claim 7 which has the melting point characteristic defined by Z* greater than or equal to 1.3.
10. Dimensionally stable yarns of claim 7 which have the melting characteristic defined by Z greater than or equal to 1.7.
11. The drawn yarn of claim 7 which has an effective crosslink density (N) between 10×1021 and 20×1021 crosslinks per cubic centimeter.
12. A high tenacity, dimensionally stable treated tire cord prepared from the yarn of claim 7.
13. A rubber article incorporating as reinforcing material the high tenacity, dimensionally stable cord of claim 12.
14. A composite incorporating as reinforcing material the drawn yarn of claim 7.
15. A drawn polyethylene terephthalate yarn which, when twisted into an 8×8 twists per inch 1000 denier 3-end greige cord and tensilized by the sequence of dipping into a first blocked diisocyanate dipping solution, stretching at 440° F. (227° C.) for 40 seconds, dipping into a second resourcinol-formaldehyde-latex dipping solution, and relaxing at 440° F. (227° C.) for 60 seconds, provides the following treated cord property combinations:
(a) a dimensional stability defined by LASE-5 of at least 2.3 grams per denier at 4 percent free shrinkage, and
(b) a tenacity of at least 7.0 grams per denier at 4 percent free shrinkage, said dimensional stability and said tenacity being determined by interpolation of LASE-5 versus free shrinkage data to 4 percent free shrinkage.
16. The yarn of claim 15 which provides a treated cord tenacity of at least 7.4 grams per denier.
17. A process for the production of a drawn polyethylene terephthalate yarn which translates to a high tenacity dimensionally stable tire cord comprising:
(a) extruding a molten melt-spinnable polyethylene terephthalate having an intrinsic viscosity of at least about 0.8 through a shaped extrusion orifice having a plurality of openings to form a molten spun yarn;
(b) solidifying gradually said molten spun yarn by passing said molten spun yarn through a solidification zone which comprises (i) a retarded cooling zone and (ii) a cooling zone adjacent said retarded cooling zone where in said cooling zone, said yarn is rapidly cooled and solidified in a gaseous atmosphere;
(c) withdrawing at sufficient speed said solidified yarn from said solidification zone to form a crystalline partially oriented yarn; and
(d) hot drawing said crystalline partially oriented yarn at a total draw ratio between about 1.5/1 and about 2.5/1 to produce a drawn yarn having an effective crosslink density (N) between about 10×1021 and about 20×1021 crosslinks per cubic centimeter.
18. The process of claim 17 wherein in said step (d), a draw point localizing jet is used.
19. The process of claim 17 wherein in said step (b), said retarded cooling zone comprises a gaseous atmosphere heated at a temperature of 150° C. to 450° C.
20. The process of claim 1 7 wherein in said step (b), said retarded cooling zone comprises a heated sleeve.
21. The process of claim 20 wherein said heated sleeve is at a temperature of 220° C. to 300° C.
US10/140,841 1988-07-05 2002-05-07 Dimensionally stable polyester yarn for high tenacity treated cords Abandoned US20020187344A1 (en)

Priority Applications (3)

Application Number Priority Date Filing Date Title
US10/140,841 US20020187344A1 (en) 1994-02-22 2002-05-07 Dimensionally stable polyester yarn for high tenacity treated cords
US10/440,642 US6828021B2 (en) 1988-07-05 2003-05-19 Dimensionally stable polyester yarn for high tenacity treated cords
US10/980,546 US7108818B2 (en) 1988-07-05 2004-11-03 Dimensionally stable polyester yarn for high tenacity treated cords

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
US20085394A 1994-02-22 1994-02-22
US08/527,292 US5646334A (en) 1995-09-12 1995-09-12 Multisample dynamic headspace sampler
US84474497A 1997-04-21 1997-04-21
US09/571,843 US6403006B1 (en) 1988-07-05 2000-05-16 Process of making dimensionally stable polyester yarn for high tenacity treated cords
US10/140,841 US20020187344A1 (en) 1994-02-22 2002-05-07 Dimensionally stable polyester yarn for high tenacity treated cords

Related Parent Applications (1)

Application Number Title Priority Date Filing Date
US09/571,843 Continuation US6403006B1 (en) 1988-07-05 2000-05-16 Process of making dimensionally stable polyester yarn for high tenacity treated cords

Related Child Applications (1)

Application Number Title Priority Date Filing Date
US10/440,642 Continuation US6828021B2 (en) 1988-07-05 2003-05-19 Dimensionally stable polyester yarn for high tenacity treated cords

Publications (1)

