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WO2008113567A1 - Fibres, rubans ou filaments comprenant une composition de polyéthylène multimodal - Google Patents

Fibres, rubans ou filaments comprenant une composition de polyéthylène multimodal Download PDF

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Publication number
WO2008113567A1
WO2008113567A1 PCT/EP2008/002190 EP2008002190W WO2008113567A1 WO 2008113567 A1 WO2008113567 A1 WO 2008113567A1 EP 2008002190 W EP2008002190 W EP 2008002190W WO 2008113567 A1 WO2008113567 A1 WO 2008113567A1
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Prior art keywords
fibre
tape
fibres
multimodal
lldpe
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PCT/EP2008/002190
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English (en)
Inventor
Henk Van Paridon
Bert Broeders
Irene Helland
Peter Voortmans
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Borealis Technology Oy
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Application filed by Borealis Technology Oy filed Critical Borealis Technology Oy
Priority to CN200880009377.6A priority Critical patent/CN101657572B/zh
Priority to EP08716622.9A priority patent/EP2137344B2/fr
Priority to AT08716622T priority patent/ATE517201T1/de
Publication of WO2008113567A1 publication Critical patent/WO2008113567A1/fr

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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
    • D01F6/28—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from copolymers obtained by reactions only involving carbon-to-carbon unsaturated bonds
    • D01F6/30—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from copolymers obtained by reactions only involving carbon-to-carbon unsaturated bonds comprising olefins as the major constituent
    • 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
    • D01F6/46—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 polyolefins

Definitions

  • Fibres, tapes or filaments comprising a multimodal polyethylene composition
  • This invention relates to the fibres, tapes and filaments comprising a multimodal polyethylene (PE) composition, to the preparation method thereof, to the use of a multimodal polyethylene composition for preparing fibres, tapes or filaments, as well as articles comprising said fibres, tapes or filaments, wide variety of application areas including, technical applications, household applications, as well as interior and sports applications.
  • PE polyethylene
  • Polyethylene materials used for fibre, tape and filament products have conventionally been unimodal. Typically they also have high density, e.g. of above 945 kg/m 3 .
  • WO2006053709 describes a multimodal polyethylene for drawn tapes, fibres and filaments having a density of at least 940 kg/m 3 .
  • Such polymers are stated to provide similar or improved properties, such as tenacity, to fibres compared to unimodal polyethylene products in the same density level.
  • fibres need to withstand heavy mechanical stress and wear.
  • the fibre material is soft, but at the same time has good abrasion, i.e. wear resistance.
  • Fibres should also preferably be resilient and/or tenacious in order to recover their original state after subjected under a mechanical stress.
  • a good UV (ultra violet) light stability is needed. The above properties would be advantageous in order to maintain a constant performance and/or appearance for longer terms.
  • Polypropylene based fibres have been used in prior art for many demanding applications, such as in sport surfaces. However, such prior art fibres may have insufficient softness and UV-stability.
  • abrasion wear resistance of prior art unimodal polyethylene fibres is usually not sufficient to maintain a constant performance, e.g. to guarantee constant sports/playing characteristics of an artificial grass for longer periods.
  • Another object of the invention is to provide alternative fibres, tapes or filaments comprising a multimodal polyethylene composition and exhibiting an excellent property balance useful for various fibre applications, i.a. for technical applications including industrial, agricultural and geological applications, such as ropes, twines, big bags, nets and geo textiles, as well as for household, interior and sports applications, e.g. for synthetic carpet and sport surfaces, such as artificial grass materials for play and sport grounds for indoor or outdoor use.
  • the invention provides a process for producing fibres, tapes and filaments of the invention, as well as articles comprising said fibres, tapes and filaments.
  • Figure 1 shows a scheme of the yarn path in a weaving simulator used in the abrasion resistance test described under Determination Methods.
  • Figure 2 is a graph illustrating the balance between tenacity and elongation at stretch ratios 1 :5 and 1 :6 measured for the example znLLDPEl of the invention and reference examples PEl and PE2.
  • Figure 3 is a graph illustrating the abrasion, i.e. wear resistance of materials of example znLLDPEl of the invention and reference examples PEl and PE2 in a weaving simulator, when subjected to a treatment of 6000 cycles under a load (12O g per tape). For each material 5 tape samples were made and the graph shows the number of tapes broken during the test and the number of cycles at the time of fracture.
  • the present invention is directed to a fibre, tape or filament comprising a multimodal linear low density polyethylene composition having a density of less than 940 kg/m 3 . Due to the low density, softer fibre materials can be provided compared to higher density fibre materials conventionally used in prior art. Surprisingly, the softer fibres, tapes and filaments provided by this invention have an excellent wear resistance expressed also as abrasion resistance. The wear resistance of the fibres, tapes or filaments is at least comparable or may even be improved compared to prior art fibres made from unimodal, higher density polyethylene. Accordingly, the multimodal linear low polyethylene of the present invention is a highly suitable alternative material for fibres, tapes or filaments.
