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    • 专利摘要:
    low density ethylene based compositions with improved melt resistance, production and mechanical properties the invention provides a composition comprising: a) a first ethylene based polymer, formed by high pressure free radical polymerization process, and which comprises the following properties: a) an mw (abs) / mw (cpg) <2.2; and b) an ms versus i2 ratio: ms (greater than equal) cx [(i2) d], where c = 13.5 cn / (dg / min.) ded = -0.55, c) a melting index ( i2) from 0.1 to 0.9 g / 10 min .; and b) a second ethylene-based polymer; and wherein the second ethylene-based polymer has a melt index (i2) of 0.1 to 4.0 g / 10 min.
    公开号:BR112015027849B1
    申请号:R112015027849-3
    申请日:2014-05-21
    公开日:2020-08-18
    发明作者:Teresa P. Karjala；Cornelis F. J. Den Doelder；Otto J. Berbee；Lori L. Kardos
    申请人:Dow Global Technologies Llc；
    IPC主号:
    专利说明:

    Cross-referencing related orders
    [0001] This application claims the benefit of US Provisional Application 61 / 826,271, filed on May 22, 2013. Foundations
    [0002] Blown film production lines are typically limited in production due to bubble stability. Mixing Linear Low Density Polyethylene (LLDPE) with Low Density Polyethylene (LDPE) increases bubble stability, in part due to the greater resistance to LDPE fusion. The increase in melt resistance, in part, provides an increase in film production. However, very high melt resistance, especially as with wide molecular weight distribution (MWD), autoclave LDPEs with fractional melt indexes, can generate gels, limiting the reduction capacity, which can result in poor quality films . In addition, LDPE resins with high melt resistance generally have reduced optics. Thus, there is a need for new compositions that contain ethylene-based polymers, such as tubular LDPEs, that have an optimized balance of melt resistance, optical and mechanical properties, for blown film applications.
    [0003] Linear Low Density Polyethylene (LLDPE) is typically more difficult to process in a blown film line with generally less bubble stability, or lower maximum production (mass / time as pounds per hour) than Low Density Polyethylene ( LDPE). Films prepared with Linear Low Density Polyethylene (LLDPE), however, generally have better film mechanical properties than those produced with low density polyethylene (LDPE). Film processing and film properties are largely improved for blown films by mixing Linear Low Density Polyethylene (LLDPE) with Low Density Polyethylene (LDPE). Mixing in smaller amounts of LDPE and LLDPE usually leads to better processing compared to pure LLDPE, better optical properties and acceptable mechanical properties. Mixing high amounts of LDPE in LLDPE improves further processing and allows a thick film of a very large bubble diameter to be produced, while the mechanical and optical properties of the film are maintained or improved over the film made from pure LDPE. LDPE-rich films are also particularly suitable for shrinking films, such as bonding films, where LDPE provides good shrinkage behavior that cannot be achieved by using an LLDPE alone. In summary, the LDPE blend component typically contributes to the processability, optical properties, and shrink performance, while the LLDPE blend component contributes to mechanical properties.
    [0004] There is a need for new compositions that can increase melt strength and processing performance over conventional LDPE / LLDPE mixtures, and that can be carried out at low costs of conversion in a tubular process. In addition, there is a need for LDPE / LLDPE compositions with better processing performance (maximum line speed and / or operation of large bubbles) and / or film properties (mechanical and shrink performance and / or optical appearance).
    [0005] Low density polyethylene and mixtures are disclosed in the following: US Publication 2014/0094583; US patent 5,741,861; US patent 7,741,415; US Patent 4,511,609; US patent 4,705,829; US Publication 2008/0038533; JP61-241339 (Abstract); JP2005-232227 (Abstract); and International Publication Nos. WO 2010/144784, WO 2011/019563, WO 2010/042390, WO 2010/144784, WO 2011/019563, WO 2012/082393, WO 2006/049783, WO 2009/114661, US 2008/0125553, EP 0792318A1 and EP 2239283B1 . However, such polymers do not provide an optimized balance of high melt strength and improved mechanical properties of the film, for blown film applications. Thus, as discussed above, there remains a need for new ethylene-based polymer compositions that have an optimized balance of melt strength, optics, processability and production, and good shrinkage. These and other needs were met by the following invention. Summary of the invention
    [0006] The invention provides a composition comprising the following: A) a first polymer based on ethylene, formed by the polymerization process of high pressure free radicals, and comprising the following properties: a) a Mw (abs) / Mw ( CPG) <2.2; and b) an MS versus 12 ratio: MS C x [(12) D], where C = 13.5 cN / (dg / min) D and D = -0.55, c) a melting index (12) of 0.1 to 0.9 g / 10 min; and B) a second ethylene-based polymer; and wherein the second ethylene-based polymer has a melt index (12) of 0.1 to 4.0 g / 10 min Brief description of the drawings
    [0007] Figures 1A and IB are schematic diagrams of polymerization flow schemes. Figure IA represents a general flow diagram. Figure 1B provides more details of the discharge from the primary compressor system.
    [0008] Figure 2 represents the maximum production in the blown film line described here in relation to the% LDPE in LLDPE1 used in the film.
    [0009] Figure 3 represents the MD shrinkage stress measured on a film made at the standard rate versus the% LDPE in LLDPE1 used in the film.
    [0010] Figure 4 represents the melt strength measured in mixtures versus the% LDPE in LLDPE1. Detailed Description
    [0011] As discussed above, the invention provides a composition comprising the following: A) a first polymer based on ethylene, formed by the polymerization process of high pressure free radicals, comprising the following properties: a) a Mw (abs) / Mw (GPC) <2.2; and b) an MS versus 12 ratio: MS C x [(12) D], where C = 13.5 cN / (dg / min) D and D = -0.55, c) a melting index (12) of 0.1 to 0.9 g / 10 min; and B) a second ethylene-based polymer; and wherein the second ethylene-based polymer has a melt index (12) of 0.1 to 4.0 g / 10 min
    [0012] The composition may comprise a combination of two or more modalities described herein.
    [0013] In characteristic a) above, Mw (abs) and Mw (GPC) are each determined by method GPC A as described here.
    [0014] In characteristic b) above, the melt strength (MS) is determined at 190 ° C; see test method described here.
    [0015] In one embodiment, the composition has a density of 0.910 to 0.999 g / cm3, still from 0.915 to 0.922 g / cm3.
    [0016] In one embodiment, the composition has a melting index (12) of 0.1 to 1.5 g / 10 min, still 0.2 to 1.0 g / 10 min, and still 0.3 at 0.9 g / 10 min.
    [0017] In one embodiment, the composition has a melting resistance (190 ° C) of 5 to 40 cN, still 10 to 40 cN, still 20 to 40 cN, still 15 to 40 cN.
    [0018] In one embodiment, when a composition of the invention is formed into a film, by means of a blown film process, the maximum production rate is at least 15 percent higher than the maximum production rate of a similar film formed from a similar composition, except that the composition contains 100 weight percent of the second ethylene-based polymer, based on the total weight of the first ethylene-based polymer and the second ethylene-based polymer.
    [0019] In one embodiment, the second ethylene-based polymer has a melting index (12) of 0.2 to 3.5 g / 10 min, still 0.3 to 3.0 g / 10 min, still from 0.4 to 2.5 g / 10 min.
    [0020] In one embodiment, the second ethylene-based polymer has a density of 0.870 to 0.969 g / cm3, still from 0.890 to 0. 950 g / cm3, still from 0.910 to 0. 940 g / cm3, still from 0.915 to 0.930 g / cm3.