Publication Number Publication Date
US20020187344A1 true US20020187344A1 (en) 2002-12-12

Family

ID=27498406

Family Applications (1)

Application Number Title Priority Date Filing Date
US10/140,841 Abandoned US20020187344A1 (en) 1988-07-05 2002-05-07 Dimensionally stable polyester yarn for high tenacity treated cords

Country Status (1)

Country Link
US (1) US20020187344A1 (en)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20050074607A1 (en) * 2003-10-06 2005-04-07 Rim Peter B. Dimensionally stable yarns
US20110024016A1 (en) * 2008-03-31 2011-02-03 Kolon Industries Inc. Undrawn polyethylene terephthalate (pet) fiber, drawn pet fiber, and tire-cord comprising the same
KR101231096B1 (en) * 2008-07-22 2013-02-07 코오롱인더스트리 주식회사 Drawn poly(ethyleneterephthalate) fiber, tire-cord and tire comprising the same

Citations (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3690362A (en) * 1970-09-28 1972-09-12 Allied Chem High strength polyethylene terephthalate yarn and cord produced therefrom
US4101525A (en) * 1976-10-26 1978-07-18 Celanese Corporation Polyester yarn of high strength possessing an unusually stable internal structure
US4195052A (en) * 1976-10-26 1980-03-25 Celanese Corporation Production of improved polyester filaments of high strength possessing an unusually stable internal structure
US4251481A (en) * 1979-05-24 1981-02-17 Allied Chemical Corporation Continuous spin-draw polyester process
US4414169A (en) * 1979-02-26 1983-11-08 Fiber Industries, Inc. Production of polyester filaments of high strength possessing an unusually stable internal structure employing improved processing conditions
US4491657A (en) * 1981-03-13 1985-01-01 Toray Industries, Inc. Polyester multifilament yarn and process for producing thereof
US4690866A (en) * 1984-07-09 1987-09-01 Teijin Limited Polyester fiber
US4827999A (en) * 1981-12-02 1989-05-09 Toyobo Petcord Co., Ltd. Polyester fiber having excellent thermal dimensional _ stability, chemical stability and high _ tenacity and process for the production thereof
US4867936A (en) * 1987-06-03 1989-09-19 Allied-Signal Inc. Process for producing high strength polyester yarn for improved fatigue resistance
US4975326A (en) * 1987-06-03 1990-12-04 Allied-Signal Inc. High strength polyester yarn for improved fatigue resistance
US5067538A (en) * 1988-10-28 1991-11-26 Allied-Signal Inc. Dimensionally stable polyester yarn for highly dimensionally stable treated cords and composite materials such as tires made therefrom
US5132067A (en) * 1988-10-28 1992-07-21 Allied-Signal Inc. Process for production of dimensionally stable polyester yarn for highly dimensionally stable treated cords
US5350632A (en) * 1985-06-19 1994-09-27 Rhone-Poulenc Viscosuisse S.A. Impregnated, dimension-stable polyester cord

Patent Citations (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3690362A (en) * 1970-09-28 1972-09-12 Allied Chem High strength polyethylene terephthalate yarn and cord produced therefrom
US4101525A (en) * 1976-10-26 1978-07-18 Celanese Corporation Polyester yarn of high strength possessing an unusually stable internal structure
US4195052A (en) * 1976-10-26 1980-03-25 Celanese Corporation Production of improved polyester filaments of high strength possessing an unusually stable internal structure
US4414169A (en) * 1979-02-26 1983-11-08 Fiber Industries, Inc. Production of polyester filaments of high strength possessing an unusually stable internal structure employing improved processing conditions
US4251481A (en) * 1979-05-24 1981-02-17 Allied Chemical Corporation Continuous spin-draw polyester process
US4491657A (en) * 1981-03-13 1985-01-01 Toray Industries, Inc. Polyester multifilament yarn and process for producing thereof
US4827999A (en) * 1981-12-02 1989-05-09 Toyobo Petcord Co., Ltd. Polyester fiber having excellent thermal dimensional _ stability, chemical stability and high _ tenacity and process for the production thereof
US4690866A (en) * 1984-07-09 1987-09-01 Teijin Limited Polyester fiber
US5350632A (en) * 1985-06-19 1994-09-27 Rhone-Poulenc Viscosuisse S.A. Impregnated, dimension-stable polyester cord
US4867936A (en) * 1987-06-03 1989-09-19 Allied-Signal Inc. Process for producing high strength polyester yarn for improved fatigue resistance
US4975326A (en) * 1987-06-03 1990-12-04 Allied-Signal Inc. High strength polyester yarn for improved fatigue resistance
US5067538A (en) * 1988-10-28 1991-11-26 Allied-Signal Inc. Dimensionally stable polyester yarn for highly dimensionally stable treated cords and composite materials such as tires made therefrom
US5132067A (en) * 1988-10-28 1992-07-21 Allied-Signal Inc. Process for production of dimensionally stable polyester yarn for highly dimensionally stable treated cords