  • the polyethylene usable in this invention is a linear polyethylene. It is thus different from low density polyethylene (LDPE) produced in a high pressure polymerisation in a tubular or an autoclave reactor using typically a free radical initiator.
  • LDPE low density polyethylene
  • the used terms and the meanings/ differences thereof are widely known in the field.
  • a polyethylene composition having a density of 940 kg/m 3 or less may sometimes be defined in the polymer literature as covering i.a. a medium density polyethylene (MDPE) composition and a linear low density ethylene (LLDPE) composition.
  • MDPE medium density polyethylene
  • LLDPE linear low density ethylene
  • Fibers, tapes or filaments used in this application for fibers, tapes and filaments of the invention is shortly abbreviated as “Fibres” and it covers and means all conventional forms known, producible and used in the field of fibres.
  • said Fibre provides, in addition to above mentioned unexpected balance between softness and wear resistance, preferably also i.a. very feasible tensile properties, expressed as a balance between tenacity and elongation at break properties, when measured as defined below under Determination Methods. Also preferably the Fibres of the invention may further have a good UV stability.
  • multimodal LLDPE material usable in said Fibres can be further tailored and optimised in relation to one or more of the additional preferable properties mentioned in relation to above mentioned Fibre embodiment, depending on the intended end use application.
  • Fibres of the invention are very suitable in wide variety of fibre applications, i.a. for technical applications including industrial, agricultural and geological applications, such as ropes and twines, big bags and geo textiles, as well as for household, interior and sports applications, e.g. for synthetic carpet and sport surfaces, such as artificial grass materials for play and sport grounds for indoor or outdoor use.
  • Fibres are attached by any conventional fixing means to a typically flat base element so that at least one of the fibre ends is freely protruding from the base element. Fibres may also be fixed to the base element from their centre part leaving the Fibre ends with a certain length free and “freely moving”.
  • the length of the free "Fibre ends” can vary depending on the desired end application, as well known in the art.
  • average diameter/width of Fibre of the invention can vary depending on the end application.
  • multimodal LLDPE composition present in said Fibres can be further tailored and optimised in relation to one or more of the additional preferable properties as listed e.g. above, depending on the end use application wherein the Fibre is intended.
  • multimodal LLDPE composition present in said Fibre as defined above or below may be polymerised using any conventional coordination catalyst.
  • multimodal LLDPE compositions usable in said Fibre include e.g. LLDPE polymerized using a Ziegler Natta catalyst (referred herein as znLLDPE), LLDPE polymerized using a single site catalyst including a metallocene and a non- metallocene catalyst (all single site based LLDPEs are referred herein as mLLDPE) or LLDPE polymerized using a Chromium catalyst.
  • multimodal LLDPE composition is a multimodal znLLDPE.
  • multimodal means herein, unless otherwise stated, multimodality with respect to molecular weight distribution and includes also bimodal polymer.
  • a polyethylene e.g. LLDPE composition
  • multimodal a polyethylene, e.g. LLDPE composition, comprising at least two polyethylene fractions, which have been produced under different polymerization conditions resulting in different (weight average) molecular weights and molecular weight distributions for the fractions.
  • multimodal relates to the number of different polymer fractions present in the polymer.
  • multimodal polymer includes so called “bimodal" polymer consisting of two fractions.
  • the form of the molecular weight distribution curve i.e.
  • the appearance of the graph of the polymer weight fraction as a function of its molecular weight, of a multimodal polymer, e.g. LLDPE, will show two or more maxima or is typically distinctly broadened in comparison with the curves for the individual fractions.
  • a polymer is produced in a sequential multistage process, utilizing reactors coupled in series and using different conditions in each reactor, the polymer fractions produced in the different reactors will each have their own molecular weight distribution and weight average molecular weight.
  • the individual curves from these fractions form typically together a broadened molecular weight distribution curve for the total resulting polymer product.
  • the multimodal LLDPE usable in the present invention comprises preferably a lower weight average molecular weight (LMW) component and a higher weight average molecular weight (HMW) component.
  • LMW lower weight average molecular weight
  • HMW weight average molecular weight
  • Said LMW component has a lower molecular weight than the HMW component.
  • said multimodal LLDPE comprises at least (i) a lower weight average molecular weight (LMW) ethylene homopolymer or copolymer component, and (ii) a higher weight average molecular weight (HMW) ethylene homopolymer or copolymer component.
  • LMW lower weight average molecular weight
  • HMW higher weight average molecular weight
  • at least one of said LMW and HMW components is a copolymer of ethylene with at least one comonomer. It is preferred that at least said HMW component is an ethylene copolymer.
  • said LMW component is preferably the homopolymer.
  • said multimodal LLDPE may comprise further polymer components, e.g. three components being a trimodal LLDPE.
  • multimodal LLDPE may also comprise e.g. up to 10 % by weight of a well known polyethylene prepolymer which is obtainable from a prepolymerisation step as well known in the art, e.g. as described in WO9618662.