    [0021] In one embodiment, the second ethylene-based polymer is present in an amount of 5 to 95 percent by weight, still 10 to 95 percent by weight, still 20 to 95 percent by weight, still of 30 to 95 weight percent, based on the weight of the composition.
    [0022] In one embodiment, the second ethylene-based polymer is present in an amount of 40 to 95 percent by weight, still 50 to 95 percent by weight, still 60 to 95 percent by weight, still of 70 to 95 weight percent, based on the weight of the composition.
    [0023] In one embodiment, the second ethylene-based polymer is an ethylene / α-olefin interpolymer, as well as a copolymer. In an additional embodiment, the ethylene / α-olefin interpolymer is a heterogeneously branched ethylene / α-olefin interpolymer, and a copolymer. Suitable alpha olefins include, but are not limited to, propylene, butene-1, pentene-1, 4-methylpentene-1, pentene-1, hexene-1 and octene-1, and preferably propylene, butene-1, hexene-1 and octene -1.
    [0024] In one embodiment, the second ethylene-based polymer is selected from an ethylene / alpha-olefin copolymer, a low density polyethylene (LDPE), a high density polyethylene (HDPE), or a combination thereof.
    [0025] The second ethylene-based polymer can comprise a combination of two or more modalities, as described herein.
    [0026] In one embodiment, the first ethylene-based polymer is present in an amount of "greater than zero" at 30 percent by weight, still 1 to 25 percent by weight, still 2 to 20 percent by weight, based on the sum of the weight of the first ethylene-based polymer and the second ethylene-based polymer.
    [0027] In one embodiment, the first ethylene-based polymer is present in an amount greater than or equal to 20 percent by weight, still greater than or equal to 50 percent by weight, based on the sum of the weight of the first polymer to ethylene-based and the second ethylene-based polymer.
    [0028] In one embodiment, the first ethylene-based polymer is present in an amount of 1 to 95 percent by weight, still 5 to 95 percent by weight, still 10 to 90 percent by weight, based in the weight of the first ethylene-based polymer and the second ethylene-based polymer.
    [0029] In one embodiment, the first ethylene-based polymer has a melting index (12) of 0.2 g / 10 min at 0.9 g / 10 min, still 0.3 g / 10 min at 0 , 9 g / 10 min (ASTM 2.16 kg / 190 ° C).
    [0030] In one embodiment, the first ethylene-based polymer has b) a Mw (abs) versus 12 ratio: Mw (abs) <A x [(12) B], where A = 5, 00 x 102 (kg / mole) / (dg / min) B and B = -0.40 (Mw (abs) by GPC method A).
    [0031] In one embodiment, the first ethylene-based polymer has b) a Mw (abs) versus 12 ratio: Mw (abs) <A x [(12) B], where A = 4.25 x 102 (kg / mole) / (dg / min) B and B = -0.40 (Mw (abs) by GPC method A).
    [0032] In one embodiment, the first ethylene-based polymer has c) an MS versus 12 ratio: MS C x [(I2) D], where C = 14.5 cN / (dg / min) D and D = -0.55 (melt strength = MS, 190 ° C).
    [0033] In one embodiment, the first ethylene-based polymer has c) an MS versus 12 MS ratio: MS C x [(I2) D], where C = 15.5 cN / (dg / min) D and D = -0.55 (melt strength = MS, 190 ° C).
    [0034] In one embodiment, the first ethylene-based polymer has a melt resistance greater than or equal to, 9.0 cN, at 190 ° C, even greater than or equal to 12.0 cN, at 190 ° C, still greater than or equal to 15.0 cN, at 190 ° C.
    [0035] In one embodiment, the first ethylene-based polymer has a melting resistance (190 ° C) of 10 to 40 cN, still 15 to 30 cN.
    [0036] In one embodiment, the first ethylene-based polymer has a "molecular weight (w) fraction greater than 106 g / mole, based on the total polymer weight, as determined by GPC (abs), which satisfies the following relationship: w <E x [(I2) F], where E = 0.110 (dg / min) "F and F = -0.38 (Method GPC A).
    [0037] In one embodiment, the first ethylene-based polymer is polymerized in at least one tubular reactor. In another embodiment, the first ethylene-based polymer is polymerized in a tubular reactor system that does not comprise an autoclave reactor.
    [0038] In one embodiment, the first ethylene-based polymer is selected from a polyethylene homopolymer or an ethylene-based interpolymer.
    [0039] In one embodiment, the first ethylene-based polymer is selected from a polyethylene homopolymer or an ethylene-based copolymer; and wherein the comonomer of the ethylene-based copolymer is selected from a vinyl acetate, an alkyl acrylate, carbon monoxide, an acrylic acid, a comonomer containing carboxylic acid, an ionomer, a mono-olefin, or selected from an acetate vinyl, an alkyl acrylate, acrylic acid, or a mono-olefin. In another embodiment, the comonomer is present in an amount of 0.5 to 30% by weight of the comonomer, based on the weight of the copolymer.
    [0040] In one embodiment, the first polymer based on ethylene is an LDPE.
    [0041] In one embodiment, the first ethylene-based polymer has a density of 0.910 to 0.940 g / cm3.
    [0042] In one embodiment, the first ethylene-based polymer has a density greater than or equal to 0.912 g / cm3, or greater than or equal to 0.915 g / cm3, or greater than or equal to 0.916 g / cm3 cm3.
    [0043] In one embodiment, the first ethylene-based polymer has a density less than or equal to 0.935 g / cm3, or less than or equal to 0.930 g / cm3, or less than or equal to 0.925 g / cm3, or less than or equal to 0.920 g / cm3.
    [0044] The first ethylene-based polymer can comprise a combination of two or more modalities, as described herein.
    [0045] A composition of the invention can comprise a combination of two or more modalities, as described herein.
    [0046] The invention also provides an article comprising at least one component formed from a composition of the invention.
    [0047] In one embodiment, the article is selected from coatings, films, foams, laminates, fibers or tapes. In another modality, the article is a film.
    [0048] The invention also provides a film comprising at least one layer formed from a composition of the invention.
    [0049] In one embodiment, the film comprises at least two layers.
    [0050] In one embodiment, the film has an MD shrinkage tension greater than 0.0207 MPa (3.00 psi).
    [0051] An article of the invention may comprise a combination of two or more embodiments, as described herein.
    [0052] A film of the invention may comprise a combination of two or more modalities, as described herein. Polymerizations
    [0053] For a polymerization process initiated by high pressure free radical, two basic types of reactors are known. The first type is a stirred autoclave container with one or more reaction zones (the autoclave reactor). The second type is a jacketed tube, which has one or more reaction zones (the tubular reactor). The pressure in each autoclave and zone of the process tubular reactor is typically 100 to 400, more typically 120 to 360, and even more typically 150 to 320 MPa. The polymerization temperature in each zone of the process tubular reactor is typically 100 to 400 ° C, more typically 130 to 360 ° C, and even more typically 140 to 330 ° C.
    [0054] The polymerization temperature in each zone of the process autoclave reactor is typically 150 to 300 ° C, more typically 165 to 290 ° C, and even more typically 180 to 280 ° C.
    [0055] The high pressure process of the present invention to produce homo polyethylene or interpolymers, having the advantageous properties, as found in accordance with the invention, is preferably performed in a tubular reactor that has at least three reaction zones.
