阅读说明：本技术 用于泡沫的共混物、由其制造的泡沫和包括其的制品 (Blends for foams, foams made therefrom, and articles comprising the same ) 是由 禹海洋 严金良 冯珊珊 R·T-H·周 于 2018-08-31 设计创作，主要内容包括：本文公开了一种可发泡组合物,所述可发泡组合物包括：烯烃共聚物,所述烯烃共聚物包括乙烯和α-烯烃；未中和的羧化烯烃共聚物；交联剂；发泡剂；以及激活剂；其中所述激活剂与所述未中和的羧化烯烃共聚物的重量比大于0.3。本文还公开了一种制造可发泡组合物的方法,所述方法包括：将以下共混在一起以形成所述可发泡组合物：烯烃共聚物,所述烯烃共聚物包括乙烯和α-烯烃；未中和的羧化烯烃共聚物；交联剂；发泡剂；以及激活剂；其中所述激活剂与所述未中和的羧化烯烃共聚物的重量比大于0.3；加热所述可发泡组合物以激活所述发泡剂,从而形成泡沫；以及使所述泡沫交联。(Disclosed herein is a foamable composition comprising: an olefin copolymer comprising ethylene and an alpha-olefin; unneutralized carboxylated olefin copolymers; a crosslinking agent; a foaming agent; and an activator; wherein the weight ratio of the activator to the unneutralized carboxylated olefin copolymer is greater than 0.3. Also disclosed herein is a method of making a foamable composition, the method comprising: blending together to form the foamable composition: an olefin copolymer comprising ethylene and an alpha-olefin; unneutralized carboxylated olefin copolymers; a crosslinking agent; a foaming agent; and an activator; wherein the weight ratio of the activator to the unneutralized carboxylated olefin copolymer is greater than 0.3; heating the foamable composition to activate the blowing agent to form a foam; and crosslinking the foam.)

1. A foamable composition comprising:

an olefin copolymer comprising ethylene and an alpha-olefin;

unneutralized carboxylated olefin copolymers;

a crosslinking agent;

a foaming agent; and

an activator comprising a metal oxide, a metal hydroxide, a metal salt, or a combination thereof;

wherein the weight ratio of the activator to the unneutralized carboxylated olefin copolymer is greater than 0.3.

2. The foamable composition of claim 1, wherein the olefin copolymer is an olefin block copolymer and the olefin copolymer is present in the foamable composition in an amount of 60 wt% to 90 wt%, based on the total weight of the foamable composition.

3. The foamable composition of claim 1 wherein the alpha olefin is octene.

4. The foamable composition of claim 1, wherein the carboxylated olefin copolymer is present in the foamable composition in an amount from 5 wt% to 20 wt%, based on the total weight of resins in the foamable composition.

5. The foamable composition of claim 1, wherein the carboxylated olefin copolymer comprises a carboxylic acid; wherein the carboxylic acid is acrylic acid or methacrylic acid.

6. The foamable composition of claim 1, wherein the crosslinking agent is a peroxide, and wherein the blowing agent is azodicarbonamide.

7. The foamable composition of claim 1, wherein a foam made from the foamable composition has a density from 0.15g/cc to 0.20g/cc, an Asker C hardness of 40 to 60 measured according to ASTM D2240, and a split tear (split tear) greater than 2.4N/mm measured according to ASTM D3574.

8. An article made from the foamable composition of claims 1 to 7.

9. The article of claim 8, wherein the article is a footwear sole.

10. A method of making a foamable composition, the method comprising:

blending together to form the foamable composition: an olefin copolymer comprising ethylene and an alpha-olefin; unneutralized carboxylated olefin copolymers; a crosslinking agent; a foaming agent; and an activator; wherein the weight ratio of the activator to the unneutralized carboxylated olefin copolymer is greater than 0.3;

heating the foamable composition to activate the blowing agent and the crosslinking agent to form a crosslinked foam.

11. The method of claim 10, further comprising molding the foamable composition.

Background

The present disclosure relates to blends for foams, foams made therefrom, and articles comprising the same.

Polymer foams are commonly used in a variety of different applications, such as thermal insulation, sound insulation, cushioning, filters, vibration and shock damping, and the like. Applications using such polymer foams include electronic devices, food packaging materials, clothing materials, building materials, interior and exterior parts of automobiles and household appliances, footwear, and the like.

Of the many commercially available foams, polyolefin foams and polyethylene vinyl/acetate foams are commonly used in footwear where properties such as cushioning and flexibility are desirable. The compression set of polyolefin foams is lower at elevated temperatures when compared to poly (ethylene/vinyl acetate) (EVA) foams. This difference is generally attributed to the melting point of the polyolefin foam as well as to the degree of cure and other factors.

Accordingly, it is desirable to produce polyolefin foams that exhibit better resistance to compression set when compared to poly (ethylene/vinyl acetate) foams, such that products using these foams will have superior properties when compared to products using poly (ethylene/vinyl acetate) foams.

Disclosure of Invention

Disclosed herein is a foamable composition comprising: an olefin copolymer comprising ethylene and an alpha-olefin; unneutralized carboxylated olefin copolymers; a crosslinking agent; a foaming agent; and an activator; wherein the weight ratio of the activator to the unneutralized carboxylated olefin copolymer is greater than 0.3.

Also disclosed herein is a method of making a foamable composition, the method comprising: blending together to form a foam: an olefin copolymer comprising ethylene and an alpha-olefin; unneutralized carboxylated olefin copolymers; a crosslinking agent; a foaming agent; and an activator; wherein the weight ratio of the activator to the unneutralized carboxylated olefin copolymer is greater than 0.3; heating the foamable composition to activate the blowing agent and the crosslinking agent to form a crosslinked foam.

Drawings

FIG. 1 shows the melting point/density relationship of an olefin block copolymer; and is

FIG. 2 is a graph depicting MDR (moving die rheometer) cure torque for OBC systems with (IE-1 and IE-4) or without (CE-3) E-MAA copolymer at the same crosslinker level;

FIG. 3 is a graph depicting MDR cure torque for EVA systems with or without (CE-5 to CE-7) E-MAA copolymers at the same crosslinker level;

FIG. 4 is a graph of foam hardness for OBC foams with and without E-MAA at different foam densities;

FIG. 5 is a graph of foam compression strength of OBC foams with and without E-MAA at different foam densities;

FIG. 6 is a graph of foam compression set versus cross-sectional tear for OBC foams with and without E-MAA at different foam densities;

FIG. 7 is a graph of foam compression set for OBC and EVA foams with or without E-MAA at different foam densities; and is

FIG. 8 depicts a spider graph comparing the performance of CE-2 (0 wt% E-MAA in OBC) and IE-6 (10 wt% E-MAA in OBC) foams.

Detailed Description

"composition" and like terms mean a mixture of two or more materials, such as polymers blended with other polymers or containing additives, fillers, and the like. The compositions comprise pre-reaction, reaction and post-reaction mixtures, the latter of which will comprise reaction products and by-products as well as unreacted components of the reaction mixture and decomposition products, if any, formed from one or more components of the pre-reaction or reaction mixture.