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20050074607A1 (en) * 2003-10-06 2005-04-07 Rim Peter B. Dimensionally stable yarns
WO2005040463A1 (en) * 2003-10-06 2005-05-06 Performance Fibers, Inc. Dimensionally stable yarns
US6902803B2 (en) 2003-10-06 2005-06-07 Performance Fibers, Inc. Dimensionally stable yarns
US20110024016A1 (en) * 2008-03-31 2011-02-03 Kolon Industries Inc. Undrawn polyethylene terephthalate (pet) fiber, drawn pet fiber, and tire-cord comprising the same
US9005754B2 (en) 2008-03-31 2015-04-14 Kolon Industries, Inc. Undrawn polyethylene terephthalate (PET) fiber, drawn PET fiber, and tire-cord comprising the same
KR101231096B1 (en) * 2008-07-22 2013-02-07 코오롱인더스트리 주식회사 Drawn poly(ethyleneterephthalate) fiber, tire-cord and tire comprising the same

Similar Documents

Publication Publication Date Title
US6403006B1 (en) Process of making dimensionally stable polyester yarn for high tenacity treated cords
US5234764A (en) Dimensionally stable polyester yarn for high tenacity treaty cords
US5067538A (en) Dimensionally stable polyester yarn for highly dimensionally stable treated cords and composite materials such as tires made therefrom
US4414169A (en) Production of polyester filaments of high strength possessing an unusually stable internal structure employing improved processing conditions
US4101525A (en) Polyester yarn of high strength possessing an unusually stable internal structure
US4195052A (en) Production of improved polyester filaments of high strength possessing an unusually stable internal structure
US3963678A (en) Large denier polyethylene terephthalate monofilaments having good transverse properties
US6828021B2 (en) Dimensionally stable polyester yarn for high tenacity treated cords
EP0450607B1 (en) Polyester fiber and method of manufacturing same
US5132067A (en) Process for production of dimensionally stable polyester yarn for highly dimensionally stable treated cords
JPH06511293A (en) High modulus polyester yarn for tire cord and composites
US20020187344A1 (en) Dimensionally stable polyester yarn for high tenacity treated cords
AU637546B2 (en) Dimensionally stable polyester yarn for high tenacity treated cords
EP0452405B1 (en) Process for dimensionally stable polyester yarn
EP0295147B1 (en) High strength polyester yarn
KR100429949B1 (en) Manufacturing Method of Polyethylene Terephthalate Fiber for Dip Cord and PET Fiber Manufactured by the Same

Legal Events

Date Code Title Description
AS Assignment

Owner name: PERFORMANCE FIBERS, INC., NORTH CAROLINA

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:HONEYWELL INTERNATIONAL, INC., A CORP. OF DELAWARE;REEL/FRAME:016164/0705

Effective date: 20041219

AS Assignment

Owner name: GENERAL ELECTRIC CAPITAL CORPORATION, CALIFORNIA

Free format text: SECURITY INTEREST;ASSIGNORS:PERFORMANCE FIBERS, INC.;PERFORMANCE FIBERS HOLDINGS, INC.;PERFORMANCE FIBERS ENTERPRISES, INC.;REEL/FRAME:016195/0354

Effective date: 20041221

STCB Information on status: application discontinuation

Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION

AS Assignment

Owner name: PERFORMANCE FIBERS ENTERPRISES, INC., VIRGINIA

Free format text: RELEASE BY SECURED PARTY;ASSIGNOR:GENERAL ELECTRIC CAPITAL CORPORATION;REEL/FRAME:020599/0191

Effective date: 20071005

Owner name: PERFORMANCE FIBERS HOLDINGS, INC., VIRGINIA

Free format text: RELEASE BY SECURED PARTY;ASSIGNOR:GENERAL ELECTRIC CAPITAL CORPORATION;REEL/FRAME:020599/0191

Effective date: 20071005

Owner name: PERFORMANCE FIBERS, INC., VIRGINIA

Free format text: RELEASE BY SECURED PARTY;ASSIGNOR:GENERAL ELECTRIC CAPITAL CORPORATION;REEL/FRAME:020599/0191

Effective date: 20071005