    [0056] The first ethylene-based polymers with a wide MWD are normally made under polymerization conditions comprising one or more of the following process elements: • Reduced operating pressure (versus maximum operating pressure of the reactor system). • High polymerization temperatures: one or more autoclave zones and / or one or more zones of the tubular reactor are operated at a maximum control or peak temperature exceeding 240 and 290 ° C respectively. • At least three autoclave and / or tubular reaction zones. • Selection of the type and / or distribution of the CTA over the reaction zones to guarantee a wide MWD product. • Optional use of a bifunctional coupling and / or branching agent. Initiators
    [0057] The first ethylene-based polymer is formed by a polymerization process of free radicals. The type of free radical initiator to be used in the present process is not critical, but preferably one of the initiators used should allow high temperature operation in the range of 300 ° C to 350 ° C. Free radical initiators that are commonly used include organic peroxides such as peresters, percetals, peroxide ketones, percarbonates, and multifunctional cyclic peroxides. These organic peroxy initiators are used in conventional amounts, typically from 0.005 to 0.2% by weight based on the weight of polymerizable monomers. Other suitable initiators include azodicarboxylic esters, azodicarboxylic dinitriles and derivatives of 1,1,2,2-tetramethylethane, and other components, capable of forming free radicals in the desired operating temperature range. Peroxides are usually injected as solutions diluted in a suitable solvent, for example, in a hydrocarbon solvent.
    [0058] In one embodiment, an initiator is added to at least one polymerization reaction zone, and in which the initiator has a "half-life temperature in one second" greater than 255 ° C, preferably greater than than 260 ° C. In another embodiment, such initiators are used at a peak polymerization temperature of 320 ° C to 350 ° C. In another embodiment, the initiator comprises at least one peroxide group incorporated in a ring structure.
    [0059] Examples of such initiators include, among others, TRIGONOX 301 (3,6,9-triethyl-3,6,9-trimethyl-1, 4,7-triperoxonane) and TRIGONOX 311 (3,3,5,7 , 7-pentamethyl-1,2,4-trioxepano), both available from Akzo Nobel, and HMCH-4-AL (3,3,6,6,9,9-hexamethyl-1,2,4,5-tetroxonane ) available from United Initiators. See also International Publications Nos. WO 02/14379 and WO 01/68723. Chain transfer agents (CTA)
    [0060] Linear chain transfer agents or telogens are used to control the melt index in a polymerization process. Chain transfer involves terminating growing polymer chains, thereby limiting the final molecular weight of the polymer material. Chain transfer agents are usually hydrogen atom donors that react with a growing polymer chain and stop the chain polymerization reaction. These agents can be of many different types, from saturated or unsaturated hydrocarbons to aldehydes, ketones or alcohols. By controlling the concentration of the selected chain transfer agent, one can control the length of polymer chains, and therefore the molecular weight, for example, the average molecular weight in number, Mn. The melt flow index (MFI or I2) of a polymer, which is related to Mn, is controlled in the same way.
    The chain transfer agents used in the process of the present invention include, but are not limited to, aliphatic and olefinic hydrocarbons, such as pentane, hexane, cyclohexane, propene, pentene or hexane; ketones, such as acetone, diethyl ketone or diamyl ketone; aldehydes such as formaldehyde or acetaldehyde; and aliphatic alcohols of saturated aldehydes, such as methanol, ethanol, propanol or butanol. The chain transfer agent can also be a monomeric chain transfer agent. For example, see WO 2012/057975, US 61/579067 and US 61/664956.
    [0062] Differentiated CTA concentrations in the reaction zones can be used to achieve and to control the desired molecular weight distribution. Means for differentiating the CTA concentration in reaction zones include, among others, methods described in W02013 / 059042, WO2011 / 075465 and W02012 / 044504.
    [0063] Another way to influence the fusion index includes the elaboration and control, in ethylene recycling currents, of incoming ethylene impurities, such as methane and ethane, peroxide dissociation products, such as tert-butanol, acetone , etc., and or solvent components used to dilute the initiators. These ethylene impurities, peroxide dissociation products and / or diluting solvent components can act as chain transfer agents. Monomers and comonomers
    [0064] The term ethylene interpolymer as used in the present description and in the claims refers to ethylene polymers and one or more comonomers. Comonomers suitable for use in the ethylene polymers of the present invention include, but are not limited to, ethylenically unsaturated monomers and, especially, C3-20 alpha-olefins, carbon monoxide, vinyl acetate, alkyl acrylate, or a bifunctional or higher functional comonomer (includes monomers with two or more monomeric groups). Usually comonomers can also act as chain transfer agents to some degree. These comonomers with high chain transfer activity are referred to as monomeric CTA. Additions
    [0065] A composition of the invention may further comprise one or more additives. Suitable additives include, among others, stabilizers; fillers, such as organic or inorganic particles, including clays, talc, titanium dioxide, zeolites, powdered metals, organic or inorganic fibers, including carbon fibers, silicon nitride fibers, steel or mesh wire, and strands of nylon or polyester, nanometric particles, clays, and so on; thickeners; and diluents, including paraffinic or naphthalenic oils. A composition of the invention can comprise other types of polymers. applications
    [0066] The polymers of the present invention can be employed in a variety of conventional thermoplastic manufacturing processes to produce useful articles, including, but not limited to, monolayer and multilayer films; molded articles, such as blow molded, injection molded, or rotational molded articles; coatings; fibers; and woven or non-woven fabric.
    [0067] A polymer of the invention can be used in a variety of films, including but not limited to extrusion coating, food packaging, consumer, industrial, agricultural (applications or films), laminating films, films that produce fresh cuts, films for meat, films for cheese, films for sweets, reducing films for whitening, reducing films for bonding, stretch films, silage films, greenhouse films, fumigation films, liner films, stretching covers, heavy transport bags , pet food, sandwich bags, sealants and diaper back sheets.
    [0068] A polymer of the invention is also useful in other applications for direct end use. A polymer of the invention can be used for wire and cable coating operations, in sheet extrusion for vacuum forming operations, and forming molded articles, including the use of injection molding, blow molding processes or processes rotational molding.
    [0069] Other suitable applications for the polymers of the invention include films and elastic fibers; soft-touch products, such as device handles; joints and cutouts; interior parts of records and clippings; foam products (both open and closed cells); impact modifiers for other thermoplastic polymers, such as high density polyethylene, or other olefin polymers; cover coatings; and floors. Definitions
    [0070] Unless otherwise stated, implied from context, or customary in the art, all parts and percentages are based on weight, and all test methods are current up to the filing date of this disclosure.
    [0071] The term "composition", as used herein, refers to a mixture of materials comprising the composition, as well as reaction products and decomposition products formed from the materials of the composition.
    [0072] The terms "mixture" or "mixture of polymers", as used, means an intimate physical mixture (i.e., without reaction) of two or more polymers. A mixture can be miscible or not (not separated into phases at the molecular level). The mixture may or may not be separated into phases. A mixture may or may not contain one or more domain configurations, as determined by transmission electronic spectroscopy, light scattering, X-ray scattering, and other methods known in the art. The mixing can be carried out by physically mixing the two or more polymers at the macro level (for example, melting mixed or manipulated resins) or at the micro level (for example, simultaneous formation in the same reactor, or formation of a polymer in the presence of another polymer).
    [0073] The term "polymer" refers to a compound prepared by polymerizing monomers, of the same or a different type. The generic term polymer thus encompasses the term homopolymer (which refers to polymers prepared from only one type of monomer, with the understanding that trace amounts of impurities can be incorporated into the polymer structure), and the term "interpolymer", as defined below. Trace amounts of impurities can be incorporated into and / or within a polymer.
    [0074] The term "interpolymer" refers to polymers prepared by the polymerization of at least two different types of monomers. The generic term interpolymer includes copolymers (which refers to polymers prepared from two different monomers), and polymers prepared from more than two different types of monomers.
    [0075] The term "ethylene-based polymer" or "ethylene polymer" refers to a polymer that comprises a major amount of ethylene polymerized based on the weight of the polymer and, optionally, can comprise at least one comonomer.