"blend," "polymer blend," and similar terms mean a composition of two or more polymers. Such blends may or may not be miscible. Such blends may or may not be phase separated. Such blends may or may not contain one or more domain configurations, as determined by transmission electron spectroscopy, light scattering, x-ray scattering, and any other method known in the art. The blend is not a laminate, but one or more layers of the laminate may contain the blend.

"Polymer" means a compound prepared by polymerizing monomers, whether of the same type or a different type. Thus, the generic term polymer encompasses the term homopolymer, which is commonly used to refer to polymers prepared from only one type of monomer, and the term interpolymer, as defined below. It also encompasses all forms of interpolymers, such as random, block, and the like. The term "ethylene/α -olefin polymer" means an interpolymer as described below. It should be noted that while a polymer is generally referred to as being "made from" a monomer, "based on" a specified monomer or monomer type, "containing" a specified monomer content, and the like, this is expressly understood to refer to the polymerization residue of the specified monomer and not to an unpolymerized species.

"interpolymer" means a polymer prepared by polymerizing at least two different monomers. This generic term encompasses copolymers, which are commonly used to refer to polymers prepared from two or more different monomers, and encompasses polymers prepared from more than two different monomers, e.g., terpolymers, tetrapolymers, etc.

"polyolefin", "polyolefin polymer", "polyolefin resin" and similar terms mean a polymer made from a simple olefin (also referred to as having the formula C)_nH_2nOlefin(s) produced. Polyethylene is prepared by polymerizing ethylene with or without one or more comonomers. Thus, the polyolefin comprises an interpolymer, such as an ethylene-alpha-olefin copolymerAnd the like.

As used herein, "melting point" (referred to the shape of the DSC curve plotted, also referred to as the melting peak) is typically measured by the DSC (differential scanning calorimetry) technique for measuring the melting point or melting peak of polyolefins as described in USP 5,783,638. The heating rate during the measurement of the melting point may be 10 to 20 c/min. The atmosphere during heat conduction may be an inert gas such as nitrogen or argon. It should be noted that many blends comprising two or more polyolefins will have more than one melting point or melting peak; many individual polyolefins will include only one melting point or peak.

The term "and/or" includes "and" as well as "or" both. For example, the terms a and/or B are interpreted to mean A, B or a and B.

"Low crystallinity," "high crystallinity," and similar terms are used in a relative sense and not in an absolute sense. However, the low crystallinity component has a crystallinity of from 1 to 25 weight percent, preferably from 1 to 20 weight percent, and more preferably from 1 to 15 weight percent, based on the total weight of the foam. The high crystallinity component has a crystallinity of 25 weight percent or greater based on the total weight of the foam.

The high crystalline polymers generally include Linear Low Density Polyethylene (LLDPE), Low Density Polyethylene (LDPE), LLDPE/LDPE blends, High Density Polyethylene (HDPE), Substantially Linear Ethylene Polymers (SLEP), Random Copolymers (RCP), and the like, as well as various blends thereof. The low crystallinity polymers of particular interest preferably comprise ethylene/α -olefin multiblock interpolymers as defined and discussed in co-pending PCT application No. PCT/US2005/008917, filed on day 3, 17, 2005 and published as WO/2005/090427 on day 9, 29, 2005 in 2005, which in turn claims priority to U.S. provisional application No. 60/553,906 filed on day 3, 17, 2004, both of which are incorporated herein by reference. The low crystalline polymer also comprises propylene/ethylene.

The term "polymer" generally includes, but is not limited to, homopolymers, copolymers, such as for example, block, graft, random and alternating copolymers, terpolymers, etc. and blends and modifications thereof. Furthermore, unless otherwise specifically limited, the term "polymer" shall encompass all possible geometrical configurations of the material. These configurations include, but are not limited to isotactic, syndiotactic and random symmetries.

All percentages specified herein are weight percentages unless otherwise indicated.

"interpolymer" means a polymer prepared by polymerizing at least two different types of monomers. The generic term "interpolymer" encompasses the term "copolymer" (which is generally used to refer to polymers prepared from two different monomers) as well as the term "terpolymer" (which is generally used to refer to polymers prepared from three different types of monomers). It also encompasses polymers prepared by polymerizing four or more monomers.

Disclosed herein is a foamable composition that can be used to make foams having cell sizes and crosslink densities that ensure lower compression set when compared to other commercially available foams for footwear applications. The foam has a density less than or equal to 0.23g/cc, preferably less than or equal to 0.22g/cc and more preferably less than or equal to 0.20 g/cc. The compression set resistance and compression strength reflect the support ability of the foam. Good compression set resistance and compressive strength increase the durability of the shoe.

The foamable composition includes a polyolefin elastomer, a carboxylated olefin copolymer, a blowing agent, a catalyst package, and a crosslinking agent. The foamable composition is free of ionomer (neutralized carboxylated olefin copolymer) prior to foaming. In one embodiment, the resulting foam may contain an ionomer (neutralized carboxylated olefin copolymer) formed during the foaming or crosslinking process.

In one embodiment, no ionomer is added to the foamable composition prior to crosslinking and foaming, and the ionomer may be formed in situ as a result of a reaction between the ingredients of the foamable composition (e.g., polyolefin elastomer, carboxylated olefin copolymer, blowing agent, catalyst package, and crosslinking agent) during crosslinking or foaming.

In exemplary embodiments, the polyolefin elastomer may include an Olefin Block Copolymer (OBC) and/or an olefin random copolymer. The polyolefin elastomer may be a copolymer comprising ethylene and an alpha-olefin. The polyolefin elastomer may be homogeneously or heterogeneously branched.

Copolymers comprising ethylene and an alpha-olefin are also referred to as ethylene/alpha-olefin interpolymers. The term "ethylene/a-olefin interpolymer" generally refers to a polymer comprising ethylene and an a-olefin having 3 or more carbon atoms. Preferably, ethylene comprises the majority mole fraction of the total polymer, i.e. ethylene comprises at least 50 mole% of the total polymer. More preferably ethylene comprises at least 60 mole%, at least 70 mole% or at least 80 mole%, wherein substantially the remainder of the entire polymer comprises at least one other comonomer which is preferably an alpha-olefin having 3 or more carbon atoms. For many ethylene/octene copolymers, preferred compositions include an ethylene content greater than 80 mole percent of the total polymer and an octene content of from 10 to 20, preferably from 15 to 20 mole percent of the total polymer. In some embodiments, the ethylene/a-olefin interpolymer does not comprise those produced in low yield or in small amounts or as a by-product of a chemical process. While the ethylene/α -olefin interpolymer may be blended with one or more polymers, the ethylene/α -olefin interpolymer so produced is substantially pure and typically comprises a major component of the reaction product of the polymerization process.

Ethylene/α -olefin interpolymers include, in polymerized form, ethylene and one or more copolymerizable α -olefin comonomers, characterized by multiple blocks or segments of two or more polymerized monomer units that differ in chemical or physical properties. That is, the ethylene/α -olefin interpolymer is a block interpolymer, preferably a multi-block interpolymer or copolymer. The terms "interpolymer" and "copolymer" are used interchangeably herein. In some embodiments, the multi-block copolymer can be represented by the formula:

(AB)_n，

wherein n is at least 1, preferably an integer greater than 1, such as 2,3, 4, 5, 10, 15, 20, 30, 40, 50, 60, 70, 80, 90, 100 or more, "a" represents a hard block or segment and "B" represents a soft block or segment. Preferably, a and B are linked in a substantially linear manner, as opposed to a substantially branched or substantially star-shaped manner. In other embodiments, the a and B blocks are randomly distributed along the polymer chain.

