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(11) | EP 0 623 179 B2 |
| (12) | NEW EUROPEAN PATENT SPECIFICATION |
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HIGH MODULUS POLYESTER YARN FOR TIRE CORDS AND COMPOSITES POLYESTERGARNE MIT HOHEM MODUL FUER REIFENKORDEN UND VERBUNDMATERIALIEN FIL DE POLYESTER A MODULE ELEVE POUR CABLES DE PNEUS ET COMPOSITES |
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[0001] This invention relates to polyethylene naphthalate (PEN) multifilament yarn and other yarns made from similarly rigid monomer combinations with extremely high modulus, good tenacity, and low shrinkage particularly useful for the textile reinforcement of tires. The PEN yarn of this invention provides enhanced modulus and dimensional stability when compared to conventionally processed PEN yarns. A process for production of the multi-filament PEN yarn is an aspect of this invention.
[0002] Currently, polyethylene terephthalate (PET) filaments are commonly used in industrial applications including radial tire bodies, conveyor belts, seat belts, V belts and hosing. However, higher modulus and dimensional stability is preferred in more demanding applications such as bodied of monoply high performance tires and is required in the belts of radial passenger tires. Dimensional stability is defined as the sum of the elongation at 4.5 g/d (39.7 mN/dtex) and shrinkage. US-A-3 616 832 provides rubber articles reinforced with PEN of good dimensional stability and tenacity and US-A-3 929 180 provides a tire with PEN used as a carcass reinforcement. However, these patents are concerned with conventionally processed PEN of low undrawn birefringence and hence do not achieve the full property potential of this material as is the object of this invention. The same is true of GB-A-1 445 464 which teaches optimized drawing of conventionally spun PEN. US-A-4 000 239 provides a process for producing a high melting point, heat resistant undrawn PEN for electrically insulating fabrics. Since these materials were prepared under high stress conditions favoring high crystallinity or at least highly nucleated structure, they lack drawability and cannot attain high modulus for the applications contemplated herein. A product for the same application is provided in US-A-4 001 479, which is concerned with partially oriented yarns of high elongation and low tenacity.
[0003] The process of the invention is defined in claim 1. The drawn yarn of the invention is defined in claim 6. The yarns of this invention are prepared by spinning PEN or other semi-crystalline polyester polymers made from similarly rigid monomer combinations to a state of optimum amorphous orientation and crystallinity. The invention is accomplished by selection of process parameters to form an undrawn polyester yarn of birefringence at least 0.030. The spun yarn is then hot drawn to a total draw ratio of between 1.5/1 and 6.0/1 with the resulting drawn semicrystalline polyester yarn having Tg greater than 100°C and a melting point elevation at least 9°C. The preferred yarn has a tenacity at least 6.5 g/d (57.4 mN/dtex), dimensional stability (EASL + Shrinkage) of less than 5%, and shrinkage 4% or less.
[0004] The resulting yarn exhibits surprisingly high modulus and tenacity together with low shrinkage when compared to prior art yarns.
[0005] The invention also provides a drawn semicrystalline polyester multifilament yarn having Tg greater than 100°C and a melting point elevation of at least 9°C, which is obtained by drawing a polyester yarn having an undrawn birefringence of at least 0.030.
[0006] Fig. 1 represents a comparison of modulus at a tenacity of 6.2 g/d (54.7 mN/dtex) for the PEN yarns of Examples 1 and 2.
[0007] The polyester multifilament yarn of the present invention provides high modulus, high dimensional stability and good tenacity, characteristics which are extremely desirable when this material is incorporated as fibrous reinforcement into rubber composites such as tires. PEN multifilament yarns or other yarns of polyester polymers made from similarly rigid monomer combinations can be used advantageously to reinforce two parts of a radial passenger tire, the carcass and the belt. Currently, passenger tire carcasses are reinforced primarily by polyethylene terephthalate. Two tire characteristics which are controlled by the carcass cord property of dimensional stability (modulus at a given shrinkage) are sidewall indentations and tire handling. The high modulus and dimensional stability of the PEN or other polyester yarns of this invention relative to PET and prior art PEN yarns means that tires with carcasses reinforced with the yarns of this invention will exhibit lower sidewall indentation and better handling behavior. The yarns of this invention are also a desirable reinforcement material because of their high glass transition temperature (Tg) greater than 100°C, i.e. 120°C for PEN, compared to a Tg of 80°C for PET. The high Tg will result in lower cord heat generation over a wider temperature range relative to PET tires, resulting in longer tire lifetimes and overall cooler tire operating temperatures. In addition, since modulus tends to drop precipitously at temperatures above Tg, the yarns of this invention will maintain modulus over a wider temperature range than PET. All of the above mentioned advantages will be of critical importance when yarns of this invention are used to reinforce high performance tires since this application requires low cord heat generation and high modulus, especially at elevated operating temperatures characteristic of high speed performance driving.