    [0076] The term "ethylene-based interpolymer" or "ethylene-interpolymer" refers to an interpolymer comprising a major amount of ethylene polymerized based on the weight of the interpolymer and comprises at least one comonomer.
    [0077] The term "ethylene-based copolymer" or "ethylene copolymer" refers to a copolymer comprising a major amount of ethylene polymerized based on the weight of the copolymer, and only one comonomer (thus, only two types of monomers).
    [0078] The terms "autoclave-based products" or "autoclave-based polymers", as used herein, refer to polymers prepared in a reactor system comprising at least one autoclave reactor.
    [0079] The term "high pressure free radical polymerization process" as used herein refers to a polymerization initiated by free radical, carried out at an elevated pressure of at least 100 MPa (1000 bar).
    [0080] The terms "comprising", "including", "having", and their derivatives, are not intended to exclude the presence of any additional component, step or process, whether or not it is specifically disclosed. For the avoidance of doubt, all compositions claimed through the use of the term "comprising" may include any additional additives, adjuvants, or compounds, whether polymeric or otherwise, unless otherwise indicated. In contrast, the term "consisting essentially of" excludes from its scope any mention following any other component, step or procedure, with the exception of those that are not essential for operability. The term "consisting of" excludes any component, step or procedure not specifically outlined or listed. Testing methods
    [0081] Density: Samples for density measurement are prepared according to ASTM D 1928. Polymer samples are pressed at 190 ° C and 207 MPa (30,000 psi) for three minutes, and then at 21 ° C and 207 MPa for one minute. Measurements are made within one hour of the pressed sample using ASTM D792, Method B.
    [0082] Melting index: melting index, or 12 = I2, (grams / 10 minutes or dg / min) is measured according to ASTM D 1238, Condition 190 ° C / 2.16 kg. MethodA: Permeation Chromatography on Gel with Triple Detector (TDGPC):
    [0083] High temperature 3Det-GPC analysis is performed on an ALLIANCE GPCV2000 instrument (Waters Corp.), set at 145 ° C. The flow rate for GPC is 1 mL / min The injection volume is 218.5 | 1L. The column set consists of four Mixed-A columns (20 pm particles; 7.5 X 300 mm; Polymer Laboratories Ltd).
    [0084] Detection can be achieved by using a PolymerChAR IR4 detector, equipped with a CH- sensor; a Wyatt Technology Dawn DSP MALS detector (Wyatt Technology Corp., Santa Barbara, CA, USA), equipped with a 30 mW argon ion laser operating at X = 488 nm; and a Waters tricapillary viscosity detector. The MALS detector is calibrated by measuring the dispersion intensity of the TCB solvent. The normalization of photodiodes is done by injection of SRM 1483, a high density polyethylene with an average molecular weight by weight (Mw) of 32,100 g / mol and polydispersity (MWD) of 1.11. A specific increment of refractive index (dn / dc) of -0.104 ml / mg, for polyethylene in TCB, is used.
    [0085] The conventional GPC calibration is done with 20 narrow PS standards (Polymer Laboratories Ltd.) with molecular weights in the range of 580 to 7,500,000 g / mol. The standard peak molecular weights of polystyrene are converted to molecular weights of polyethylene from the following equation:
    r with A = 0.39, B = 1. The value of A is determined using a linear high density polyethylene (HDPE) homopolymer with Mw of 115,000 g / mol. The HDPE reference material is also used to calibrate the IR detector and viscometer assuming 100% mass recovery and an intrinsic viscosity of 1,873 dL / g.
    [0086] The column calibration curve was obtained by adjusting a first order polynomial for the respective polyethylene equivalent calibration points obtained from the above equation, for the observed elution volumes.
    [0087] Numerical, weight and average Z molecular weights (GPC) were calculated according to the following equations:
    where, Wf ± is the weight fraction of the 1st component and M ± is the molecular weight of the 1st component. The molecular weight distribution (MWD) was expressed as the ratio of the weight average molecular weight (Mw) to the numerical average molecular weight (Mn).
    [0088] Grade "Baker Analyzed" 1,2,4-trichlorobenzene distillate (JT Baker, Deventer, Netherlands), containing 200 ppm 2,6-di-tert-butyl-4-methylphenol (Merck, Hohenbrunn, Germany ), is used as a solvent for sample preparation, as well as for the 3Det-GPC experiment. HDPE SRM 1483 is obtained from the US National Institute of Standards and Technology (Gaithersburg, MD, USA).
    [0089] LDPE solutions are prepared by dissolving the samples under gentle agitation for three hours at 160 ° C. The PS standards are dissolved under the same conditions for 30 minutes. The sample concentration for the 3Det-GPC experiment is 1.5 mg / mL, and the polystyrene concentrations are 0.2 mg / mL.
    [0090] A MALS detector measures the scattered signal of polymers or particles in a sample under different angles of dispersion θ. The basic light scattering equation (from M. Anderson, B. Wittgren, K.-G. Wahlund, Anal. Chem. 75, 4279 (2003)) can be written as follows:
    where Rθ is the excess Rayleigh ratio, K is an optical constant, which is, among other things, dependent on the increment of the specific shrinkage index (dn / dc), c is the concentration of the solute, M is the molecular weight, Rg is the radius of rotation and, A, is the wavelength of the incident light. The calculation of the molecular weight and the radius of rotation from the light scattering data require extrapolation to zero angle (see also PJ Wyatt, Anal. Chim. Acta 272, 1 (1993)). This is done from the graph (Kc / Rθ) 14 as a function of sin2 (θ / 2) in the so-called Debye graph. The molecular weight can be calculated from the intersection with the ordinate, and the radius of rotation of the initial slope of the curve. The second viral coefficient is considered insignificant. The intrinsic viscosity numbers are calculated from both signals from both the viscosity and concentration detector signals, taking the ratio between the specific viscosity and the concentration in each elution slice.
    [0091] The ASTRA 4.72 software (Wyatt Technology Corp.) is used to collect the signals from the IR detector, the viscometer, and the MALS detector, and to perform the calculations.
    [0092] Calculated molecular weights, for example, Mw (abs), and molecular weight distributions (for example, Mw (abs) / Mn (abs)) are obtained using a light scattering constant derived from one or more of the mentioned polyethylene standards and a refractive index concentration coefficient, dn / dc, of 0.104. Generally, the response of the mass detector and the light scattering constant should be determined from a linear pattern with a molecular weight greater than about 50,000 Daltons. Calibration of the viscometer can be performed using the methods described by the manufacturer, or alternatively, using the published values of suitable linear standards, such as reference standard materials (SRM) 1475a, 1482a, 1483, or 1484a. Chromatographic concentrations are assumed to be low enough to eliminate the targeting of the 2nd virial coefficient effects (concentration effects on molecular weight).
    [0093] The MWD (abs) curve obtained from TD-GPC is summarized with three characteristic parameters: Mw (abs), Mn (abs), ew, where w is defined as "fraction of molecular weight greater than 106 g / mole, based on the total polymer weight, and as determined by GPC (abs) ".
    [0094] In the form of an equation, the parameters are determined as follows. Numerical integration from the "logM" and "dw / dlogM" table is usually done with the trapezoidal rule:
    Method B: Permeation Chromatography on Triple Detector Gel (TDGPC) - Conventional GPC data
    [0095] A Triple Detector Gel Permeation Chromatography system (3D-GPC or TDGPC) consisting of a Model 220 high temperature chromatograph from Polymer Laboratories (now Agilent), equipped with a 2 laser light scattering detector angles (LS) Model 2040 (Precision Detectors, now Agilent), an IR-4 infrared detector from Polymer Char (Valencia, Spain), and a 4 capillary solution (DP) viscometer (Viscotek, now Malvern) were used. Data collection was performed using the Polymer Char 100 DM data acquisition box and related software (Valencia, Spain). The system was also equipped with an in-line solvent degassing device from Polymer Laboratories (now Agilent).