  • the prepolymer component is comprised in one of LMW and HMW components, preferably LMW component, as defined above.
  • said multimodal LLDPE is bimodal LLDPE comprising said LMW and HMW components and optionally a prepolymerised fraction as defined above.
  • multimodality and density as defined in claim 1 for multimodal LLDPE provides the unexpected effect of the invention, i.a. softness and wear resistance.
  • the other properties of said multimodal LLDPE can further contribute to excellent properties of the invention and can be varied within the scope of the invention depending on the desired end application use. Accordingly, said multimodal LLDPE composition may have any of the preferred properties given generally below, in any combination.
  • Said multimodal LLDPE composition useful in the present invention as defined above or below has preferably a density of 938 kg/m 3 or less.
  • the lower limit is typically more than 905 kg/m 3 , preferably 915 kg/m 3 or more, more preferably 920 kg/m 3 or more.
  • the melt flow rate, MFR 2 , of said multimodal LLDPE is preferably in the range of 0.01 to 20 g/10min, e.g. of 0.05 to 10 g/lOmin, preferably of 0.05 to 6.0 g/10min, more preferably in the range of 0.1 to 5 g/10min.
  • MFR 2 of said multimodal LLDPE may be even less than 3 g/10 min, e.g. 0.1 to 2.5 g/10min.
  • the MFR 5 of said multimodal LLDPE as defined above or below may be up to 10 g/10 min, preferably in the range of 0.01 to 5 g/10 min, such as of 0.05 to 4 g/10min.
  • the Mw of LLDPE may be in the range of 100,000 to 300,000, preferably of 150,000 to 270,000.
  • the molecular weight distribution (MWD), Mw/Mn, of the multimodal LLDPE is preferably at least 5, more preferably at least 8, such as in the range of 10 to 40, preferably up to 30, and, depending on the end application, also a Mw/Mn in the range of 10 to 25 may be desired.
  • ethylene copolymer or "LLDPE copolymer” as used herein encompasses polymers comprising repeat units deriving from ethylene and at least one other C3- 20 alpha olefin monomer as comonomer.
  • said multimodal LLDPE copolymer may be formed from ethylene along with at least one C3-12 alpha-olefin comonomer, e.g. 1-butene, 1-hexene or 1-octene.
  • said multimodal LLDPE is a binary copolymer, i.e. the polymer contains ethylene and one comonomer, or a terpolymer, i.e.
  • the polymer contains ethylene and two or three comonomers.
  • said multimodal LLDPE comprises an ethylene hexene copolymer, ethylene octene copolymer or ethylene butene copolymer.
  • the amount of comonomer present in said multimodal LLDPE is preferably at least 0.25 mol-%, more preferably at least 0.5 mol-%, such as 0.5 to 12 mol%, e.g. 2 to 10 mol-% relative to ethylene. In some embodiments a comonomer range of 4 to 8 mol-% may be desired.
  • comonomer contents present in said multimodal LLDPE may be 1.5 to 10 wt%, especially 2 to 8 wt% relative to ethylene.
  • any copolymeric HMW component preferably at least 0.5 mol-%, e.g. at least l-mol%, such as up to 10 mol-%, of repeat units are derived from said comonomer.
  • Said LMW component of said multimodal LLDPE as defined above or below may have a MFR 2 of at least 50, typically 50 to 3000 g/10 min, preferably at least 100 g/10 min, more preferably 110 to 500 g/10 min.
  • the molecular weight of said LMW component should preferably range from 15,000 to 50,000, e.g. 20,000 to 40,000.
  • the density of said LMW component may range from 930 to 980 kg/m 3 , e.g. 930 to 970 kg/m 3 , such as 935 to 960 kg/m 3 , and typically 940 to 980 kg/m 3 , preferably 960 to 975 kg/m 3 in case of a LMW homopolymer.
  • Said LMW component amounts preferably from 30 to 70 wt%, e.g. 40 to 60% by weight of the total weight of said multimodal LLDPE.
  • Said HMW component forms typically 70 to 30 wt%, e.g. 40 to 60% by weight of said multimodal LLDPE.
  • said HMW component forms 50 wt% or more of the multimodal LLDPE as defined above or below.
  • Said HMW component of said multimodal LLDPE as defined above or below has a lower MFR 2 and a lower density than said LMW component.
  • Said HMW component has preferably an MFR 2 of less than 1 g/10 min, preferably less than 0.5 g/10 min, especially less than 0.2 g/lOmin.
  • the density of said HMW component may be above 900 kg/m 3 , preferably a density of 910 to 930, e.g. up to 925 kg/m 3 .
  • the Mw of HMW component may range from 100,000 to 1,000,000, preferably 250,000 to 500,000.
  • said multimodal LLDPE as defined above or below is a multimodal znLLDPE copolymer of ethylene with at least one comonomer, as defined above.
  • Suitable multimodal LLDPE preferably znLLDPE, as defined above or below for preparing Fibres of the invention can be any conventional, e.g. commercially available, polymer composition.