[0008] PEN multifilament yarns and other polyester yarns of this invention can also be used to reinforce the belts of radial passenger tires and the carcasses of radial truck tires. Currently steel is used for these applications since PET prossesses insufficient strength and modulus for a given cord diameter. The high modulus of PEN relative to PET, and the additional modulus advantages of the PEN of this invention will make PEN an ideal material to be used as a steel substitute.
[0009] The polyethylene naphthalate yarn of the invention contains at least 90 mol percent polyethylene naphthalate. In a preferred embodiment, the polyester is substantially all polyethylene naphthalate. 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 2,6 naphthylene dicarboxylic acid or their derivatives.
[0010] Illustrative examples of other ester forming ingredients which may be copolymerized with the polyethylene naphthalate units include glycols such as 1,3-propanediol, 1,4-butanediol, 1,6-hexanediol, etc., and dicarboxylic acids such as terephthalic acid, isophthalic acid, hexahydroterephthalic acid, stilbene dicarboxylic acid, bibenzoic acid, adipic acid, sebacic acid, azelaic acid, etc.
[0011] Other polyester yarns of the invention can be prepared to contain polyester polymer made from suitable combinations of rigid and flexible monomers providing the resulting polymer is melt-spinnable, is semi-crystalline, and has a Tg greater than 100°. Examples of rigid monomers include dicarboxylic acids such as 2,6-naphthalene dicarboxylic acid, 2,7-naphthalene dicarboxylic acid, diphenyl dicarboxylic acid, stilbene dicarboxylic acid and terephthalic acid; dihydroxy compounds such as hydroquinone, biphenol, p-xylene glycol, 1,4 cyclohexanedimethanol, neopentylene glycol; and hydroxycarboxylic acid such as P-hydroxybenzoic acid and 7-hydroxy-β-naphthoic acid. Examples of flexible monomers include dicarboxylic acids such as oxalic acid, succinic acid, adipic acid, sebacic acid, and dihydroxy compounds such as ethylene glycol, 1,3 propanediol, 1,4 butanediol, 1,6 hexanediol. It is important that the thermal stability of the polymer above its melting point be sufficient to allow melt processing without excessive degradation.
[0012] The multi-filament 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.
[0013] The multi-filament yarn is particularly suited for use in industrial applications wherein high strength polyester fibers have been utilized in the prior art.
[0014] The fibers are particularly suited for use in environments where elevated temperatures (e.g. 100°C) are encountered. Not only does the filamentary material provide enhanced modulus but it undergoes a very low degree of shrinkage for a high modulus fibrous thermoplastic.
[0015] The unexpected dimensional stability advantage seems to originate from the formation of a unique morphology during spinning which arises from the crystallization of highly oriented amorphous regions characterized by an undrawn birefringence of at least 0.03, preferably 0.03 to 0.30. This crystallization occurs in either the drawing stage or the spinning stage depending on the level of stress imposed during spinning. If too much stress is applied during spinning, the undrawn yarns tend to lack drawability and characteristically exhibit melting points greater than 290°C for PEN. The characterization parameters referred to herein may conveniently be determined by testing the multifilament yarn which consists of substantially parallel filaments.
1. BIREFRINGENCE - Birefringence was determined using a polarizing light microscope equipped with a Berek compensator. If the black primary extinction band is not visible the purple colored band should be used for this measurement.
2. DENSITY - Densities were determined in a n-heptane/carbon tetrachloride density gradient column at 23°C. The gradient column was prepared and calibrated according to ASTM D1505-68.