In still other embodiments, the block copolymer generally does not have a third type of block, which includes one or more different comonomers. In yet other embodiments, block a and block B each have a monomer or comonomer substantially randomly distributed within the block. In other words, neither block a nor block B includes two or more sub-segments (or sub-blocks) of different compositions, such as end segments, which have a composition that is substantially different from the remainder of the block.

Multiblock polymers generally include various amounts of "hard" and "soft" segments. "hard" segment means a block of polymerized units in which ethylene is present in an amount greater than 95 weight percent and preferably greater than 98 weight percent, based on the weight of the polymer. In other words, the comonomer content (monomer content other than ethylene) in the hard segments is less than 5 wt% and preferably less than 2 wt% based on the weight of the polymer. In some embodiments, the hard segments comprise all or substantially all of the ethylene. On the other hand, a "soft" segment refers to a block of polymerized units in which the comonomer content (monomer content other than ethylene) is greater than 5 wt.%, preferably greater than 8 wt.%, greater than 10 wt.%, or greater than 15 wt.%, based on the weight of the polymer. In some embodiments, the comonomer content in the soft segment can be greater than 20 wt.%, greater than 25 wt.%, greater than 30 wt.%, greater than 35 wt.%, greater than 40 wt.%, greater than 45 wt.%, greater than 50 wt.%, or greater than 60 wt.%.

The soft segment can typically be present in the block interpolymer from 1 to 99 weight percent of the total weight of the block interpolymer, preferably from 5 to 95 weight percent, from 10 to 90 weight percent, from 15 to 85 weight percent, from 20 to 80 weight percent, from 25 to 75 weight percent, from 30 to 70 weight percent, from 35 to 65 weight percent, from 40 to 60 weight percent, or from 45 to 55 weight percent of the total weight of the block interpolymer. Conversely, hard segments may be present in similar ranges. The soft segment weight percent and hard segment weight percent can be calculated based on data obtained from DSC or NMR. Such methods and calculations are disclosed in U.S. patent application serial No. 11/376,835, filed on 15.2006 in the name of Colin l.p.shann, Lonnie hazlit et al and assigned to Dow Global technology, llc entitled "ethylene/a-olefin block interpolymer," the disclosure of which is incorporated herein by reference in its entirety.

In one embodiment, the ethylene/a-olefin interpolymers (also referred to as "interpolymers" or "polymers") used in the embodiments comprise, in polymerized form, ethylene and one or more copolymerizable a-olefin comonomers, characterized by multiple blocks or segments of two or more polymerized monomer units differing in chemical or physical properties (block interpolymers), preferably multi-block copolymers. The ethylene/a-olefin interpolymers are characterized by one or more of the aspects described below.

In one aspect, M for the ethylene/α -olefin interpolymers of embodiments of the present invention_w/M_nIs 1.7 to 3.5 and has at least one melting point T in degrees Celsius_mAnd a density d in grams per cubic centimeter, wherein the numerical values of the variables correspond to the relationship:

T_m>-2002.9+4538.5(d)-2422.2(d)²and preferably, is

T_m≧-6288.1+13141(d)-6720.3(d)²And more preferably

T_m≧858.91-1825.3(d)+1112.8(d)²。

This melting point/density relationship is shown in figure 1. Unlike conventional random copolymers of ethylene/alpha-olefins, which have melting points that decrease with decreasing density, interpolymers (represented by diamonds) exhibit a melting point that is substantially independent of density, particularly when the density is between 0.87g/cc and 0.95 g/cc. For example, when the density ranges from 0.875g/cc to 0.945g/cc, the melting point of such polymers is in the range of 110 ℃ to 130 ℃. In some embodiments, the melting point of such polymers is in the range of 115 ℃ to 125 ℃ when the density ranges from 0.875g/cc to 0.945 g/cc.

In another aspect, an ethylene/α -olefin interpolymer comprises ethylene and one or more α -olefins in polymerized form and is characterized by a Δ T in degrees celsius, a temperature defined as the highest differential scanning calorimetry ("DSC") peak minus the temperature of the highest crystallographic analysis fractionation ("CRYSTAF") peak, and a heat of fusion, Δ H, in J/g, and the Δ T and Δ H satisfy the following relationship:

Δ T > -0.1299(Δ H) +62.81, and preferably

DeltaT ≧ -0.1299 (DeltaH) +64.38, and more preferably

ΔT≧-0.1299(ΔH)+65.95，

Up to 130J/g for Δ H. Further, for Δ H greater than 130J/g, Δ T is equal to or greater than 48 ℃. The CRYSTAF peak is determined using at least 5% cumulative polymer (i.e., the desired peak represents at least 5% cumulative polymer), and if less than 5% of the polymer has an identifiable CRYSTAF peak, the CRYSTAF temperature is 30 ℃, and Δ H is the value of the heat of fusion in J/g. More preferably, the highest CRYSTAF peak contains at least 10 percent cumulative polymer.

In yet another aspect, when fractionated using temperature rising elution fractionation ("TREF"), the ethylene/a-olefin interpolymer has a molecular fraction that elutes between 40 ℃ and 130 ℃, characterized in that the fraction has a higher molar comonomer content, preferably at least 5% higher, more preferably at least 10% higher, than a comparable random ethylene interpolymer fraction that elutes at the same temperature, wherein the comparable random ethylene interpolymer contains one or more of the same comonomer, and has a melt index, density, and molar comonomer content (based on the entire polymer) within 10% of the block interpolymer. Preferably, the Mw/Mn of the comparable interpolymer is also within 10% of the Mw/Mn of the block interpolymer, and/or the comparable interpolymer has a total comonomer content within 10 weight percent of the total comonomer content of the block interpolymer.

In yet another aspect, the ethylene/α -olefin interpolymer is characterized by an elastic recovery, Re, in percent measured at 300% strain and 1 cycle on a compression molded film of the ethylene/α -olefin interpolymer, and has a density, d, in grams/cubic centimeter, wherein the numerical values of Re and d satisfy the following relationship when the ethylene/α -olefin interpolymer is substantially free of a crosslinking phase:

re >1481-1629 (d); and preferably

Re ≧ 1491-1629 (d); and more preferably

Re ≧ 1501-1629 (d); and even more preferably

Re≧1511-1629(d)。

In some embodiments, the ethylene/a-olefin interpolymer has a tensile strength greater than 10MPa, preferably a tensile strength ≧ 11MPa, more preferably a tensile strength ≧ 13MPa, and/or an elongation at break of at least 600%, more preferably at least 700%, highly preferably at least 800% and most preferably at least 900% at a beam displacement rate of 11 cm/min.

In other embodiments, the ethylene/α -olefin interpolymer has a (1) storage modulus ratio, G '(25 ℃)/G' (100 ℃), of from 1 to 50, preferably from 1 to 20, more preferably from 1 to 10; and/or (2) a compression set at 70 ℃ of less than 80%, preferably less than 70%, in particular less than 60%, less than 50% or less than 40%, down to a compression set of zero.