  • Commercially available useful multimodal LLDPE polymers are, without limiting to these, i.a. LLDPE grades available from Borealis e.g. under trademark Borstar® FBXXX, such as Borstar® FB4370 etc.
  • suitable multimodal LLDPE polymer compositions can be produced in a known manner according to or analogously to conventional polymerisation processes, including solution, slurry and gas phase processes, described in the literature of polymer chemistry.
  • Multimodal (e.g. bimodal) LLDPE useful in the present invention can be obtainable by blending two or more, separately prepared polymer components mechanically or, preferably, by in-situ blending in a multistage polymerisation process during the preparation process of the polymer components. Both mechanical and in-situ blending are well known in the field.
  • preferred multimodal LLDPE polymers are obtainable by in-situ blending in a multistage, i.e. two or more stage, polymerization process including solution, slurry and gas phase process, in any order.
  • said multimodal LLDPE may be obtainable by using two or more different polymerization catalysts, including multi- or dual site catalysts, in a one stage polymerization.
  • the multimodal LLDPE is produced in at least two-stage polymerization using the same catalyst, e.g. a single site or Ziegler-Natta catalyst.
  • a single site or Ziegler-Natta catalyst e.g. a single site or Ziegler-Natta catalyst.
  • the multimodal LLDPE is made using a slurry polymerization in a loop reactor followed by a gas phase polymerization in a gas phase reactor.
  • a loop reactor - gas phase reactor system is well known as Borealis technology, i.e. as a BORSTAR ® reactor system.
  • Any multimodal LLDPE present in the Fibre of the invention is thus preferably formed in a two stage process comprising a first slurry loop polymerisation followed by gas phase polymerisation.
  • Such multistage process is disclosed e.g. in EP517868.
  • the reaction temperature will generally be in the range 60 to 110°C, e.g. 85-110°C
  • the reactor pressure will generally be in the range 5 to 80 bar, e.g. 50-65 bar
  • the residence time will generally be in the range 0.3 to 5 hours, e.g. 0.5 to 2 hours.
  • the diluent used will generally be an aliphatic hydrocarbon having a boiling point in the range -70 to +100°C.
  • polymerization may if desired be effected under supercritical conditions.
  • Slurry polymerisation may also be carried out in bulk where the reaction medium is formed from the monomer being polymerised.
  • the reaction temperature used will generally be in the range 60 to 115°C, e.g. 70 to 110°C
  • the reactor pressure will generally be in the range 10 to 25 bar
  • the residence time will generally be 1 to 8 hours.
  • the gas used will commonly be a non-reactive gas such as nitrogen or low boiling point hydrocarbons such as propane together with monomer, e.g. ethylene.
  • a chain-transfer agent preferably hydrogen
  • at least 100 to preferably at least 200, and up to 1500, preferably up to 800 moles of H 2 /kmoles of ethylene are added to the loop reactor, when the LMW fraction is produced in this reactor, and 0 to 60 or 0 to 50 , moles of H 2 /kmoles of ethylene and, again depending on the desired end application, in certain embodiments even up to 100, or up to 500 moles of H 2 /kmoles of ethylene are added to the gas phase reactor when this reactor is producing the HMW fraction.
  • the lower molecular weight polymer fraction is produced in a continuously operating loop reactor where ethylene is polymerised in the presence of a polymerization catalyst as stated above and a chain transfer agent such as hydrogen.
  • the diluent is typically an inert aliphatic hydrocarbon, preferably isobutane or propane.
  • the reaction product is then transferred, preferably to continuously operating gas phase reactor.
  • the HMW component can then be formed in a gas phase reactor using preferably the same catalyst. Prepolymerisation step may precede the actual polymerisation process. Where the HMW component is made as a second step in a multistage polymerisation it is not possible to measure its properties directly. However, e.g.
  • the density, MFR 2 etc of the HMW component can be calculated using Kim McAuley's equations.
  • both density and MFR 2 can be found using K. K. McAuley and J. F. McGregor: On-line Inference of Polymer Properties in an Industrial Polyethylene Reactor, AIChE Journal, June 1991, Vol. 37, No, 6, pages 825-835.
  • the density is calculated from McAuley's equation 37, where final density and density after the first reactor is known.
  • MFR 2 is calculated from McAuley's equation 25, where final MFR 2 and MFR 2 after the first reactor is calculated.
  • the multimodal LLDPE as defined above or below, suitable in the present invention may be made using any conventional catalyst, such as a chromium, single site catalysts, including metallocenes and non-metallocenes as well known in the field, or Ziegler-Natta catalysts as is also known in the art.
  • Preferred catalysts are any conventional Ziegler Natta catalysts and the choice of an individual catalyst used to make znLLDPE is not critical.
  • the polyethylene polymer composition is manufactured using Ziegler-Natta catalysis.
  • Preferred Ziegler-Natta catalysts comprise a transition metal component and an activator.