3. MELTING POINT - Melting points were determined with a Perkin-Elmer Differential
Scanning Calorimeter (DSC) from the maxima of the endotherm resulting from scanning
a 10 mg sample at 20°C per minute. Tg is to be taken under the same experimental conditions
as the inflection point in the change heat capacity associated with the glass transition
temperature. Melting point elevation for drawn yarns (Δ Tm) is defined as:
where Tm1 is the melting point of the drawn yarn of interest and Tm11 is the melting point of a yarn which is pre-melted and rapidly cooled in the DSC
before analysis.
4. INTRINSIC VISCOSITY - 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 (ηr) in a mixture of phenol and tetrachloroethane (60/40 by weight) solvents. ηr is the ratio of the flow time of a PEN/solvent solution to the flow time of pure solvent through a standard capillary. IV is calculated by extrapolation of relative solution viscosity data to a concentration of zero.
5. PHYSICAL PROPERTIES - The tensile properties referred to herein were determined
through the utilization of an Instron tensile tester using a 10 inch (25.4 cm) gauge
length and a strain rate of 120 percent per minute. All tensile measurements were
made at room temperature. Dimensional stability refers to the level of stress achieved
at a given shrinkage. In the tire industry, dimensional stability is defined as the
sum of elongation at a specified bad plus shrinkage. For the present case, the elongation
at a specified load (EASL) is derived from the initial modulus data using the following
equation:
[0016] It is well known that tenacity and modulus increase with increasing draw-ratio. While higher tenacity per se is almost always highly desirable, the high extension ratios are often not achievable due to yarn quality problems or to excessive shrinkage. Materials of this invention possess high levels of modulus for a given level of tenacity. This is quantified as the LT parameter, by ratioing L-5 to tenacity as follows :
L-5 or LASE-5 is a measure of modulus defined as load in g/d at 5% elongation. The materials of this invention have LT at least 25. If L-5 is not measurable because of yarn elongations less than 5% the yarns will be pre-relaxed at elevated temperatures before testing to increase elongation beyond 5%.
[0017] Shrinkage values were determined in accordance with ASTM D885 after one minute at 177°C employing a constraining force of 0.05 g/denier (0.44 mN/dtex).
[0018] 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.
[0019] 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 350°C, preferably 320°C.
[0020] 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 preferably comprises (a) a retarded cooling zone comprising a gaseous atmosphere heated at a temperature to at least 150°C, preferably 150 to 500°C, and (b) a cooling zone adjacent to 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 adjust processing conditions to achieve a highly oriented undrawn yarn of birefringence at least 0.03 and an elevated melting point of 1-25°C, preferably 3-23°C. For PEN a melting point of 265 to 290°C, preferably 268 to 288°C must be achieved. One skilled in the art can achieve this by adjusting the following conditions: length and temperature of the retarded cooling zone adjacent to the spinnerette, diameter of the spinnerette holes, method of blowing the quench, quench air velocity, and drawdown in the solidification zone. 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. The spun yarn is then drawn by conventional means in either a continuous or non-continuous process to yield a drawn yarn with Tg greater than 100°C and a melting point elevation at least 9°C, preferably 9 to 15°C. It is preferred to have the following drawn yarn properties: tenacity at least 6.5 g/d (57.4 mN/dtex), preferably at least 7.5 g/d (66.2 mN/dtex); dimensional stability (EASL + shrinkage) of less than 5%; and shrinkage of 4% or less.
EXAMPLE I - (COMPARATIVE)
[0021] A PEN undrawn yarn was produced by extruding 32 filaments through a spinnerette with orifices of length 0.042 inches (0.107cm) and of width 0.021 inches (0.053 cm) at a thruput of 23.2 cc/min. The filaments were solidified in an air quenching column and taken up at winder speeds of 305 m/min.
[0022] This yarn was drawn in two stages using conventional heated rolls. The undrawn yarn properties, drawn yarn properties, and drawing conditions are summarized in Table I.
[0023] The yarn of this example, which was prepared conventionally from an undrawn yarn of Δ n = 0.004, possesses poorer modulus than the yarns of this invention as evidenced by LT less than 25. Also the dimensional stability parameter (EASL + shrinkage) of 8.3 is higher than that of yarns of this invention, indicating poorer dimensional stability (see Example III).