    [0096] High temperature GPC columns consisting of four 30 cm columns, 20 um Mixed A LS from Polymer Laboratories (now Agilent) were used. The sample carousel compartment was operated at 140 ° C, and the column compartment was operated at 150 ° C. The samples were prepared at a concentration of 0.1 grams of polymer in 50 milliliters of solvent. The chromatographic solvent and the sample preparation solvent were 1,2,4-trichlorobenzene (TCB) containing 200 ppm 2,6-di-tert-butyl-4methylphenol (BHT). The solvent was sparged with nitrogen. The polymer samples were gently stirred at 160 ° C for four hours. The injection volume was 200 microliters. The flow through the GPC was adjusted to 1.0 mL / minute.
    [0097] Column calibration and examples of molecular weight calculations were performed using Polymer Char "GPC One" software. The calibration of the GPC columns was performed with 21 polystyrene standards of narrow molecular weight distribution. The molecular weights of the polystyrene standards ranged from 580 to 8,400,000 g / mole, and were arranged in 6 "cocktail" mixtures, with at least a group of ten separating between the individual molecular weights.
    [0098] The peak molecular weights of polystyrene standards were converted to molecular weights of polyethylene from the following equation ('as described in Williams and Ward, J. Polym. Sci., Polym. Let, 6, 621 (1968) ):
    here B has a value of 1.0, and the value of A experimentally determined is about 0.38 to 0.44.
    [0099] The column calibration curve was obtained by adjusting a first order polynomial for the respective polyethylene equivalent calibration points obtained from the above equation, for the observed elution volumes.
    [0100] Number, weight and molecular weights of the mean -z were calculated according to the following equations:
    where, Wf ± is the weight fraction of the 1st component and M ± is the molecular weight of the 1st component. The molecular weight distribution (MWD) was expressed as the ratio between the weight average molecular weight (Mw) to the numerical average molecular weight (Mn).
    [0101] The value of A was determined by adjusting the value A in the Williams and Ward equation to Mw, the weight average molecular weight calculated using the above equation, and the corresponding retention volume polynomial was in accordance with the determined Mw value independently obtained according to the linear reference homopolymer with a known molecular weight of 115,000 g / mol. Fusion Resistance
    [0102] Fusion resistance (MS) measurements were performed on a Gõttfert Rheotens 71.97 (Gõttfert Inc .; Rock Hill, SC) connected to a Gõttfert Rheotester 2000 capillary rheometer. A molten polymer is extruded through a capillary matrix at an angle flat entrance (180 degrees) with a capillary diameter of 2.0 mm and an aspect ratio (capillary length / capillary diameter) of 15.
    [0103] After equilibrating the samples at 190 ° C for 10 minutes, the piston was activated at a constant piston speed of 0.265 mm / second. The standard test temperature was 190 ° C. The sample is taken uniaxially for a set of acceleration grips located 100 mm below the matrix, with an acceleration of 2.4 mm / second2. The tension force is recorded as a function of the pickup speed of the clamping rollers. Fusion strength is reported as the plateau strength (cN) before the cord breaks. The following conditions were used in the melt strength measurements: piston speed = 0.265 mm / second; wheel acceleration = 2.4 mm / s2; capillary diameter = 2.0 mm; capillary length = 30 mm; and cylinder diameter = 12 mm. Nuclear Magnetic Resonance (13C NMR)
    [0104] Samples were prepared by adding approximately "3 g of a 50/50 mixture of tetrachloroethane-d2 / orthodichlorobenzene, containing 0.025 M Cr (AcAc) 3" to a sample of "0.25 to 0.40 g of polymer "in a 10 mm NMR tube. Oxygen was removed from the sample by placing the tubes open in a nitrogen environment for at least 45 minutes. The samples were then homogenized and dissolved by heating the tube, and its contents to 150 ° C, using a heating block and heat gun. Each dissolved sample was visually inspected to ensure homogeneity. The samples were thoroughly mixed, immediately before analysis, and were not allowed to cool before insertion into the heated NMR sample holder.
    [0105] All data was collected using a 400 MHz Bruker spectrometer. Data were acquired using a six-second pulse repeat delay, 90 degree fin angles, and reverse door decoupling, with a sample temperature 125 ° C. All measurements were made on samples that did not rotate in locked mode. The samples were allowed to thermally equilibrate for seven minutes before data acquisition. The chemical shifts of 13C NMR were referenced internally for the EEE triad at 30.0 ppm. The C6 + value was a direct measure of C6 + branches in LDPE, where the long branches were not distinguished from the ends of the chain. The 32.2 ppm peak, which represents the third carbon from the end of all six or more carbon chains or branches, was used to determine the C6 + value. Nuclear magnetic resonance (1H NMR) Sample preparation
    [0106] Samples were prepared by adding approximately 130 mg of sample to "3.25 g 50/50 wt. Tetrachloroethane-d2 / perchlorethylene" with 0.001 M Cr (AcAc) 3 in a NORELL 1001- NMR tube 7, 10 mm. The samples were purged by bubbling N2 through the solvent, using a pipette inserted into the tube, for about five minutes, to avoid oxidation. Each tube was capped, sealed with TEFLON tape, and then soaked at room temperature, overnight, to facilitate sample dissolution. The samples were kept in an N2 purge box, during storage, before and after preparation, to minimize exposure to 02. The samples were heated and stirred at 115 ° C to ensure homogeneity. Data Acquisition Parameters
    [0107] 0 1H NMR was performed on a Bruker AVANCE 400 MHz spectrometer, equipped with a Bruker Dual DUL high temperature CryoProbe, and a sample temperature of 120 ° C. Two experiments were performed to obtain the spectra, a control spectrum to quantify the total polymer protons, and a double pre-saturation experiment, which suppressed the intense peaks of the polymer backbone, and allowed highly sensitive spectra for quantification terminal groups. Control was performed with ZG pulse, 4 scans, SWH 10,000 Hz, AQ 1, 64s, Dl 14s. The double pre-saturation experiment was performed with a modified pulse sequence, TD 32768, 100 scans, DS 4, SWH 10,000 Hz, AQ 1, 64s, Dl Is, D13 13s. Data Analysis - 1H NMR Calculations
    [0108] The residual 1H signal in the TCE-d2 (at 6.0 ppm) was integrated, and adjusted to a value of 100, and the integral from 3 to -0.5 ppm was used as the signal for the entire polymer in the control experiment. For the pre-saturation experiment, the TCE signal was also adjusted to 100, and the corresponding integrals for unsaturation (vinylene at about 5.40 to 5.60 ppm, tri-substituted at about 5.16 to 5.35 ppm , vinyl at about 4.95 to 5.15 ppm, and vinylidene at about 4.70 to 4.90 ppm) were obtained.
    [0109] In the spectrum of the pre-saturation experiment, the regions for cis and trans-vinylene, tri-substituted, vinyl and vinylidene were integrated. The integral of the whole polymer from the control experiment was divided by two to obtain a value that represents X thousands of carbon atoms (that is, if the integral of the polymer = 28000, this represents 14,000 carbon atoms, and X = 14).