  • the transition metal component comprises a metal of Group 4 or 5 of the Periodic System (IUPAC) as an active metal. In addition, it may contain other metals or elements, like elements of Groups 2, 13 and 17.
  • the transition metal component is a solid. More preferably, it has been supported on a support material, such as inorganic oxide carrier or magnesium halide. Examples of such catalysts are given, among others in WO 95/35323, WO 01/55230, WO 2004/000933, EP 810235 and WO 99/51646.
  • the polyethylene composition is produced using a Ziegler Natta catalysts disclosed in WO 2004/000933 or EP 688794.
  • the obtained reaction product of said multimodal LLDPE polymerisation process is typically pelletised in well known manner and the pellets of multimodal LLDPE are then used for Fibre formation.
  • the Fibres of the invention may contain other polymer than multimodal LLDPE as well.
  • the Fibre consists of multimodal LLDPE.
  • Said term "consists of " when used in this application in relation to polymer composition present in Fibre means only that no other polymer components are present in such Fibre embodiment, but naturally said Fibres of such embodiment may comprise conventional fibre additives such as antioxidants, UV stabilisers, colour masterbatches, acid scavengers, nucleating agents, anti-blocking agents, slip agents etc. as well as polymer processing agent (PPA).
  • PPA polymer processing agent
  • this can be added to the polymer composition e.g. during the preparation of the polymer of during the fibre preparation process.
  • the multimodal LLDPE polymer product as defined above or below, typically in the form of pellets, is converted to Fibres of the invention in a manner well known and documented in the art.
  • the fibres can preferably be produced via a film extrusion process, such as cast film or blown film process, via film slitting to produce i.a. tapes, or via a direct extrusion process to produce filaments, preferably monofilaments.
  • a film extrusion process such as cast film or blown film process
  • film slitting to produce i.a. tapes or via a direct extrusion process to produce filaments, preferably monofilaments.
  • filaments preferably monofilaments.
  • Fibres of the invention comprise a mixture of multimodal LLDPE together with other polymer components, the different polymer components are typically intimately mixed prior to extrusion as is well known in the art.
  • said multimodal LLDPE polymer product can be extruded into fibres, tapes or filaments, preferably monofilaments, using know filament extrusion process.
  • One useful process for producing the Fibres of invention is described in "Fiber Technology" Hans A.Krassig, J ⁇ rgen Lenz, Herman F. Mark; ISBN: 0-8247-7097-8.
  • said multimodal LLDPE composition may be extruded into a film which is subsequently cut into fibres and tapes in a known manner. Both preparation methods are conventional and generally known in the production of fibres, tapes and filaments.
  • the film may be prepared by any conventional film formation process including extrusion procedures, such as cast film or blown film extrusion, lamination processes or any combination thereof.
  • the film may be mono or multilayer film, e.g. coextruded multilayer film, hi case of multilayer film, preferably, the film layers may comprise the same or different polymer composition, whereby at least one layer comprises said multimodal LLPDE of the invention.
  • all layers of a multilayer film comprise, more preferably consist of, the same multimodal LLDPE composition.
  • the film is formed by blown film extrusion and in case of multilayered film structure by blown film coextrusion processes.
  • the LLDPE composition may be blown (co)extruded at a temperature in the range 160°C to 240°C, and cooled by blowing gas (generally air) at a temperature of 10 to 50 0 C to provide a frost line height of 1 or 2 to 8 times the diameter of the die.
  • blowing gas generally air
  • the blow up ratio should generally be less than 6, e.g. less than 4, more preferably between 1.0 to 1.5, and even more preferably 1.0 to 1.2.
  • the film may be (co)extruded to form first a bubble which is then collapsed and cooled, if necessary, and the obtained tubular film is cut to fibres.
  • the (co)extruded bubble may be collapsed and split into two film laminates. The formed film is then cut to Fibres.
  • Fibres can be cut from a cast film that is produced by procedures well known in the field.
  • Fibres are in stretched, i.e. oriented, form.
  • Fibres are stretched uniaxially, more preferably in the machine direction (MD).
  • MD machine direction
  • said Fibres can be stretched to a desired draw ratio after extrusion to filaments
  • said film can be stretched before cutting to stretched Fibres, e.g. tapes, or the film is first cut e.g. to tapes and then the formed tapes are stretched to form final Fibres.
  • the Film is first cut e.g. to tapes which are then stretched to a desired draw ratio to form final Fibres.
  • stretched Fibres are provided which are preferably in stretched, i.e. oriented, form, preferably in uniaxially oriented form.
  • the Fibre preparation process preferably comprises a step of stretching extruded filaments, of stretching fibres/tapes cut from a film, or of stretching film prior to cutting into fibres/tapes, whereby the stretching is preferably effected in the machine direction (MD) in a draw ratio of at least 1 :3.
  • MD machine direction
  • a preferable Fibre preparation process thus comprises a step of extruding the multimodal LLDPE into
  • Fibre which is optionally stretched, preferably in MD, at least 3 times its original length, or
  • extruded fibres, fibres/tapes cut from a film or a film prior to cutting into fibres/tapes is/are stretched 3 to 10 times its/their original length in the MD.