In still other embodiments, the ethylene/a-olefin interpolymer has a 70 ℃ compression set of less than 80%, less than 70%, less than 60%, or less than 50%. Preferably, the interpolymer has a 70 ℃ compression set of less than 40%, less than 30%, less than 20%, and can be lowered to 0%.

In some embodiments, the ethylene/α -olefin interpolymer has a heat of fusion of less than 85J/g and/or a pellet blocking strength equal to or less than 100 pounds per square foot (4800Pa), preferably equal to or less than 50lbs/ft²(2400Pa), in particular equal to or less than 5lbs/ft²(240Pa) and as low as 0lbs/ft²(0Pa)。

In other embodiments, the ethylene/a-olefin interpolymer comprises, in polymerized form, at least 50 mole percent ethylene, and has a 70 ℃ compression set of less than 80%, preferably less than 70% or less than 60%, most preferably less than 40 to 50% and down to near zero%.

In some embodiments, the multi-block copolymer has a polydispersity index (PDI) that fits a Schultz-Flory distribution rather than a Poisson distribution. The copolymer is further characterized as having both a polydisperse block distribution and a polydisperse block size distribution, and as having the most likely block length distribution. Preferred multi-block copolymers are those containing 4 or more blocks or segments (including end blocks). More preferably, the copolymer comprises at least 5, 10 or 20 blocks or segments (including end blocks).

Comonomer content can be measured using any suitable technique, with techniques based on nuclear magnetic resonance ("NMR") spectroscopy being preferred. Furthermore, for polymers or polymer blends having a relatively broad TREF curve, it is desirable to first use TREF to fractionate the polymer into fractions each having an elution temperature range of 10 ℃ or less. That is, the collection temperature window for each eluted fraction was 10 ℃ or less. Using this technique, the block interpolymer has at least one such fraction having a higher molar comonomer content than the corresponding fraction of the comparable interpolymer.

In another aspect, the polymer is an olefin interpolymer, preferably comprising ethylene and one or more copolymerizable comonomers in polymerized form, characterized by multiple blocks (i.e., at least two blocks) or segments (block interpolymer), most preferably a multi-block copolymer, of two or more polymerized monomer units differing in chemical or physical properties, said block interpolymer having a peak (but not only the molecular fraction) eluting between 40 ℃ and 130 ℃ (but not collecting and/or isolating individual fractions), characterized in that said peak has a comonomer content as estimated by infrared spectroscopy when expanded using full width/half maximum (FWHM) area calculations, as compared to the equivalent random ethylene interpolymer peak at the same elution temperature and expanded using full width/half maximum (FWHM) area calculations, the average comonomer molar content of the peaks is higher,preferably at least 5% higher, more preferably at least 10% higher, wherein the comparable random ethylene interpolymer has one or more of the same comonomer(s) and has a melt index, density, and comonomer molar content (based on the entire polymer) within 10% of the block interpolymer. Preferably, the Mw/Mn of the comparable interpolymer is also within 10% of the Mw/Mn of the block interpolymer, and/or the comparable interpolymer has a total comonomer content within 10 weight percent of the total comonomer content of the block interpolymer. Full width/half maximum (FWHM) calculations are based on the methyl and methylene response areas [ CH ] from the ATREF infrared detector₃/CH₂]Wherein the highest (highest) peak is identified from the baseline, and then determining the FWHM area. For the distribution measured using the ATREF peak, the FWHM area is defined as T₁And T₂Area under the curve in between, wherein T₁And T₂Are points determined to the left and right of the ATREF peak by dividing the peak height by two and then plotting a line horizontal to the baseline that intersects the left and right portions of the ATREF curve. A calibration curve of comonomer content was prepared using random ethylene/alpha-olefin copolymers, plotting the comonomer content from NMR versus the FWHM area ratio of the TREF peak. For this infrared method, calibration curves are generated for the same comonomer type of interest. The comonomer content of the TREF peak of a polymer can be determined by reference to the FWHM methyl to methylene area ratio [ CH ] using its TREF peak₃/CH₂]Is determined from this calibration curve.

Comonomer content can be measured using any suitable technique, with techniques based on Nuclear Magnetic Resonance (NMR) spectroscopy being preferred. Using this technique, the block interpolymers have a higher comonomer mole content than the corresponding equivalent interpolymers.

Preferably, for interpolymers of ethylene and 1-octene, the TREF fraction of the block interpolymer that elutes between 40 and 130 ℃ has a comonomer content greater than or equal to the amount (-0.2013) T +20.07, more preferably greater than or equal to the amount (-0.2013) T +21.07, where T is the number of peak elution temperatures of the TREF fractions being compared, measured in degrees Celsius.

In addition to the above aspects and properties described herein, the polymer may be characterized by one or more other characteristics. In one aspect, the polymer is an olefin interpolymer, preferably comprising ethylene and one or more copolymerizable comonomers in polymerized form, characterized by multiple blocks or segments of two or more polymerized monomer units differing in chemical or physical properties (block interpolymer), most preferably a multi-block copolymer, said block interpolymer having a molecular fraction eluting between 40 ℃ and 130 ℃, when fractionated using TREF increments, characterized in that said fraction has a higher molar comonomer content, preferably at least 5% higher, more preferably at least 10, 15, 20 or 25% higher, as compared to the molar comonomer content of a comparable random ethylene interpolymer fraction eluting at the same temperature, wherein said comparable random ethylene interpolymer comprises one or more identical comonomers, preferably which are one or more identical comonomers and have a melt index within 10% of the block interpolymer, Density and comonomer molar content (based on the whole polymer). Preferably, the Mw/Mn of the comparable interpolymer is also within 10% of the Mw/Mn of the block interpolymer, and/or the comparable interpolymer has a total comonomer content within 10 weight percent of the total comonomer content of the block interpolymer.

Preferably, the above interpolymer is an interpolymer of ethylene and at least one alpha-olefin, especially having a total polymer density of from 0.855 to 0.935g/cm³And more particularly for polymers having greater than 1 mole percent comonomer, the TREF fraction of the block interpolymer that elutes between 40 and 130 ℃ has a comonomer content greater than or equal to the amount (-0.1356) T +13.89, more preferably greater than or equal to the amount (-0.1356) T +14.93, and most preferably greater than or equal to the amount (-0.2013) T +21.07, where T is the value of the peak ATREF elution temperature, measured in degrees Celsius, of the TREF fractions being compared.

Preferably, for the above interpolymers of ethylene and at least one alpha-olefin, especially the total polymer density is from 0.855 to 0.935g/cm³And more specifically for poly having greater than 1 mole% comonomerThe TREF fractions of the block interpolymers that elute between 40 and 130 ℃ have a comonomer content greater than or equal to the amount (-0.2013) T +20.07, more preferably greater than or equal to the amount (-0.2013) T +21.07, where T is the value of the peak elution temperature, measured in degrees Celsius, of the TREF fractions being compared.