    [0110] The integrals of unsaturated group, divided by the corresponding number of protons that contribute to the integral, represent the moles of each type of unsaturation per X thousand carbons. Dividing the moles of each type of unsaturation by X, then generates moles of unsaturated groups by 1000 moles of carbon atoms. Film Test
    [0111] The following physical properties were measured on the films as described in the experimental section. The film thickness was measured using a Measuretech instrument.
    [0112] Total opacity (general) and Internal opacity: Internal opacity and total opacity were measured according to ASTM D 1003-07. Internal opacity was obtained through the corresponding refractive index using mineral oil (1-2 teaspoons), which was applied as a coating on each surface of the film. A Hazegard Plus (BYK-Gardner USA; Columbia, MD) was used for the test. For each test, samples of five were examined, and a reported average. Sample dimensions were "15.2 cm x 15.2 cm (6 in. X 6 in.)".
    [0113] 45 ° brightness: ASTM D 2457-08 (average of five film samples; each sample "25.4 cm x 24.5 cm (10 in. X 10 in.)").
    [0114] Clarity: ASTM D 1746-09 (average of five film samples; each sample "25.4 cm x 24.5 cm (10 in. X 10 in.)").
    [0115] Secante Module 2% - MD (machine direction) and CD (cross direction): ASTM D 882-10 (average of five film samples in each direction; each sample "2.5 cm x 15.2 cm ( 1 in. X 6 in.) ").
    [0116] Elmendorf MD and CD breaking strength: ASTM D 1922-09 (average of 15 film samples in each direction; each sample "7.6 cm x 6.4 cm (3 in. X 2.5 in.)) "half moon shape).
    [0117] MD and CD Tensile Strength: ASTM D 882-10 (average of five film samples in each direction; each sample "2.5 cm x 15.2 cm (1 in. X 6 in.)").
    [0118] Dart Impact Resistance: ASTM D 1709-09 (minimum of 20 drops to achieve 50% failure, typically ten strips "25.4 cm x 91.4 cm (10 in. X 36 in.)" .
    [0119] Puncture resistance: Perforation was measured on an INSTRON Model 4201 with SINTECH SOFTWARE TESTWORKS version 3.10. The sample size was "15.2 cm x 15.2 cm (6 in. X 6 in.)", And four measurements were taken to determine an average perforation value. The film was conditioned for 40 hours after the film was produced, and at least 24 hours in a controlled ASTM laboratory (23 ° C and 50% relative humidity). The "45.4 kg (100 lb)" load cell was used with a round 10.15 cm (4 inch) diameter sample holder. The drill rig is a polished stainless steel ball "1.3 cm in diameter) in diameter" (on a 6.4 cm (2.5 ") rod) with a" maximum travel length of 19.1 cm (7.5 inches) ".
    [0120] There was no gauge length, and the probe was as close as possible, but not touching, the specimen. The probe was adjusted by increasing the probe until it touched the specimen. Then, the probe was gradually reduced, until it did not touch the specimen. Then, the crosshead was set to zero. Considering the maximum travel distance, the distance would be approximately 0.3 cm (0.10 inch). The crosshead speed was 25.4 cm / min (10 inches / minute). The thickness was measured in the middle of the specimen. The thickness of the film, the distance traveled from the crosshead, and the peak load were used to determine the perforation by the software. The drilling rig was made using a "KIM-WIPE" after each specimen.
    [0121] Retraction stress: retraction stress was measured according to the method described in Y. Jin, T. Hermel-Davidock, T. Karjala, M. Demirors, J. Wang, E. Leyva, and D. Allen, "Shrink Force Measurement of Low Shrink Force Films", SPE ANTEC Proceedings, p. 1264 (2008). The shrinkage resistance of film samples was measured using a temperature rise test that was performed on an RSA-III Dynamic Mechanical analyzer (TA Instruments, New Castle, DE) with a film fastener. Film specimens of "1.27 cm wide" and "6.35 cm long" were cut in a matrix from the film sample, in the machine direction (MD) or in the transverse direction (CD), for testing . The film thickness was measured by a Mitutoyo Absolute digital indicator (Model C112CEXB). This indicator had a maximum measurement range of 1.27 mm, with a resolution of 0.01 cm. The average of three thickness measurements, at different locations on each film specimen, and the width of the specimen, was used to calculate the cross section film area (A), where "A = width x thickness" of the specimen film that was used in shrink film tests. A standard TA Instruments film tensioner was used for the measurement. The RSA-III oven was equilibrated at 25 ° C for at least 30 minutes, before zeroing the gap and axial force. The initial gap was adjusted to 2 cm.
    [0122] The film specimen was then attached at both the top and bottom. Typically, measurements for MD require only one-fold film. Since the retraction voltage in the CD direction is normally low, two or four layers of film are stacked together for each measurement to improve the signal-to-noise ratio. In such a case, the thickness of the film is the sum of all layers. In this work, a single layer was used in the MD direction and two layers were used in the CD direction. After the film reached the initial temperature of 25 ° C, the upper fixation was raised or lowered manually slightly to obtain an axial force of -1.0 g. This was to ensure that no deformation or excessive stretching of the film occurred at the beginning of the test. Then the test started. A constant fixation gap was maintained throughout the measurement.
    [0123] The temperature ramp started at a rate of 90 ° C / min, from 25 ° C to 80 ° C, followed by a rate of 20 ° C / min, from 80 ° C to 160 ° C . During the ramp from 80 ° C to 160 ° C, as the film shrunk, the retraction force, measured by the force transducer, was recorded as a function of temperature, for later analysis. The difference between the "peak force" and the "baseline value before the start of the peak shrinkage force" is considered the retraction force (F) of the film. The film's shrinkage stress is the ratio of the shrinkage force (F) to the initial cross-sectional area (A) of the film.
    [0124] For the MD retraction stress, three film samples were tested, and a reported average.
    [0125] For the CD retraction tension, three film samples were tested, and a reported average. Experimental First ethylene-based polymers
    [0126] IE1: The polymerization was carried out in a tubular reactor with three reaction zones. In each reaction zone, pressurized water was used for cooling and / or heating the reaction medium, circulating this water through the reactor jacket. The inlet pressure was 2100 bar, and the pressure drop across the entire tubular reactor system was around 30 MPa (300 bar). Each reaction zone had an entrance and an exit. Each input stream consisted of the output stream from the previous reaction zone and / or an ethylene rich feed stream added. Ethylene was supplied according to a specification, which allowed a trace amount (maximum of 5 mol ppm) of acetylene in ethylene. Unconverted ethylene, and other gaseous components at the reactor outlet, were recycled through a low-pressure and a high-pressure recycling system and were compressed and distributed through a booster compressor system, a primary and a hypercompressor ( secondary), according to the flow diagram shown in Figure 1B. As seen in Figure 1B, both discharge currents (2 and 3) from the primary compressor were sent to the supply current of the reactor 5.
