Classifications

• • D—TEXTILES; PAPER
  • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
  • D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
  • D01F6/00—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof
  • D01F6/44—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from mixtures of polymers obtained by reactions only involving carbon-to-carbon unsaturated bonds as major constituent with other polymers or low-molecular-weight compounds
  • D01F6/50—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from mixtures of polymers obtained by reactions only involving carbon-to-carbon unsaturated bonds as major constituent with other polymers or low-molecular-weight compounds of polyalcohols, polyacetals or polyketals
• • D—TEXTILES; PAPER
  • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
  • D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
  • D01F6/00—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof
  • D01F6/02—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from homopolymers obtained by reactions only involving carbon-to-carbon unsaturated bonds
  • D01F6/04—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from homopolymers obtained by reactions only involving carbon-to-carbon unsaturated bonds from polyolefins
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
  • B29C55/00—Shaping by stretching, e.g. drawing through a die; Apparatus therefor
  • B29C55/005—Shaping by stretching, e.g. drawing through a die; Apparatus therefor characterised by the choice of materials
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
  • C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
  • C08J5/18—Manufacture of films or sheets
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
  • C08L23/00—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers
  • C08L23/02—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers not modified by chemical after-treatment
  • C08L23/04—Homopolymers or copolymers of ethene
  • C08L23/08—Copolymers of ethene
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
  • B29K2023/00—Use of polyalkenes or derivatives thereof as moulding material
  • B29K2023/04—Polymers of ethylene
  • B29K2023/06—PE, i.e. polyethylene
  • B29K2023/0658—PE, i.e. polyethylene characterised by its molecular weight
  • B29K2023/0683—UHMWPE, i.e. ultra high molecular weight polyethylene
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
  • C08J2323/00—Characterised by the use of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Derivatives of such polymers
  • C08J2323/02—Characterised by the use of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Derivatives of such polymers not modified by chemical after treatment
  • C08J2323/04—Homopolymers or copolymers of ethene
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
  • C08L2205/00—Polymer mixtures characterised by other features
  • C08L2205/02—Polymer mixtures characterised by other features containing two or more polymers of the same C08L -group

Definitions

• the invention relates to a process for preparing articles, such as filaments, tapes, films, tubes, rods and profiles, from high molecular weight polyethylene, with a high tensile strength and a high modulus and low creep. It is known to prepare articles of high tensile strength and modulus, in particular filaments or tapes, starting from solutions of high molecular weight polyethylene, see US-A-4,344,908; 4,411,854; 4,422,993; 4,430,383 and 4,436,689. In these known processes, a semidilute solution of a linear, high molecular weight polyethylene is via e.g. spinning converted to a solvent-containing article, e.g.
• a filament which is subsequently converted to an article of high strength and modulus by thermoreversible gelation and drawing.
• a polyethylene with a weight-average molecular weight of at least 4 x 10 5 , in particular at least 6 x 10 5 , and preferably above 1 x 10 6 will generally be started from.
• the present invention provides articles with a high modulus, a high tensile strength and low creep, and a process or preparing such articles.
• the invention relates to a process for preparing polyethylene articles of high tensile strength, high modulus and low creep, in which a polyethylene feedstock with a viscosity-average molecular weight of at least 500,000 kg/kmole mixed with a solvent or a mixture of solvents for the polyethylene is converted to a shaped, solvent- containing article at a temperature above the dissolving point, this article is cooled to form a solid gel-like article, and this solid article obtained after cooling is drawn at an elevated temperature, whether or not after complete or partial removal of solvent this process being characterized in that a polyethylene feedstock is used which contains 2-20 alkyl side chains per 1000 carbon atoms.
• a polyethylene copolymer which has a viscosity-average molecular weight of more than 6 x 10 5 , in particular more than 8 x 10 5 and more in particular more than 1 x 10 6 kg/kmole and which preferably contains 3-12 alkyl side chains per 1000 carbon atoms, which side chains preferably contain at most two carbon atoms.
• (B) a polyethylene containing at least 4 alkyl side chains per 1000 carbon atoms, both (A) and (B) having a visosity-average molecular weight of at least 500,000 Kg/Kmole.
• both component (A) and (3) have preferably a viscosity- average molecular weight of more than 6 x 10 5 , in particular more than 8 x 10 5 and more in particular 1 x 10 6 Kg/Kmole, while the blend of (A) and (B) preferably contains 2.5-10 and more preferably 4-7 alkyl side chains per 1000 carbon atoms, which side chains preferably contain at most two carbon atoms.