In yet another aspect, the polymer is an olefin interpolymer, preferably comprising, in polymerized form, ethylene and one or more copolymerizable comonomers, characterized by multiple blocks or segments of two or more polymerized monomer units differing in chemical or physical properties (block interpolymer), most preferably a multi-block copolymer, said block interpolymer having molecular fractions eluting between 40 ℃ and 130 ℃, each fraction having a comonomer content of at least 6 mole percent when fractionated using TREF increments having a melting point greater than 100 ℃. For those fractions having a comonomer content of 3 to 6 mole%, the DSC melting point of each fraction is 110 ℃ or higher. More preferably, the polymer fraction having at least 1 mol% comonomer has a DSC melting point corresponding to the formula:

tm ≧ 5.5926 (mol% of comonomer in fraction) + 135.90.

In yet another aspect, the polymer is an olefin interpolymer, preferably comprising ethylene and one or more copolymerizable comonomers in polymerized form, characterized by multiple blocks or segments of two or more polymerized monomer units differing in chemical or physical properties (block interpolymer), most preferably a multi-block copolymer, said block interpolymer having molecular fractions eluting between 40 ℃ and 130 ℃, each fraction having an ATREF elution temperature greater than or equal to 76 ℃ when fractionated using TREF increments, having a melting enthalpy (heat of fusion) as measured by DSC corresponding to the formula:

heat of fusion (J/gm) ≦ 3.1718 (ATREF elution temperature in degrees Celsius) 136.58.

The block interpolymers have molecular fractions that elute between 40 ℃ and 130 ℃, when fractionated using TREF increments, characterized in that each fraction having an ATREF elution temperature between 40 ℃ and less than 76 ℃ has a melting enthalpy (heat of fusion) as measured by DSC corresponding to the formula:

heat of fusion (J/gm) ≦ 1.1312 (ATREF elution temperature in degrees celsius) + 22.97.

The comonomer composition of the TREF peak can be measured using an IR4 infrared detector from Perry Moire, Inc. (Polymer Char, Valencia, Spain) (http:// www.polymerchar.com /) in Balencia, Spain.

The "composition mode" of the detector is equipped with a measurement sensor (CH)₂) And a composition sensor (CH)₃) Which is 2800-3000cm^-1A fixed narrow band infrared filter in the region. Measurement sensor for detecting methylene (CH) on polymer₂) Carbon (which is directly related to the polymer concentration in solution), while the composition sensor detects the methyl (CH) group of the polymer₃) A group. Component signal (CH)₃) Divided by the measurement signal (CH)₂) Is sensitive to the comonomer content of the measured polymer in solution and its response is calibrated with known ethylene alpha-olefin copolymer standards.

When used with an ATREF instrument, the detector provides the concentration of eluting polymer (CH) during the TREF process₂) And Composition (CH)₃) The signal is responded to. The CH of a polymer having a known comonomer content can be measured, preferably by NMR₃And CH₂The area ratio of (a) to (b) yields a polymer-specific calibration. Comonomer content of the ATREF peak of a polymer can be determined by applying a single CH₃And CH₂Reference calibration of area ratio of response (i.e., area ratio CH)₃/CH₂For comonomer content).

After applying the appropriate baseline to integrate the individual signal responses from the TREF chromatogram, the area of the peak can be calculated using a full width/half maximum (FWHM) calculation. The full width/half maximum calculation is based on the methyl and methylene response area [ CH ] according to the ATREF infrared detector₃/CH₂]Wherein the highest (highest) peak is identified from the baseline, and then determining the FWHM area. For the distribution measured using the ATREF peak, the FWHM area is defined as the curve between T1 and T2Lower area, where T1 and T2 are points determined to the left and right of the ATREF peak by dividing the peak height by two and then plotting a line horizontal to the baseline that intersects the left and right portions of the ATREF curve.

The use of infrared spectroscopy to measure the comonomer content of polymers in this ATREF-infrared method is in principle similar to the use of GPC/FTIR systems as described in the following references: markovich, Ronald p.; hazlitt, Lonnie g.; smith, linear; "Development of gel-permeation chromatography-Fourier transform Infrared Spectroscopy for characterization of ethylene-based polyolefin copolymers" (Polymeric Materials Science and Engineering) (1991),65, 98-100; and Deslauriers, p.j.; rohlfinfg, d.c.; shieh, e.t.; "quantification of short-chain branched microstructures in ethylene-1-olefin copolymers using size exclusion chromatography and Fourier transform Infrared Spectroscopy (SEC-FTIR)" quantitative short chain branched microstructures in ethylene-1-olefin copolymers using size exclusion chromatography and Fourier transform Infrared Spectroscopy (SEC-FTIR) "," Polymer (Polymer) (2002),43,59-170 ", both of which are incorporated herein by reference in their entirety.

In other embodiments, the ethylene/a-olefin interpolymer is characterized by an average block index, ABI, greater than zero and up to 1.0, and a molecular weight distribution, M_W/M_nGreater than 1.3. The average block index ABI is the weighted average of the block indices ("BI") of each polymer fraction obtained from 20 ℃ and 110 ℃ in preparative TREF with an increment of 5 ℃:

ABI＝∑(w_iBI_i)

wherein BI_iIs the block index of the i fraction of the ethylene/alpha-olefin interpolymer obtained in preparative TREF, and w_iIs the weight% of fraction i.

For each polymer fraction, the BI is defined by one of the following two equations (both equations have the same BI value):

or

Wherein T is_XIs the preparative ATREF elution temperature (preferably expressed in Kelvin) of fraction i, P_XIs the ethylene mole fraction of the i-th fraction, which can be measured by NMR or IR as described above. P_ABIs the ethylene mole fraction of the entire ethylene/a-olefin interpolymer (prior to fractionation), which can also be measured by NMR or IR. T is_AAnd P_AATREF elution temperature and ethylene mole fraction are pure "hard segments" (which refers to the crystalline segments of the interpolymer). As a first approximation, if the actual value of "hard segment" is not available, then T will be_AAnd P_AThe values are set to those of the high density polyethylene homopolymer. For the calculations performed herein, T_AIs 372 DEG K, P_AIs 1.

T_ABIs of the same composition and has an ethylene mole fraction of P_ABThe ATREF temperature of the random copolymer of (a). T is_ABCan be calculated according to the following equation:

Ln P_AB＝α/T_AB+β

where α and β are two constants that can be determined by calibration using many known random ethylene copolymers. It should be noted that α and β may vary from instrument to instrument. Furthermore, it would be desirable to create its own calibration curve with the polymer composition of interest and also within a similar molecular weight range as the fractions. There was a slight molecular weight effect. If the calibration curve is obtained from a similar molecular weight range, this effect will be substantially negligible. In some embodiments, the random ethylene copolymer satisfies the following relationship:

Ln P＝-237.83/T_ATREF+0.639

T_XOis of the same composition and has an ethylene mole fraction of P_XThe ATREF temperature of the random copolymer of (a). T is_XOMay be according to LnP_X＝α/T_XO+ β. In contrast, P_XOIs of the same composition and has an ATREF temperature of T_XEthylene mole fraction of the random copolymer of (a), which can be in terms of Ln P_XO＝α/T_X+ β.

Once the Block Index (BI) for each preparative TREF fraction is obtained, the weight average block index ABI of the entire polymer can be calculated. In some embodiments, ABI is greater than zero but less than 0.3 or from 0.1 to 0.3. In other embodiments, ABI is greater than 0.3 and at most 1.0. Preferably, ABI should be in the range of 0.4 to 0.7, 0.5 to 0.7, or 0.6 to 0.9. In some embodiments, ABI is in a range of 0.3 to 0.9, 0.3 to 0.8, or 0.3 to 0.7, 0.3 to 0.6, 0.3 to 0.5, or 0.3 to 0.4. In other embodiments, ABI is in a range of 0.4 to 1.0, 0.5 to 1.0, or 0.6 to 1.0, 0.7 to 1.0, 0.8 to 1.0, or 0.9 to 1.0.