TABLE I
| A. UNDRAWN YARN | |
| Δ n | 0.004 |
| Tenacity (g/d) | 0.6 (5.3 mN/dtex) |
| Modulus (g/d) | 18.6 (164 mN/dtex) |
| Tm (°C) | 268 |
| B. DRAWN YARN | |
| Draw Ratio | 6.3 |
| Roll 1 (°C) | 140 |
| Roll 2 (°C) | 157 |
| Roll 3 (°C) | RT |
| Δ n | 0.426 |
| Tenacity (g/d) | 6.2 (54.7 mN/dtex) |
| Modulus (g/d) | 176 (1553 mN/dtex) |
| Tm (°C) | 272 |
| Shrinkage (%) | 5.7 |
| EASL + Shrink (%) | 8.3 |
| Δ Tm (°C) | 7 |
EXAMPLE II
[0024] PEN yarns were produced by extruding seven filaments through a spinnerette with orifices of length 0.036 inches (0.091 cm) and width of 0.016 inches (0.041 cm) at a thruput of 9.6 cm3/min. The filaments were solidified in an air quenching column and taken up at winder speeds ranging from 770-5000 m/min. These yarns were drawn in two stages using a heating plate in draw zone two. The undrawn yarn properties, drawn yarn properties, and drawing conditions are summarized in Table II.
[0025] Visual inspection of the data in this example illustrates that for yarns drawn to a given tenacity, modulus increases with increasing spinning speed and with drawn and undrawn melting point. This is reflected in the increasing LT parameter with increasing spinning speed. Undrawn birefringence alone is not sufficient to characterize the yarns of this invention. Since this parameter is insensitive to morphological changes which occur at high spinning stresses, both melting point and birefringence must be used to define the scope of this invention. In order to compare the data of this example with that of comparative Example I, the modulus values of Table II were interpolated to 6.2 g/d (54.7 mN/dtex) tenacity and plotted vs spinning speed (Fig. 1). This analysis clearly shows the advantages of the yarns of this invention relative to prior art yarns.
EXAMPLE III
[0026] The undrawn yarns of Example II spun at 770 m/min and 4000 m/min were drawn to their ultimate limit.
[0027] The 770 m/min sample was drawn in one stage using an oven in the draw zone and the 4000 m/min sample was drawn in two stages using a heated plate in the second draw zone.
[0028] The drawn yarn properties and drawing conditions are summarized in Table III. This example shows that the yarns of this invention possess extremely high modulus, high tenacity, and low shrinkage making them desirable for in-rubber applications.
TABLE Ill
| A DRAWN YARN | ||
| Take-up Speed (m/min) | ||
| 770 | 4000 | |
| Draw Ratio | 5.9 | 2.0 |
| Roll 1 (°C) | 120 | 95 |
| Oven (°C) | 170 | -- |
| Roll 2 (°C) | RT | RT |
| Heating Plate (°C) | -- | 240 |
| Roll 3 (°C) | -- | RT |
| Tenacity (g/d) (mN/dtex) | 10.3 (90.9) | 7.6 (67.1) |
| Modulus (g/d) (mN/dtex) | 362 (3204) | 417 (3680) |
| Shrinkage (%) | 3.5 | <1 |
| EASL + Shrink (%) | 4.8 | <2.1 |
| L-5 (g/d) (mN/dtex) | 8.3 (73.3) | 7.5 (66.2) |
| LT | 28 | 90 |
EXAMPLE IV
[0029] This example shows that undrawn yarns of high birefringence, modulus, and melting point can be produced at spinning speeds slower than those of Example II, thereby yielding a more commercially feasible process for those lacking high speed capabilities. PEN yarns were produced by extruding seven filaments through a spinnerette with orifices of length 0.069 inches and width 0.030 inches at a thruput of 9.6 cc/min. The filaments were solidified in an air quenching column and taken up at winder speeds ranging from 410 m/min to 2500 m/min. The properties of these yarns are summarized in Table IV.