• the side chains are too long, e.g. 5, 6 or more carbon atoms, the decrease in creep diminished and moreover also the tensile strength and modulus decrease. If a blend of polyethylene is used the amount of side chains in the component with the highest amount of side chains must be below 100, preferably below 20 per 1000 carbon atoms.
• the invention further relates to articles with decreased creep, with a modulus of at least 70 GPa and a tensile strength of at least 2.0 GPa, consisting of an ethylene polymer with a viscosity- average molecular weight of at least 500,000 kg/kmole, which contains 2-20 side chains per 1000 carbon atoms, which side chains are methyl or ethyl groups. It has been found that the articles according to the invention have a plateau creep rate, as defined in Polymer Vol. 19, Aug. 1973, p. 969 (by Wilding, M.A. et al.), which is 10-100 times lower than that of articles from a similar polyethylene with virtually no side chains.
• the invention particularly relates to polyethylene articles having a creep rate of at most 3 x 10 -7 sec -1 (measured at 50oC with a load of 0.75 GPa), preferably at most 2 x 10 -7 sec -1 , and more preferably not more than 1 x 10 -7 sec -1 , while the tensile strength amounts particularly to above 2.5 GPa, preferably at least 3 GPa, and the modulus to above 80 GPa.
• the "a" axis of the crystal unit cell measured by a wide angle X-ray at 20oC and a humidity of 65 % is not less than 7.45 ⁇ .
• the articles are in the form of filaments tapes or films.
• various solvents can be employed. Suitable solvents are, for example, halogenated or non-halogenated hydrocarbons, such as paraffins, paraffinic waxes, toluene, xylene, tetralin, decalin, monochlorobenzene, nonane, decane or mineral oil fractions. Obviously, also mixtures of solvents can be used.
• the polyethylene concentration in the solution may vary, depending on the nature of the solvent and the molecular weight of the polyethylene.
• solutions with a concentration of more than 50 wt.% are rather difficult to handle on account of the high viscosity that occurs.
• solutions with a concentration of, for example, less than 0.5 wt.% is disadvantageous in that the yield is lower and the cost of solvent separation and recovery higher.
• a polyethylene solution with a concentration of between 1 and 50 wt.%, in particular 3-35 wt.% will be used.
• solutions to be used can be prepared in various ways, for example by suspending solid polyethylene in the solvent followed by stirring at an elevated temperature, or by converting the suspension with the aid of a twin-screw extruder equipped with mixing and con- veying parts.
• the conversion of the solution to a shaped, solvent-containing article can be carried out in various ways, for example by spinning via a spinneret with a round or slitshaped die to obtain a filament or a tape, respectively, or extrusion with an extruder, usually with a profiled die.
• the temperature during conversion should be chosen above the dissolving point.
• This dissolving point depends, of course, on the solvent chosen, the concentration, the molar weight and chemical composition of the polyethylene and the pressure applied, and is preferably at least 90°C, in particular at least 100oC. Of course, this temperature is chosen below the decomposition temperature of the polyethylene.
• the solvent-containing article can be drawn before cooling, for example with a draw ratio of 2-20.
• the process according to the invention involves the cooling of the shaped, solvent-containing article to below the gel point, in such a way that virtually no solvent is removed, applying fast cooling, preferably with air and/or a liquid quenching medium, for example water.
• the gel point depends in part on the solvent, of course, and in general virtually coincides with the aforementioned dissolving point.
• the article is cooled to about ambient temperature.
• the article thus obtained can subsequently be drawn.
• it is also possible to remove at least a portion of the solvent before drawing for example by extraction with, for example, dichloroethane.
• the articles are drawn at an elevated temperature, e.g. above the glass transition temperature and below the decomposition temperature of the polyethylene.
• the drawing operation is performed above 75oC. This drawing is preferably carried out in several steps at raising temperatures. It has been found that in the process of the invention high draw ratios can be applied.
• a draw ratio of at least 10, preferably at least 20, and in particular at least 40 is applied.
• the draw ratio can be lower, if a high drawing is applied before cooling.
• the articles according to the invention are suitable for virtually all technical applications where strength and stiffness are required and where weight saving is advantageous.