Another characteristic of the ethylene/α -olefin interpolymer is that the ethylene/α -olefin interpolymer comprises at least one polymer fraction, which can be obtained by preparative TREF, wherein the fraction has a block index greater than 0.1 and up to 1.0 and a molecular weight distribution, M_w/M_nGreater than 1.3. In some embodiments, the block index of the polymer fraction is greater than 0.6 and up to 1.0, greater than 0.7 and up to 1.0, greater than 0.8 and up to 1.0, or greater than 0.9 and up to 1.0. In other embodiments, the block index of the polymer fraction is greater than 0.1 and up to 1.0, greater than 0.2 and up to 1.0, greater than 0.3 and up to 1.0, greater than 0.4 and up to 1.0, or greater than 0.4 and up to 1.0. In still other embodiments, the block index of the polymer fraction is greater than 0.1 and up to 0.5, greater than 0.2 and up to 0.5, greater than 0.3 and up to 0.5, or greater than 0.4 and up to 0.5. In still other embodiments, the block index of the polymer fraction is greater than 0.2 and up to 0.9, greater than 0.3 and up to 0.8, greater than 0.4 and up to 0.7, or greater than 0.5 and up to 0.6.

For copolymers of ethylene and alpha-olefins, the polymer preferably has (1) a PDI of at least 1.3, more preferably at least 1.5, at least 1.7 or at least 2.0 and most preferably at least 2.6, up to a maximum of 5.0, more preferably up to a maximum of 5.0A value of 3.5 and especially at most a maximum of 2.7; (2) a heat of fusion of 80J/g or less; (3) an ethylene content of at least 50 wt%; (4) glass transition temperature T_gLess than-25 ℃, more preferably less than-30 ℃, and/or (5) one and only one T_m。

Further, the polymer can have a storage modulus G ', alone or in combination with any other property disclosed herein, such that log (G') is greater than or equal to 400kPa, preferably greater than or equal to 1.0MPa at a temperature of 100 ℃. Furthermore, the polymers have a relatively flat storage modulus as a function of temperature in the range from 0 to 100 ℃, which is characteristic of block copolymers and for olefin copolymers, in particular ethylene and one or more C' s_3-8Copolymers of aliphatic alpha-olefins have not been known to date. In this context, the term "relatively flat" means that the log G' (in pascals) decreases by less than an order of magnitude between 50 and 100 ℃, preferably between 0 and 100 ℃.

The interpolymer may be further characterized by a thermomechanical analysis penetration depth of 1mm and a flexural modulus of 3kpsi (20MPa) to 13kpsi (90MPa) at a temperature of at least 90 ℃. Alternatively, the interpolymer can have a thermomechanical analysis penetration depth of 1mm and a flexural modulus of at least 3kpsi (20MPa) at a temperature of at least 104 ℃. The polymer may be characterized by an abrasion resistance (or volume loss) of less than 90mm³. The flexibility-heat resistance balance of the polymer is significantly better than that of other polymers.

Additionally, the ethylene/alpha-olefin interpolymer has a melt index, I₂May be from 0.01 to 2000 g/10 min, preferably from 0.01 to 1000 g/10 min, more preferably from 0.01 to 500 g/10 min, and especially from 0.01 to 100 g/10 min. In certain embodiments, the ethylene/a-olefin interpolymer has a melt index, I₂From 0.01 to 10 g/10 min, from 0.5 to 50 g/10 min, from 1 to 30 g/10 min, from 1 to 6 g/10 min, or from 0.3 to 10 g/10 min. In certain embodiments, the ethylene/α -olefin polymer has a melt index of 1 g/10 minutes, 3 g/10 minutes, or 5 g/10 minutes.

Molecular weight M of the Polymer_wMay be 1,000 gramsFrom/mole to 5,000,000 g/mole, preferably from 1000 g/mole to 1,000,000, more preferably from 10,000 g/mole to 500,000 g/mole and especially from 10,000 g/mole to 300,000 g/mole. The density of the polymer may be from 0.80 to 0.99g/cm³And preferably 0.85g/cm for ethylene containing polymers³To 0.97g/cm³. In certain embodiments, the ethylene/alpha-olefin polymer has a density of from 0.860 to 0.925g/cm³Or 0.867 to 0.910g/cm³。

Methods for preparing polymers have been disclosed in the following patent applications: U.S. provisional application No. 60/553,906 filed on 17.3.2004; U.S. provisional application No. 60/662,937, filed on 17.3.2005; U.S. provisional application No. 60/662,939, filed on 17.3.2005; U.S. provisional application No. 60/5662938, filed on 17.3.2005; PCT application No. PCT/US2005/008916, filed on 17.3.2005; PCT application No. PCT/US2005/008915, filed on 17.3.2005; and PCT application No. PCT/US2005/008917, filed on 17.3.2005, which is hereby incorporated by reference in its entirety.

The interpolymers also exhibit a unique relationship of crystallinity and branching distribution. That is, the interpolymers have a relatively large difference between the highest peak temperatures measured using CRYSTAF and DSC, which is a function of the heat of fusion, particularly as compared to a random copolymer or physical blend of polymers containing the same monomers and monomer levels, such as a blend of a high density polymer and a low density copolymer at equivalent overall densities. It is believed that this unique feature of the interpolymer is due to the unique distribution of the comonomers in the blocks within the polymer backbone. In particular, the interpolymer may comprise alternating blocks (comprising homopolymer blocks) having different comonomer contents. The interpolymer may also comprise a distribution of the number and/or block sizes of polymer blocks having different densities or comonomer contents, which is a schulz-flory type distribution. In addition, the interpolymers also have unique peak melting points and crystallization temperature profiles that are substantially independent of polymer density, modulus, and morphology. In preferred embodiments, the crystallite grade of the polymer shows characteristic spherulites and platelets distinguishable from random or block copolymers, even at PDI values of less than 1.7 or even less than 1.5, down to less than 1.3.

In addition, the interpolymers can be prepared using techniques that affect the degree or level of blockiness. That is, the amount of comonomer and the length of each polymer block or segment can be varied by controlling the ratio and type of catalyst and shuttling agent, as well as the polymerization temperature and other polymerization variables. The surprising benefit of this phenomenon is the discovery that as the degree of blockiness increases, the optical properties, tear strength, and high temperature recovery properties of the resulting polymer improve. Specifically, as the average number of blocks in the polymer increases, haze decreases while clarity, tear strength, and high temperature recovery properties increase. Other forms of polymer termination can be effectively inhibited by selecting a shuttling agent and catalyst combination having the desired chain transfer capability (high shuttling rate with low levels of chain termination). Thus, little, if any, β -hydride elimination is observed in the polymerization of ethylene/α -olefin comonomer mixtures according to embodiments of the present invention, and the resulting crystalline blocks are highly or substantially fully linear with little or no long chain branching.