TABLE IV
| TAKE-UP SPEED (M/MIN) | ||||||
| 410 | 770 | 1200 | 1600 | 2000 | 2500 | |
| Δn | 0.178 | 0.154 | 0.192 | 0.232 | 0.233 | 0.226 |
| Tenacity (g/d) | 2.1 | 2.0 | 2.6 | 3.8 | 4.0 | 4.5 |
| (mN/dtex) | (18.5) | (17.7) | (22.9) | (33.5) | (35.3) | (39.7) |
| Modulus (g/d) | 64 | 58 | 63 | 114 | 143 | 158 |
| (mN/dtex) | (565) | (512) | (556) | (1006) | (1262) | (1395) |
| Tm (°C) | 269 | 267 | 268 | 279 | 291* | 292* |
| * not within the process of the invention |
1. A process for production of a drawn polyester yarn of enhanced modulus and good tenacity,
comprising:
(a) extruding a molten crystallizable polyester polymer having Tg greater than 100°C and having an intrinsic viscosity of 0.6 or greater through a shaped extrusion orifice having a plurality of openings to form a molten spun yarn,
(b) solidifying the spun yarn by passing through a solidification zone,
(c) withdrawing the solidified yarn at a sufficient undrawn take-up speed to form a partially oriented yarn of birefringence of 0.030 to 0.30 and melting point elevation of 1-25°C, and
(d) hot drawing the yarn to a total draw ratio of at least 1.5/1 to form a drawn yarn having LT at least 25.
2. The process of Claim 1 wherein the spun yarn is solidified by passing through a solidification
zone which comprises (a) a retarded cooling zone comprising a gaseous atmosphere heated
at a temperature of at least 150°C, and (b) a cooling zone adjacent to said retarded
cooling zone wherein said yarn is rapidly cooled and solidified in a blown air atmosphere.
3. The process of Claim 1 or Claim 2 wherein the undrawn take-up speed is 400 to 4500
m/min.
4. The process of Claims 1 or 2 for production of a drawn polyethylene naphthalate yarn
wherein the molten polyester polymer extruded in step (a) is polyethylene naphthalate.
5. The process of claim 4 wherein the undrawn take-up speed is 400 to 4500 m/min., and
the melting point elevation of the partially oriented yarn is 3-23°C.
6. A drawn semi-crystalline polyester multifilament yarn having Tg greater than 100°C
and a melting point elevation of at least 9°C, which is obtained by drawing a polyester
yarn having an undrawn birefringence of at least 0.030, and which has LT at least 25.
7. The drawn yarn of claim 6 having a tenacity of at least 6.5 g/d (57.4 mN/dtex), a
dimensional stability (EASL + shrinkage) of less than 5%, and a shrinkage of 4% or
less.
8. The drawn yarn of claim 7 which is polyethylene naphthalate.
9. The drawn polyethylene naphthalate yarn of claim 8 wherein the melting point elevation
is 9 to 15°C, the modulus is at least 280 g/d (2470 mN/dtex) and the tenacity is at
least 7.5 g/d (66.2 mN/dtex).
1. Verfahren zur Herstellung eines verstreckten Polyestergarns erhöhten Moduls und guter
Zugfestigkeit, bei dem man
(a) eine Schmelze eines kristallisierbaren Polyesters mit Tg größer 100°C und einer intrinsischen Viskosität von 0,6 und mehr durch eine profilierte Mehrlochausformöffnung unter Bildung eines schmelzflüssigen Spinnfadens extrudiert,
(b) den Spinnfaden durch Passage einer Erstarrungszone zum Erstarren bringt,
(c) den erstarrten Faden mit einer zur Bildung eines teilorientierten Garns einer Doppelbrechung von 0,030 bis 0,30 und einer Schmelzpunkterhöhung von 1-25°C ausreichenden, aber keine Verstreckung bewirkenden Aufnahmegeschwindigkeit abzieht und
(d) das Garn auf ein Gesamtstreckverhältnis von mindestens 1,5:1 zu einem verstreckten Garn mit LT mindestens 25 heißverstreckt.
2. Verfahren nach Anspruch 1, bei dem man den Spinnfaden durch Passage einer Erstarrungszone
zum Erstarren bringt, die (a) eine eine auf eine Temperatur von mindestens 150°C erhitzte
Gasatmosphäre enthaltende Zone verzögerter Kühlung und (b) eine sich daran anschließende
Kühlzone, in der sich der Faden unter Luftanblasung schnell abkühlt und erstarrt,
umfaßt.
3. Verfahren nach Anspruch 1 oder Anspruch 2, bei dem man das unverstreckte Garn mit
einer Geschwindigkeit von 400 bis 4500 m/min aufnimmt.
4. Verfahren nach den Ansprüchen 1 oder 2 zur Herstellung eines verstreckten Polyethylennaphthalatgarns,
bei dem man in Schritt (a) als Polyesterschmelze eine aus Polyethylennaphthalat extrudiert.