    [0127] Organic peroxides were fed to each reaction zone (see Table 1). Propionaldehyde (PA) was used as a chain transfer agent, and was present at each reaction zone entrance, coming from low pressure and high pressure recycling flows (13 and 15), as well as from chain 7 and / or chains mounted on newly injected CTA. The polymer was prepared at a melting index of 0.58g / 10 min
    [0128] After reaching the first peak temperature (maximum temperature) in reaction zone 1, the reaction medium was cooled with the help of pressurized water. Upon leaving reaction zone 1, the reaction medium was then cooled by injecting a fresh, cold, ethylene-rich feed stream (20), and the reaction was restarted by feedback from an organic peroxide. This process was repeated at the end of the second reaction zone, to allow additional polymerization in the third reaction zone. The polymer was extruded and pelletized (about 30 pellets per gram), using a "single screw" extrusion system at a melting temperature around 230-250 ° C. The weight ratio of the ethylene-rich feed streams (9:20:21) for the three reaction zones was 1.00: 0.76: 0.24. The values of R2 and R3 each approached infinity. R values are calculated in accordance with International Publication WO 2013/059042 (International Patent Application PCT / US 12/059469 filed October 10, 2012). Rn (n = reaction zone number, n> l) is the ratio of the "mass fraction of fresh ethylene fed to the first reaction zone (RZ1)" to "mass fraction of fresh ethylene fed to the in the reaction zone reaction (RZn) "is (Rn = RZl / RZn). The internal process speed was about 12.5, 9 and 11 m / s, respectively, for the first, second and third reaction zones. In this example of the invention, the weight ratio of the assembled CTA chains 7 and 6 was 2. Additional information can be found in Tables 2 and 3. Example IE2
    [0129] Polymerization was carried out in a tubular reactor with three reaction zones, as discussed above for IE1 (see Figure 1B). The weight ratio of the ethylene-rich feed streams (9:20:21) for the three reaction zones was 1.00: 0.76: 0.24 The polymer was prepared at a melt index of 0.37 g / 10 min. Each of the values of R2 and R3 reached approached infinity (∞). In this example of the invention, the weight ratio of CTA-mounted chains 7 and 6 was 1.35. Additional information can be found in Tables 2 and 3. The CTA was propionaldehyde (PA).
    [0130] In summary, in order to achieve tubular resins with high melt resistance, suitable as a mixing component in extrusion coating compositions, typically in conjunction with a low or lower melt resistance component, polymerization conditions need to be selected and balanced; for example, as discussed above. Important process parameters include maximum polymerization temperatures, inlet reactor pressure, conversion level, as well as the type, level and distribution of the chain transfer agent. The properties of the polymer (IE1, IE2 and other polymers) are shown in Tables 4 and 5.
    * EC: Compared; IE: Inventive; AC: based on Autoclave; tub: Tubular. ** Commercial polymers available from The Dow Chemical Company. t): All MWD metrics in this table obtained from GPC Method A.
    a) Mw (abs) <A x [(I2) B], where A = 5.00 x 102 (kg / mole) / (dg / min) B, and B = -0.40 [Mw (abs), GPC Method THE]. b) MS> C x [(12) D], where C = 13.5 cN / (dg / min) D, and D = -0.55 [= melt resistance MS, 190 ° C]. t): All MWD metrics in this table obtained from GPC Method A. Table 6 contains the branches per 1000C as measured by 13C NMR. These LDPE polymers contain amyl, or C5 branches, which are not contained in substantially linear polyethylenes such as AFFINITY polyolefin plastomers, or Ziegler-Natta catalyzed LLDPE, such as DOWLEX polyethylene resins, both produced by The Dow Chemical Company. Each LDPE shown in Table 6 contains more than, or equal to 2.0, amyl groups (branches) per 1000 carbon atoms. Table 7 contains the results of unsaturation 1H NMR. Table 6: Branching results in branches per 1000C by 13C NMR of Inventive Examples and Comparative Examples
    ND = not detected. * The values in column C6 + for the DOWLEX and AFFINITY samples represent C6 octene branches only, and do not include the chain ends.
    Formulations
    [0131] Blown films were prepared, and the physical properties measured, with different LDPEs and one LLDPE, LLDPE1 (DOWLEX 2045G). LLDPE1 had a melt index of 1.0 (MI or 12), and a density of 0.920 g / cm3. The films were prepared at 5% by weight, 10% by weight, 20% by weight, 50% by weight and 80% by weight of the respective LDPE, based on the weight of LDPE and LLDPE1.
    [0132] Each formulation was combined in a MAGUIRE gravimetric mixer. A polymer processing aid (PPA), Dynamar FX-5920A, was added to each formulation. PPA was added to 1% by weight of the master batch, based on the total weight of the formulation. The PPA master batch (Ingenia AC-01-01, available from Ingenia Polymers) contained 8% by weight of DYNAMAR FX-5920A in a polyethylene support. This is equivalent to 800 ppm PPA in the polymer.
    [0133] LLDPE1 was also used as the LLDPE in films prepared in maximum production. Maximum production was determined in samples prepared with the following components: 95% by weight of DOWLEX 2045G and 5% by weight of LDPE; 90% by weight of DOWLEX 2045G and 10% by weight of LDPE; and 80% by weight of DOWLEX 2045G and 20% by weight of LDPE. Blown Film Production
    [0134] Blown monolayer films were prepared in an "8 inch matrix" with a polyethylene "Standard Davis II Barrier screw". External cooling through an air ring and internal bubble cooling were used. General blown film parameters, used to produce each blown film, are shown in Table 8. Temperatures are the temperatures closest to the pellet feed hopper (Cylinder 1), and in ascending order, as the polymer has been blown through the die. Films at normal rates were run at 113.4 kg / h (250 lb / h).
    Film Production for Determination of Maximum Blown Film Production Rate
    [0135] The film samples were prepared at a controlled speed and at a maximum rate. The controlled rate was 113.4 kg / h (250 lb / h), which is equivalent to a specific outlet rate of 4.5 kg / h / cm (10.0 lb / h / inch) for the circumference of the matrix. The matrix diameter used for the maximum production tests was an 8 inch matrix, so that, for the controlled rate, as an example, the conversion between kg / h ("lb / h") and kg / h / cm ("lb / h / inch") of the matrix circumference, is shown below. Likewise, such an equation can be used for other rates, such as the maximum rate, replacing the maximum rate in the equation below to determine the kg / h / cm ("lb / h / inch") of the matrix circumference. Specific Production = (113.4 kg / h (250 lb / h)) / (20.3 cm (8 inches) * π) = (4.5 kg / h / cm (10 lb / h / inches)) of matrix circumference
    [0136] The maximum production rate for a given sample was determined by increasing the production rate to the point where bubble stability was the limiting factor. The extrusion profile was maintained for both samples (standard rate and maximum rate), however, the melting temperature was higher for the maximum rate samples, due to the increase in shear speed, with higher engine speed (rpm , rotations per minute). The bubble stability, at maximum production rate, was determined by taking the bubble to the point where it would not rest on the air ring. At that point, the rate was reduced to where the bubble was reset (maximum rate of production) in the air ring, and then a sample was taken. The cooling in the bubble was adjusted by adjusting the air ring and maintaining the bubble. This process determined the maximum production rate, while maintaining bubble stability.
    [0137] The results of the film are summarized in Tables 9-16. Table 9 shows film results at the standard rate, with Film # 1 being 100% LLDPE1, and Film # 2-6 being 95% LLDPE / 5% LDPE. Film # 2, containing IE1 and Film # 3 containing IE2, show advantages of good optics (low opacity, and high brightness and clarity), MD rupture (high), dart drop impact (high), and drying module (high) . These properties are important for a variety of films with the desirable properties of good optical and mechanical properties. These LDPEs allow the potential to reduce the thickness, or to reduce the thickness of the film, while maintaining good mechanical properties. Table 10 shows the film results at the maximum rate with Film # 7 being 100% LLDPE1, and Movies # 8-12 being 95% LLDPEl / 5% LDPE. These films show advantages, as seen in Table 9, at a standard rate. In addition, compositions containing IE1 and IE2 show improvement in film production rates of 0.5 to 3.2% over compositions containing the other LDPEs, even with this low level of addition of 5% by weight. The% increase in maximum production, as shown in Table 10, was calculated as, for example, for IE1:% Increase in Production Due to IE1, in comparison with Reference LDPE = (Maximum production mix with IE1 - Production mix maximum with Reference LDPE) X 100. Maximum production mix with Reference LDPE
    [0138] Table 11 contains the results for 10% LDPE added to LLDPE1 for Movies # 13-17, and Table 12 contains the results for 10% LDPE added to LLDPE1 for Movies # 18-22, prepared at maximum rate. These results show advantages of films similar to those observed in 5% LDPE (good optics, MD rupture, dart drop impact, and drying module). In addition, increases in the maximum rate over the reference LDPEs vary up to 8.4%, as shown in Table 12.