  • the expressions "stretching 3 times its/their original length” and “drawn down to 3 times its/their original length” mean the same and can also be expressed as a "stretch ratio of at least 1 :3" and, respectively, “draw ratio of at least 1 :3", wherein "1" represents the original length of the film and "3" denotes that it has been stretched/drawn down to 3 times that original length.
  • Preferred films of the invention are stretched in a draw ratio of at least 1 :4, more preferably in the range of 1 :5 to 1 :8, e.g. in a draw ratio of between 1 :5 and 1 :7.
  • An effect of stretching, i.e. drawing, is that the thickness of the film is similarly reduced.
  • a draw ratio of at least 1 :3 means preferably that also the thickness of the film is at least three times less than the original thickness.
  • Fibres can then be further processed to articles such as ropes, twines, nets, bags or textiles for technical and agricultural use, or i.a. artificial grass for use e.g. in sports grounds etc.
  • Fibre of the invention
  • the Fibre can be in a form of a fibre, tape or filament comprising a multimodal LLDPE, preferably znLLDPE, copolymer as defined above.
  • the Fibre forms part of the invention.
  • said Fibre consists of a multimodal LLDPE copolymer, preferably a multimodal znLLDPE copolymer, as defined above or in claims below.
  • the Fibre of the invention does not have a hollow core, rather it is solid across ts cross section. It is preferred therefore if the Fibre of the invention is not hollow.
  • Fibre thus naturally covers fibres, tapes and filaments of any shape and size. The dimensions thereof depend on the end application area, as well known in the art. Filaments are preferably monofilaments.
  • Fibre is in stretched form as defined above.
  • such tape of the invention may typically have a width of at least 0.5 mm, preferably of at least 1 mm.
  • the upper limit of a tape width is not critical and can be e.g. up to 10 mm, preferably up to 6 mm.
  • the thickness of a tape of the invention may be e.g. at least 5 ⁇ m, preferably at least 10 ⁇ m.
  • the upper limit of a tape thickness is not limited and can be e.g. up to 80 ⁇ m, preferably up to 50 ⁇ m, in some end applications preferably up to 20 ⁇ m.
  • the dimensions thereof typically correspond to the size range, i.e. dimensions, given above for a tape form.
  • Fibres in stretched form are in stretched form and may have the width and other dimensions as defined above.
  • the Fibres have an excellent balance between softness and wear resistance, and preferably one or more of the following properties may also be very advantageous: UV-stability, tenacity and/or resilience properties.
  • the application area of Fibres is not limited and it has unexpectedly found that the "soft" Fibres of the invention are very feasible for mechanically demanding applications wherein good mechanical properties, such as good wear resistance, are needed.
  • Fibres show good tensile properties expressed as a balance between tenacity and elongation at break, when measured using tensile tests according to ISO 2062 (year 1993) as defined below under Determination Methods.
  • the samples used for the tensile determinations were prepared as described under Sample Preparation.
  • Fibre of the invention comprises a multimodal LLDPE as defined above or in claims which multimodal LLDPE has a tenacity of at least 0.40 N/tex and residual elongation at break of at least 13 %, preferably of at least 15 %, when measured according to ISO 2062 (year 1993) using a tape sample consisting of said- multimodal LLDPE and drawn to 6 times it original length. Said method is described below under Determination Methods. The tape sample was prepared as described below under Fibre Sample Preparation.
  • Fibre of the invention when drawn to 6 times to its original length has a tenacity of at least 0.40 N/tex and residual elongation at break of at least 13 %, preferably of at least 15 %, when measured according to ISO 2062 (year 1993) as defined below.
  • the Fibres can be used to prepare articles.
  • the invention thus further provides an article comprising fibres, tapes or filaments as defined above.
  • articles are i.a. ropes and twines, big bags, nets and geo textiles, as well as synthetic carpet and sport surfaces, such as artificial grass materials for play and sport grounds for indoor or outdoor use, or carpets for private and public premises, such as for corridors, offices and show rooms.
  • the Fibres of the invention are sufficiently soft and have good wear resistance, i.e. they are resistant to abrasion. Preferably they also have good resilience and/or UV stability which is needed especially for outdoor applications.
  • Fibre Sample Preparation the properties of Fibre of the invention given above in the description and below in claims are not limited to the Fibre Sample used in the determinations, but apply generally to the Fibre of the invention as defined in claims and/or in preferred embodiments.
  • the Fibre Sample defined herein is merely for meeting the sufficiency/reproducibility of the invention.
  • Density of the materials is measured according to ISO 1183:1987 (E), method D, with isopropanol-water as gradient liquid.
  • the cooling rate of the plaques when crystallising the samples was 15 C/min. Conditioning time was 16 hours.
  • MFR 2 , MFR 5 and MFR 2I measured according to ISO 1133 at 190°C at loads of 2.16, 5.0, and 21.6 kg respectively.