5. Verfahren nach Anspruch 4, bei dem man das teilorientierte unverstreckte Garn einer
Schmelzpunkterhöhung von 3-23°C mit einer Geschwindigkeit von 400 bis 4500 m/min aufnimmt.
6. Verstrecktes halbkristallines Polyestermultifilamentgarn mit Tg größer 100°C und einer
Schmelzpunkterhöhung von mindestens 9°C, hergestellt durch Verstreckung eines Polyestergarns
mit einer Doppelbrechung von mindestens 0,030 im unverstreckten Zustand und mit einem
LT Wert von mindestens 25.
7. Verstrecktes Garn nach Anspruch 6 mit einer feinheitsbezogenen Zugfestigkeit von mindestens
6,5 g/d (57,4 mN/dtex), einer Dimensionsstabilität (Bezugsdehnung + Schrumpfung) von
weniger als 5% und einer Schrumpfung von 4% und weniger.
8. Verstrecktes Garn nach Anspruch 7 aus Polyethylennaphthalat.
9. Verstrecktes Polyethylennaphthalatgarn nach Anspruch 8 mit einer Schmelzpunkterhöhung
von 9 bis 15°C, einem Modul von mindestens 280 g/d (2470 mN/dtex) und einer feinheitsbezogenen
Zugfestigkeit von mindestens 7,5 g/d (66,2 mN/dtex).
1. Procédé de production d'un fil de polyester étiré ayant un module accru et une bonne
ténacité, comprenant :
(a) l'extrusion d'un polymère polyester fondu cristallisable ayant une Tv supérieure à 100°C et ayant une viscosité intrinsèque de 0,6 ou plus, à travers un orifice d'extrusion mis en forme présentant une pluralité d'ouvertures, en vue de former un filé fondu,
(b) la solidification du filé en le faisant passer à travers une zone de solidification,
(c) le retrait du fil solidifié à une vitesse d'enroulement à l'état non étiré suffisante pour former un fil partiellement orienté ayant biréfringence de 0,030 à 0,30 et une élévation de point de fusion de +25°C, et
(d) l'étirage à chaud du fil à un rapport d'étirage total d'au moins 1,5/1 pour former un fil étiré ayant un LT d'au moins 25.
2. Procédé selon la revendication 1, dans lequel le filé est solidifié en le faisant
passer à travers une zone de solidification comprenant (a) une zone de refroidissement
retardé comprenant une atmosphère gazeuse chauffée à une température d'au moins 150°C,
et (b) une zone de refroidissement adjacente à ladite zone de refroidissement retardé
dans laquelle ledit fil est rapidement refroidi et solidifié dans une atmosphère d'air
pulsé.
3. Procédé selon la revendication 1 ou la revendication 2, dans lequel la vitesse d'enroulement
à l'état non étiré est de 400 à 4500 m/min.
4. Procédé selon les revendication 1 ou 2, pour la production d'un fil de polyéthylène-naphtalate
étiré, dans lequel le polymère polyester fondu extrudé à l'étape (a) est du polyéthylène-naphtalate.
5. Procédé selon la revendication 4, dans lequel la vitesse d'enroulement à l'état non
étiré est de 400 à 4500 m/min, et l'élévation de point de fusion du fil partiellement
orienté est de 3 à 23°C.
6. Fil multifilament en polyester semi-cristallin étiré ayant une Tv supérieure à 100°C
et une élévation de point de fusion d'au moins 9°C, qui est obtenu en étirant un fil
de polyester ayant une biréfringence à l'état non étiré d'au moins 0,030, et qui a
un LT d'au moins 25.
7. Fil étiré selon la revendication 6 ayant une ténacité d'au moins 6,5 g/d (57,4 mN/dtex),
une stabilité dimensionnelle (EASL (allongement sous une charge spécifiée) + retrait)
inférieure à 5% et un retrait de 4% ou moins.
8. Fil étiré selon la revendication 7, qui est en polyéthylène-naphtalate.
9. Fil en polyéthylène-naphtalate étiré selon la revendication 8, dans lequel l'élévation
de point de fusion est de 9 à 15°C, le module est d'au moins 280 g/d (2470 mN/dtex),
et la ténacité est d'au moins 7,5 g/d (66,2 mN/dtex).