Polymers with highly crystalline chain ends can be selectively prepared according to embodiments of the present invention. In elastomer applications, reducing the relative amount of polymer end-capped with amorphous blocks reduces the intermolecular dilution effect on crystalline regions. This result can be achieved by selecting chain shuttling agents and catalysts that have the appropriate response to hydrogen or other chain terminating agents. In particular, if a catalyst that produces a highly crystalline polymer is more prone to chain termination (e.g., by the use of hydrogen) than a catalyst that is responsible for producing a less crystalline polymer segment (e.g., by higher comonomer incorporation, regioregularity, or atactic polymer formation), the highly crystalline polymer segment will preferentially fill the terminal portion of the (copolymer) polymer. Not only is the resulting end-capping group crystalline, but upon termination, the catalyst sites that form the highly crystalline polymer can be used again to reinitiate polymer formation. Thus, the initially formed polymer is another highly crystalline polymer segment. Therefore, both ends of the resulting multiblock copolymer are preferably highly crystalline.

The ethylene alpha-olefin interpolymers used in some embodiments are preferably ethylene with at least one C₃-C₂₀Interpolymers of alpha-olefins. Ethylene and C₃-C₂₀Copolymers of alpha-olefins are particularly preferred. The interpolymer may further comprise C₄-C₁₈Dienes and/or alkenylbenzenes. Unsaturated comonomers suitable for polymerization with ethylene include, for example, ethylenically unsaturated monomers, conjugated or non-conjugated dienes, polyenes, alkenylbenzenes, and the like. Examples of such comonomers include C₃-C₂₀Alpha-olefins such as propylene, isobutylene, 1-butene, 1-hexene, 1-pentene, 4-methyl-1-pentene, 1-heptene, 1-octene, 1-nonene, 1-decene, etc. Particularly preferred are 1-butene and 1-octene. Other suitable monomers include styrene, halo-or alkyl-substituted styrenes, vinylbenzocyclobutane, 1, 4-hexadiene, 1, 7-octadiene, and cycloalkanes (e.g., cyclopentene, cyclohexene, and cyclooctene).

While ethylene/α -olefin interpolymers are preferred polymers, other ethylene/olefin polymers may also be used. Olefins, as used herein, refer to a family of unsaturated hydrocarbon-based compounds having at least one carbon-carbon double bond. Any olefin may be used in the examples of the present invention, depending on the choice of catalyst. Preferably, the suitable olefin is C containing vinyl unsaturation₃-C₂₀Aliphatic and aromatic compounds, as well as cyclic compounds, such as cyclobutene, cyclopentene, dicyclopentadiene, and norbornene, including but not limited to, substituted with C at the 5 and 6 positions₁-C₂₀Hydrocarbyl or cycloalkyl substituted norbornenes. Also mixtures comprising such olefins and mixtures of such olefins with C₄-C₄₀Mixtures of diolefin compounds.

Examples of olefin monomers include, but are not limited to, propylene, isobutylene, 1-butene, 1-pentene, 1-hexene, 1-heptene, 1-octene, 1-nonene, 1-decene and 1-dodecene, 1-tetradecene, 1-hexadecene, 1-octadecene, 1-eicosene, 3-methyl-1-butene, 3-methyl-1-pentene, 4, 6-dimethyl-1-heptene, 4-vinylcyclohexene,vinylcyclohexane, norbornadiene, ethylidene norbornene, cyclopentene, cyclohexene, dicyclopentadiene, cyclooctene, C₄-C₄₀Dienes including, but not limited to, 1, 3-butadiene, 1, 3-pentadiene, 1, 4-hexadiene, 1, 5-hexadiene, 1, 7-octadiene, 1, 9-decadiene, other C₄-C₄₀Alpha-olefins, and the like. In certain embodiments, the alpha-olefin is propylene, 1-butene, 1-pentene, 1-hexene, 1-octene, or combinations thereof. While any hydrocarbon containing a vinyl group can potentially be used in embodiments of the present invention, practical issues such as monomer availability, cost, and the ability to conveniently remove unreacted monomer from the resulting polymer can become more problematic as the molecular weight of the monomer becomes too high.

The polymerization processes described herein are well suited for producing olefin polymers comprising monovinylidene aromatic monomers including styrene, o-methylstyrene, p-methylstyrene, t-butylstyrene, and the like. Specifically, interpolymers comprising ethylene and styrene can be prepared by following the teachings herein. Optionally, compositions comprising ethylene, styrene and C having improved properties can be prepared₃-C₂₀Alpha olefins (optionally including C)₄-C₂₀Diene).

Suitable non-conjugated diene monomers may be straight chain, branched chain or cyclic hydrocarbon dienes having from 6 to 15 carbon atoms. Examples of suitable non-conjugated dienes include, but are not limited to, linear acyclic dienes such as 1, 4-hexadiene, 1, 6-octadiene, 1, 7-octadiene, 1, 9-decadiene, branched chain acyclic dienes such as 5-methyl-1, 4-hexadiene; 3, 7-dimethyl-1, 6-octadiene; 3, 7-dimethyl-1, 7-octadiene and mixed isomers of dihydromyrcene and dihydroocimene, monocyclic alicyclic dienes such as 1, 3-cyclopentadiene; 1, 4-cyclohexadiene; 1, 5-cyclooctadiene and 1, 5-cyclododecadiene, and polycyclic alicyclic fused and bridged ring dienes, such as tetrahydroindene, methyltetrahydroindene, dicyclopentadiene, bicyclo- (2,2,1) -hepta-2, 5-diene; alkenyl, alkylene, cycloalkenyl, and cycloalkylene norbornenes, such as 5-methylene-2-norbornene (MNB); 5-propenyl-2-norbornene, 5-isopropylidene-2-norbornene, 5- (4-cyclopentenyl) -2-norbornene, 5-cyclohexylidene-2-norbornene, 5-vinyl-2-norbornene and norbornadiene. Among the dienes commonly used to prepare EPDM, particularly preferred dienes are 1, 4-Hexadiene (HD), 5-ethylidene-2-norbornene (ENB), 5-vinylidene-2-norbornene (VNB), 5-methylene-2-norbornene (MNB) and dicyclopentadiene (DCPD). Particularly preferred dienes are 5-ethylidene-2-norbornene (ENB) and 1, 4-Hexadiene (HD).

One class of desirable polymers that can be prepared according to embodiments of the present invention are ethylene, C₃-C₂₀Elastomeric interpolymers of alpha-olefins, especially propylene, and optionally one or more diene monomers. The preferred alpha-olefin for this embodiment of the invention is represented by the formula CH₂═ CHR, wherein R is a linear or branched alkyl group having 1 to 12 carbon atoms. Examples of suitable alpha-olefins include, but are not limited to, propylene, isobutylene, 1-butene, 1-pentene, 1-hexene, 4-methyl-1-pentene, and 1-octene. A particularly preferred alpha-olefin is propylene. Propylene-based polymers are commonly referred to in the art as EP or EPDM polymers. Suitable dienes for use in preparing such polymers, especially multi-block EPDM type polymers, include conjugated or non-conjugated dienes comprising from 4 to 20 carbons, straight or branched chain dienes, cyclic or polycyclic dienes. Preferred dienes include 1, 4-pentadiene, 1, 4-hexadiene, 5-ethylidene-2-norbornene, dicyclopentadiene, cyclohexadiene and 5-butylidene-2-norbornene. A particularly preferred diene is 5-ethylidene-2-norbornene.