  • a Waters 150CV plus instrument, equipped with refractive index detector and online viscosimeter was used with 3 x HT6E styragel columns from Waters (styrene-divinylbenzene) and 1 ,2,4-trichlorobenzene (TCB, stabilized with 250 mg/L 2,6-Di tert butyl-4-methyl-phenol) as solvent at 140 °C and at a constant flow rate of 1 mL/min. 500 ⁇ L of sample solution were injected per analysis.
  • the column set was calibrated using universal calibration (according to ISO 16014-2:2003) with 15 narrow MWD polystyrene (PS) standards in the range of 1.0 kg/mol to 12 000 kg/mol.
  • Melting temperature and Crystallisation temperature, Tm and Tcr both were measured according to ISO 11357-1 on Perkin Elmer DSC-7 differential scanning calorimetry. Heating curves were taken from -10 0 C to 200 0 C at 10°C/min. Hold for 10 min at 200 0 C. Cooling curves were taken from 200 0 C to -10 0 C at 10 0 C per min. Melting and crystallization temperatures were taken as the peaks of endotherms and exotherms. The degree of crystallinity was calculated by comparison with heat of fusion of a perfectly crystalline polyethylene, i.e. 290 J/g.
  • Comonomer content (mol%) was determined based on Fourier transform infrared spectroscopy (FTIR) determination calibrated with C13-NMR.
  • FTIR Fourier transform infrared spectroscopy
  • Tenacity and elongation at break were determined by tensile tests. Tensile tests were performed on an Instron apparatus according to the ISO 2062 (year 1993) Norm with the following measuring settings:
  • Abrasion resistance i.e. wear resistance
  • Centexbel the abrasion resistance, i.e. wear resistance
  • Fibre samples were tape samples which were prepared by using a state of the art pilot cast film stretch tape line.
  • the extruder was equipped with a metering pump to ensure a constant output.
  • the water quenching tank, godets and oven used were Riefenhhauser components.
  • the temperature profile of the extruder used was 225 °C, 230°C and 235 °C.
  • the die was kept at 235 °C.
  • Film die had a 0.1 mm gap width.
  • a 75 micron primary film was extruded into a water quench (30 °C) water bath.
  • the take of speed off the first godet roll was kept at 10 m/min.
  • Fibre sample series tape samples were drawn 5 times their original length (draw ratio of 1 :5) and 2.
  • Fibre sample series tape samples were drawn 6 times their original length (draw ratio of 1 :6), unless otherwise stated.
  • znLLDPEl of Invention A multimodal znLLDPE having a MFR 2 of 0.4 g/10 min,
  • Reference PEl A commercially available unimodal znPE copolymer grade for fibres having a MFR 2 of 0.60 g/10 min, MFR 2I of 19 g/10 min and a density of 947 kg/m 3 .
  • Reference PE2 A commercially available unimodal polyethylene copolymer grade for fibres produced using a Cr catalyst and having a MFR 2 of 0.4 g/10 min, MFR 2I of 28 g/10 min and a density of 945 kg/m 3 .
  • a multimodal znLLDPEl polymer was prepared in a pilot scale multistage reactor system containing a loop reactor and a gas phase reactor.
  • a prepolymerisation step preceded the actual polymerisation step.
  • the prepolymerisation stage was carried out in slurry in a 50 dm 3 loop reactor at about 80°C in a pressure of about 65 bar using the polymerisation catalyst prepared analogously to Example 3 of EP 688794 using silica support having average particle size of 25 ⁇ m and triethylaluminium as the cocatalyst.
  • the molar ratio of aluminium of the cocatalyst to titanium of the catalyst was about 20.
  • Ethylene was fed in a ratio of (20Og of C2)/(lg/catalyst).
  • Propane was used as the diluent and hydrogen was feeded in amount to adjust the MFR2 of the prepolymer to about 10 g/10 min.
  • the obtained slurry together with prepolymerised catalyst and triethyl aluminium cocatalyst were introduced into a 500 dm 3 loop reactor, wherein also a continuous feeds of propane, ethylene and hydrogen were introduced.
  • the feed ratio of H2/C2 was 395 mol/kmol.
  • the loop reactor was operated at 95 °C temperature and 60 bar.
  • the process conditions were adjusted to form polymer having an MFR 2 of 400 g/10 min and a density of about 970 kg/m 3 .
  • the obtained slurry was then transferred to a fluidised bed gas phase reactor, where also additional ethylene, 1-butene comonomer and hydrogen were added, together with nitrogen as an inert gas to produce the HMW component in the presence of the
  • the gas phase reactor was operated at a temperature of 80 °C and a pressure of 20 bar and the feed ratio of H2/C2 and the feed ratio of C4/C2 were adjusted in a manner known to a skilled person to produce prepolymerised final bimodal polymer which, after collecting the polymer, blending with additives and extruding into pellets in a counter rotating twin-screw extruder JSW CIM90P, resulted to a polymer having an MFR 2 of 0.4 g/10 min and density of 937 kg/m 3 .