    [0139] Table 13 shows the results for 80% LLDPE / 20% LDPE at the standard rate, and Table 14 shows the results for 20% LDPE / 80% LLDPE1 at maximum rates. These results show properties similar to mixtures with lower% LDPE, but additionally, at maximum rates, good shrinkage stress is found for the compositions of the invention. Maximum production rates compared to other LDPEs are excellent with an improvement of up to 44%. Although the LDPE 6621 autoclave has good production rates, it suffers from weaker optics and perforation. These very substantial differences in production are new to the compositions of the invention, and will be translated into larger blown film lines, and even more differentiation and greater gains in the speed at which blown films can be produced are likely, which leads to cost savings. for the producer. In addition, the main advantages of film properties are maintained.
    [0140] Tables 15 and 16 show the results at 50% LDPE and 80% LDPE, respectively. Maximum production was not measured in these samples, but the production of IE1 and IE2 is expected to be very good and, generally, better than the comparative examples. Again, the optics, compared to the LDPE 6621 autoclave, are greatly improved, retaining other properties of the film.
    [0141] Figure 2 shows the maximum output for the different LDPE in LLDPE1, at 0%, 5%, 10%, and 20% LDPE, and the differentiation and advantage of IE1 and IE2, compared to other LDPEs. Figure 3 shows the MD shrinkage tension for films prepared in standard production for the different LDPEs in LLDPE1, at 0%, 5%, 10%, and 20% LDPE, and the differentiation and advantage of IE1 and IE2, in comparison with other LDPEs. Table 9: Properties of the 100% LLDPE1 film; and 95% LLDPEl / 5% LDPE Films # 1-6 prepared in 50.8 gm (2 mil) at a standard rate of 113.4 kg (250 lb / h) (20.3 cm (8 ") matrix)











    Mixing Compositions
    [0142] Mixtures of the same compositions used for blown films were prepared for further characterization. The components of the mixture were manipulated using a "18 mm" double screw extruder (micro-18). The twin screw extruder was a Leistritz machine controlled by Haake software. The extruder had five heated zones, a feed zone, and a "3 mm" chain mold. The feed zone was cooled by flowing water, while the remaining zones 1-5 and the matrix were electrically heated and cooled to 120, 135, 150, 190, 190, and 190 ° C, respectively. The pelletized polymer components were combined in a plastic bag, and mixed by drop by hand. After pre-heating the extruder, the cell load and pressure transducers of the matrix were calibrated. The drive unit for the extruder was run at 20 0 rpm, which resulted in gear transfer at a thread speed of 250 rpm. The dry mix was then fed (2.7-3.6 kg / h (6-8 lbs / h)) to the extruder through a double drill K-Tron feeder (model # K2VT20) using pellet drills. The hopper of the feeder was filled with nitrogen, and the feed cone for the extruder was covered with foil, to minimize air intrusion to minimize the possible oxygen degradation of the polymer. The resulting chain was quenched by water, dried with an air knife, and pelleted with a Conair crusher.
    [0143] The results are shown in Table 17 for compositions similar to those shown in Tables 9-16, along with the measured melt index, melt index ratio, density, and Mw, Mw / Mn and Mz. The melt strength data are shown in Figure 4 showing the differentiation and advantage of IE1 and IE2, compared to all other LDPEs. IE2 shows a behavior similar to the LDPE 6621 autoclave, but without the poor optical disadvantages and gels that can result in a film prepared from autoclave resins.
    权利要求:
    Claims (13)
    [0001]
    1. Composition, characterized by the fact that it comprises the following: A) a first polymer based on ethylene, formed by a polymerization process of high pressure of free radicals, and which comprises the following properties: a) a Mw (abs) / Mw ( GPC) <2.2, and b) an MS versus 12 ratio: MS C x [(12) D], where C = 13.5 cN / (dg / min) D and D = -0.55, c) one melting index (12) from 0.1 to 0.9 g / 10 min; and B) a second ethylene-based polymer; and wherein the second ethylene-based polymer has a melt index (12) of 0.1 to 4.0 g / 10 min.
    [0002]
    2. Composition according to claim 1, characterized by the fact that the first ethylene-based polymer is present in an amount greater than 0.5 weight percent, based on the sum of the weight of the first ethylene-based polymer and the second ethylene-based polymer.
    [0003]
    Composition according to any one of claims 1 to 2, characterized in that the second ethylene-based polymer is present in an amount of 10 to 95% by weight, based on the weight of the composition.
    [0004]
    Composition according to any one of claims 1 to 3, characterized in that the second ethylene-based polymer is an ethylene / alpha-olefin interpolymer.
    [0005]
    5. Composition according to claim 4, characterized in that the ethylene / α-olefin interpolymer is a heterogeneously branched ethylene / α-olefin interpolymer.
    [0006]
    6. Composition according to any one of claims 1 to 5, characterized in that the composition has a melt resistance (190 ° C) of 5 cN to 40 cN.
    [0007]
    Composition according to any one of claims 1 to 6, characterized in that the composition has a density of 0.910 to 0.925 g / cm3.
    [0008]
    8. Composition according to any one of claims 1 to 7, characterized in that the composition has a melting index (12) of 0.1 to 1.5 g / 10 min.
    [0009]
    9. Composition, according to any one of claims 1 to 8, characterized by the fact that when said composition is formed into a film, by means of a blown film process, the maximum production rate is at least 15 percent higher than the maximum rate of production of a similar film formed by a similar composition, except that the composition contains 100% by weight of the second ethylene-based polymer, based on the total weight of the first ethylene-based polymer and the second polymer-based of ethylene.
    [0010]
    10. Article, characterized by the fact that it comprises at least one component formed from the composition, as defined in any one of claims 1 to 9.
    [0011]
    11. Film, characterized by the fact that it comprises at least one layer formed from the composition, as defined in any of claims 1 to 9.
    [0012]
    12. Film according to claim 11, characterized in that the film comprises at least two layers.
    [0013]
    13. Film, according to claim 11 or claim 12, characterized by the fact that the film has an MD shrinkage tension greater than 0.0207 MPa (3.00 psi).
    类似技术:
    公开号 | 公开日 | 专利标题
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    同族专利:
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    CN105189639A|2015-12-23|
    JP6377141B2|2018-08-22|
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    US20160083568A1|2016-03-24|
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    法律状态:
    2018-02-27| B06F| Objections, documents and/or translations needed after an examination request according [chapter 6.6 patent gazette]|
    2019-12-10| B06U| Preliminary requirement: requests with searches performed by other patent offices: procedure suspended [chapter 6.21 patent gazette]|
    2020-06-09| B09A| Decision: intention to grant [chapter 9.1 patent gazette]|
    2020-08-18| B16A| Patent or certificate of addition of invention granted [chapter 16.1 patent gazette]|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 21/05/2014, OBSERVADAS AS CONDICOES LEGAIS. |
    优先权:
    申请号 | 申请日 | 专利标题
    US201361826271P| true| 2013-05-22|2013-05-22|
    US61/826,271|2013-05-22|
    PCT/US2014/038944|WO2014190039A1|2013-05-22|2014-05-21|Low density ethylene-based compositions with improved melt strength, output, and mechanical properties|
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