• the measurement was carried out according to JIS-1013. That is, a S-S curve was determined by using Tensilon manufactured by Toyo Bouldwin Company under the conditions of the sample length of 200 mm and the elongation rate of 100 mm/min to calculate a tensile strength and a tensile modulus. The tensile modulus was calculated from the maximum incline about the origin of the S-S curve.
• Polyethylene powder or a finely pulverized molded article was dissolved in o-dichlorobenzene at 120oC so that a 10% by weight solution was obtained.
• the 13c NMR spectrum at 75 MHz of this solution was observed at 120°C.
• the identification of the signals was made with reference to Makromol. Chem. 184, 569 (1983). Further, a degree of branching was expressed by the ratio of intensity of a peak derived from branching points to that of methylene peak of the main chain.
• Determination of a wide angle X-ray scattering pattern is carried out by using, for example, a X-ray generator CRU-3H type) manufacture by Rigaku Denki Company.
• a copper pair electrode Cu K ⁇ ⁇ 1.5418 ⁇ ) of a tube voltage 45 kv and a tube current of 70 mA which is monochromatized with a nickel filter.
• a filament sample is attached to a sample holder in such a manner that monofilaments are in parallel with each other.
• its thickness is 0.5 to 1.0 mm.
• a wide angle X-ray diffraction pattern is obtained by arranging the fiber axis of the filaments in parallel with each other so that it is oriented to the meridional direction and, size of the "a" axis of a crystal unit cell can be calculated based on the scattering angle 2 ⁇ at the diffraction peak position of the face (200) of the equatorial diffraction curve according to the following formula.
• the creep rate used herein means a deformation rate at a stage where the rate of change of elongation to time after applying a load to a sample becomes constant or, at least, the rate of change becomes the minimum, i.e., at plateau creep as shown, for example, by Journal of Polymer Science, 22, 561 (1984).
• a length of the sample at a certain time (t sec) is represented by l(t) (cm)
• the creep rate can be calculated by the following formula
• Creep rate (sec-1) wherein l o is the length (cm) of the sampel without applying a load; and a is an optional very short period of time (sec).
• Example I A polyethylene with an Mv of about 1.6 x 10 6 kg/kmole, containing about 10 methyl side groups per 1000 C atoms, was suspended in xylene to a nominal concentration of 2 wt.% and, after addition of a stabilizer package and deaeration, dissolved at 130oC. Next, the solution was poured into stainless steel containers and quenched. The solvent was evaporated at room temperature and solvent residues were extracted with dichloroethane. The dry gel films obtained were cut and, at a temperature gradient of 110-130oC, were drawn in a number of steps to a draw ratio of 60. The drawn tapes had an E-modulus of 85 GPa, a tensile strength of 2.0 GPa and a plateau creep rate ( ⁇ ) at room temperature and at a load of 0.9 GPa of 10 -8 sec -1 .
• Example I The procedure of Example I was repeated, but with a polyethylene with an Mv of about 1.5 x 106 kg/kmole, which had 4 methyl side groups per 1000 C-atoms.
• the tapes obtained had an E-modulus of 88 GPa, a tensile strength of 2.1 GPa and a plateau creep rate of 3 x 10 -8 sec -1 . Comparative example A
• Examples I and II The process of Examples I and II was repeated, but with a polyethylene with an Mv of about 1.4 x 10 6 kg/kmole and 1 methyl side group per 1000 C-atoms.
• the tapes obtained had an E-modulus of 90 GPa, a tensile strength of 2.2 GPa and a plateau creep rate of 8 x 10 -7 sec -1 .
• the solution obtained was spun, cooled in water and extracted in dichloromethane, followed by drawing of the gel filaments at 120oC and a draw ratio of 30.
• the filaments obtained had an E-modulus of 95 GPa, a tensile strength of 2.7 GPa and a plateau creep rate of 5 X 10 -8 sec -1 at 50oC and a load of 0.6 GPa.
• Comparative example B The process of Example III was repeated, but with a polyethylene with an Mv of 1.6 x 10 6 kg/kmole and less than 1 methyl side group per 1000 C-atoms.
• the filaments obtained had an E-modulus of 110 GPa, a tensi le strength of 3 GPa and a plateau creep rate of 10 -6 sec -1 .
• Powders of a polyethylene (A) having an Mv of 1.9 x 10 6 and 1.2 methyl side chains per 1000 carbon atoms of the main chain as determined by a high resolving power NMR, and a polyethylene (3) having an Mv of 1.9 x 10 6 and 13.0 methyl side chains per 1000 carbon atoms of the main chain as determined by the same NMR were blended in the weight ratio of 10 : 90.