  • the split between the polymer produced in the loop reactor and the polymer produced in the gas phase reactor was 43/57.
  • Fibre samples of the invention comprising the multimodal LLDPE polymer material of the invention and the comparative test fibre samples were produced according to the procedure defined under "Fibre Sample Preparation” and tested for mechanical properties listed in Table 1 and Table 2 below and are further illustrated in figures 2 and 3.
  • Tensile tests The balance between tenacity and elongation was determined for two series of tape samples, i.e. for sample series stretched 5 times their original length and for sample series stretched 6 times their original length.
  • Abrasion Resistance i.e. abrasion resistance
  • Wear resistance i.e. abrasion resistance
  • abrasion resistance was determined as described above under Determination Methods using tape samples which had been stretched 6 times their original length (draw ratio of 1 :6).
  • 5 tape samples were subjected to a treatment of 60000 cycles, with a weight load of 12Og per tape. After 6000 cycles the test was stopped.
  • tapes were broken before the end of the treatment. The mechanical properties were reevaluated after the applied treatment.
  • Figure 3 shows the results of each 5 tape sample of the tested materials and number of cycles at fracture for any broken tapes.
  • Table 2 shows the tensile test results measured from test samples after the "weaving" test. The test shows that Fibres of the invention have very good wear resistance which is improved compared to prior art commercial fibres comprising higher density PE. Table 2. Residual tensile strength and elongation at break after treatment on the weaving simulator

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  • Chemical & Material Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • General Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Textile Engineering (AREA)
  • Artificial Filaments (AREA)
  • Compositions Of Macromolecular Compounds (AREA)

Abstract

La présente invention porte sur des fibres, des rubans ou des filaments comprenant une composition de polyéthylène multimodal, sur leur procédé de fabrication, sur l'utilisation d'une composition de polyéthylène multimodal, ainsi que sur des articles comprenant lesdites fibres, rubans ou filaments.
PCT/EP2008/002190 2007-03-22 2008-03-19 Fibres, rubans ou filaments comprenant une composition de polyéthylène multimodal WO2008113567A1 (fr)

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CN200880009377.6A CN101657572B (zh) 2007-03-22 2008-03-19 含有多峰聚乙烯组合物的纤维、带或丝
EP08716622.9A EP2137344B2 (fr) 2007-03-22 2008-03-19 Fibres, rubans ou filaments comprenant une composition de polyéthylène multimodal
AT08716622T ATE517201T1 (de) 2007-03-22 2008-03-19 Fasern, bänder oder filamente mit multimodaler polyethylenzusammensetzung

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EP07005908.4 2007-03-22
EP07005908A EP1972703A1 (fr) 2007-03-22 2007-03-22 Fibres, bandes ou filaments comportant une composition de polyéthylène multimodale

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WO2010075098A1 (fr) 2008-12-15 2010-07-01 Textile Management Associates, Inc. Procédé de recyclage de gazon synthétique et produit de remplissage
PL2563957T3 (pl) * 2010-04-30 2018-09-28 Basell Polyolefine Gmbh Polimerowy filament lub włókno
WO2012004422A1 (fr) 2010-07-06 2012-01-12 Dow Global Technologies Llc Mélanges de polymères d'éthylène et articles orientés à résistance améliorée à la contraction
US9200142B2 (en) 2013-09-23 2015-12-01 Milliken & Company Thermoplastic polymer composition
US9120914B2 (en) 2013-09-23 2015-09-01 Milliken & Company Thermoplastic polymer composition
US9200144B2 (en) 2013-09-23 2015-12-01 Milliken & Company Thermoplastic polymer composition
US9580575B2 (en) * 2013-09-23 2017-02-28 Milliken & Company Polyethylene articles
US9193845B2 (en) 2013-09-23 2015-11-24 Milliken & Company Thermoplastic polymer composition
CN105017625B (zh) * 2014-04-15 2017-07-14 中国石化扬子石油化工有限公司 一种乙烯‑α‑烯烃共聚物、其制造方法及其应用
BR112018010260B1 (pt) * 2015-12-10 2022-03-22 Dow Global Technologies Llc Fita, fibra ou monofilamento de polietileno, artigo de malha, artigo tecido
CN111745927B (zh) * 2020-06-30 2022-01-28 中国石油化工科技开发有限公司 一种高耐磨高润滑聚乙烯制品及其制备方法
CN114990719B (zh) * 2022-06-10 2023-06-20 湖北工业大学 一种用于人造草坪的纤维丝及其制备方法

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CN101657572B (zh) 2014-05-14
EP1972703A1 (fr) 2008-09-24
ATE517201T1 (de) 2011-08-15
EP2137344B1 (fr) 2011-07-20
EP2137344A1 (fr) 2009-12-30
CN101657572A (zh) 2010-02-24
EP2137344B2 (fr) 2015-03-04

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