• decalin 90 parts by weight
• the stock was kneaded and molten with a twin screw extruder having a temperature of 230oC to extrude a clear and uniform dissolved material from an orifice having 0.5 mm diameter.
• the extruded dissolved material was drawn down at a draw-down rate of 30 m/min. with cooling in air flow and then stretched at the draw ratio of 5 times in an air heating oven. Accordingly, the take-up rate of the intermediate stretched material was 150 m/min. Then, the material was stretched at the maximum draw ratio of 3.2 times (therefore, the total draw ratio was 16.0 times) with an oven having 50 m in length under heating atmosphere. The stretching take-up rate of this stage was 100 m/min.
• filaments were prepared except that the polymer blend ratio of the branched polymer (B) to the polymer (A) was changed as shown in Table 1 and the maximum draw ratio of the two stage stretching was changed as shown in Table 1 with respect to each Example (the final take-up rate was constant at 100 m/min). Thus, there was difference between resulting strength of the end molded article.
• Example 2 there are shown the maximum resulting strength of the articles obtained in Examples and Comparative Examples and the creep rate at that time measured at 50oC with a load of 0.75 GPa.
• the article shows excellent high properties and superior creep resistance.
• Example VI about 1/20 creep resistance is shown in comparison with that of Comparative
• Example C Although creep is low when using 100% of a branched polymer as shown in Comparative Example D, high tenacity filaments can not be obtained.

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• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Chemical Kinetics & Catalysis (AREA)
• Health & Medical Sciences (AREA)
• Medicinal Chemistry (AREA)
• Polymers & Plastics (AREA)
• Organic Chemistry (AREA)
• Manufacturing & Machinery (AREA)
• General Chemical & Material Sciences (AREA)
• Textile Engineering (AREA)
• Materials Engineering (AREA)
• Mechanical Engineering (AREA)
• Manufacture Of Macromolecular Shaped Articles (AREA)
• Addition Polymer Or Copolymer, Post-Treatments, Or Chemical Modifications (AREA)
• Artificial Filaments (AREA)
• Macromolecular Compounds Obtained By Forming Nitrogen-Containing Linkages In General (AREA)
• Materials For Medical Uses (AREA)
• Compositions Of Macromolecular Compounds (AREA)
• Preventing Corrosion Or Incrustation Of Metals (AREA)
• Polyesters Or Polycarbonates (AREA)
• Solid-Sorbent Or Filter-Aiding Compositions (AREA)

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• 1987
  • 1987-10-20 IN IN760/MAS/87A patent/IN170335B/en unknown
  • 1987-10-27 BR BR8707520A patent/BR8707520A/pt not_active Application Discontinuation
  • 1987-10-27 ES ES198787202055T patent/ES2025633T3/es not_active Expired - Lifetime
  • 1987-10-27 WO PCT/NL1987/000029 patent/WO1988003184A1/en active Application Filing
  • 1987-10-27 AT AT87202055T patent/ATE66703T1/de not_active IP Right Cessation
  • 1987-10-27 AU AU81067/87A patent/AU603838B2/en not_active Ceased
  • 1987-10-27 US US07/540,462 patent/US5128415A/en not_active Expired - Lifetime
  • 1987-10-27 EP EP87202055A patent/EP0269151B2/en not_active Expired - Lifetime
  • 1987-10-27 DE DE8787202055T patent/DE3772525D1/de not_active Expired - Lifetime
  • 1987-10-28 MX MX009008A patent/MX168759B/es unknown
  • 1987-10-29 IL IL84313A patent/IL84313A/xx not_active IP Right Cessation
  • 1987-10-29 CA CA000550530A patent/CA1329873C/en not_active Expired - Lifetime
  • 1987-10-30 IE IE291987A patent/IE60694B1/en not_active IP Right Cessation
  • 1987-10-30 NZ NZ222368A patent/NZ222368A/xx unknown
• 1988
  • 1988-06-29 FI FI883113A patent/FI883113A/fi not_active Application Discontinuation
  • 1988-06-29 DK DK359988A patent/DK359988D0/da not_active Application Discontinuation
  • 1988-06-30 NO NO882932A patent/NO170293C/no unknown
  • 1988-06-30 KR KR1019880700755A patent/KR890700177A/ko not_active Application Discontinuation
• 1991
  • 1991-11-27 GR GR91401817T patent/GR3003200T3/el unknown

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