Because the diene-containing polymer includes alternating segments or blocks containing greater or lesser amounts of diene (including no diene) and alpha-olefin (including no alpha-olefin), the total amount of diene and alpha-olefin can be reduced without loss of subsequent polymer properties. That is, because the diene and alpha-olefin monomers are preferentially incorporated into one type of block of the polymer, rather than being homogeneously or randomly incorporated throughout the polymer, they are more efficiently utilized and the crosslink density of the polymer can be better controlled subsequently. Such crosslinkable elastomers and cured products have advantageous properties, including higher tensile strength and better elastic recovery.

In some embodiments, the weight ratio of the thus-formed blocks of the interpolymer prepared with the two catalysts incorporating different amounts of comonomer is from 95:5 to 5: 95. Desirably, the elastomeric polymer has an ethylene content of 20 to 90%, a diene content of 0.1 to 10%, and an alpha-olefin content of 10 to 80% by total weight of the polymer. Further preferably, the multi-block elastomeric polymer has an ethylene content of 60 to 90%, a diene content of 0.1 to 10% and an alpha-olefin content of 10 to 40% by total weight of the polymer. Preferred polymers are high molecular weight polymers having a weight average molecular weight (Mw) of 10,000 to 2,500,000, preferably 20,000 to 500,000, more preferably 20,000 to 350,000, and a polydispersity of less than 3.5, more preferably less than 3.0, and a mooney viscosity (ML (1+4)125 ℃) of 1 to 250. More preferably, such polymers have an ethylene content of 65 to 75%, a diene content of 0 to 6% and an alpha-olefin content of 20 to 35%.

The ethylene/a-olefin interpolymer may be functionalized by incorporating at least one functional group in its polymer structure. Exemplary functional groups can include, for example, ethylenically unsaturated mono-and difunctional carboxylic acids, ethylenically unsaturated mono-and difunctional carboxylic anhydrides, salts thereof, and esters thereof. Such functional groups can be grafted to the ethylene/a-olefin interpolymer, or it can be copolymerized with ethylene and optionally additional comonomers to form an interpolymer of ethylene, functional comonomer, and optionally one or more other comonomers. Means for grafting functional groups to polyethylene are described, for example, in U.S. Pat. nos. 4,762,890, 4,927,888, and 4,950,541, the disclosures of which are incorporated herein by reference in their entirety. One particularly useful functional group is maleic anhydride.

The amount of functional groups present in the functional interpolymer can vary. The functional groups may generally be present in the copolymer-type functionalized interpolymer in an amount of at least 1.0 weight percent, preferably at least 5 weight percent, and more preferably at least 7 weight percent. The functional groups will generally be present in the copolymer-type functionalized interpolymer in an amount less than 40 weight percent, preferably less than 30 weight percent, and more preferably less than 25 weight percent.

Exemplary olefin block copolymers include ethylene and octene. A commercially available olefin block copolymer that may be used in the foam is INFUSE from Dow Chemical company^TM。

Another exemplary ethylene as an elastomer is a homogeneously branched ethylene-alpha-olefin copolymer. These copolymers can be prepared with single site catalysts, such as metallocene catalysts or constrained geometry catalysts, and typically have melting points less than 105 ℃, specifically less than 90 ℃, more specifically less than 85 ℃, even more specifically less than 80 ℃ and still more specifically less than 75 ℃. Melting points are measured by Differential Scanning Calorimetry (DSC) as described, for example, in USP 5,783,638. The alpha-olefin is preferably C_3-20Linear, branched or cyclic alpha-olefins. C_3-20Examples of the α -olefin include propylene, 1-butene, 4-methyl-1-pentene, 1-hexene, 1-octene, 1-decene, 1-dodecene, 1-tetradecene, 1-hexadecene, and 1-octadecene. The alpha-olefins may also contain cyclic structures such as cyclohexane or cyclopentane, thereby producing alpha-olefins such as 3-cyclohexyl-1-propene (allylcyclohexane) and vinylcyclohexane.

Exemplary homogeneously branched ethylene-a-olefin copolymers include ethylene/propylene, ethylene/butene, ethylene/1-hexene, ethylene/1-octene, ethylene/styrene, and the like. Exemplary terpolymers include ethylene/propylene/1-octene, ethylene/propylene/butene, ethylene/butene/1-octene, and ethylene/butene/styrene. The copolymer may be a random copolymer or a block copolymer.

Examples of commercially available homogeneously branched ethylene- α -olefin interpolymers include homogeneously branched, linear ethylene- α -olefin copolymers (e.g., TAFMER of Mitsui Petrochemicals Company Limited)^TMAnd EXACT from Exxon Chemical Company^TM) And homogeneously branched, substantially linear ethylene-alpha-olefin polymers (e.g., AFFINITY available from dow chemical company)^TMAnd ENGAGE^TMPolyethylene).

The elastomer (i.e., ethylene/a-olefin interpolymer) may be used in the foamable composition in an amount of from 60 to 90 wt%, preferably from 70 to 88 wt%, and more preferably from 80 to 85 wt%, based on the total weight of the foamable composition.

The composition also includes an unneutralized carboxylated olefin copolymer. In other words, the acid functionality in the carboxylated olefin copolymer is not neutralized with metal ions. The unneutralized carboxylated olefin copolymer plays a useful role in controlling cell size. The carboxylated olefin copolymer is not covalently or ionically bonded to the elastomer (olefin block or random copolymer) prior to undergoing the crosslinking reaction.

Carboxylated olefin copolymers include ethylene polymers having grafted thereto (or copolymerized thereto) an unsaturated carboxylic acid or anhydride, ester, amide or imide, hereinafter referred to as "graft compound". The grafting compound is preferably an aliphatic unsaturated dicarboxylic acid or anhydride. The carboxylic acid preferably contains at most 4, preferably at most 5 and more preferably at most 6 carbon atoms. Examples of unsaturated carboxylic acids are maleic acid, fumaric acid, itaconic acid, acrylic acid, methacrylic acid, crotonic acid and citraconic acid. Examples of derivatives of unsaturated carboxylic acids are maleic anhydride, citraconic anhydride, itaconic anhydride, methyl acrylate, methyl methacrylate, ethyl acrylate, ethyl methacrylate, butyl acrylate, butyl methacrylate, glycidyl acrylate, glycidyl methacrylate, monoethyl maleate, diethyl maleate, monomethyl fumarate, dimethyl fumarate, monomethyl itaconate, diethyl itaconate, acrylamide, methacrylamide, monomaleimide, dimaleamide, N-diethylmaleate, N-monobutylmaleimide, N-dibutylmaleimide, monofumaramide, difumalamide, N-monoethylfumaramide, N-diethylfumaramide, N-monobutylfumamide, N-dibutylfumaramide, N-monoethylfumaramide, N-diethylfumaramide, N-monobutylfumalamide, N-dibutylfumaramide, Maleimide, N-butylmaleimide, N-phenylmaleimide, sodium acrylate, sodium methacrylate, potassium acrylate, and potassium methacrylate.

Examples of the carboxylated olefin copolymer include an ethylene/(meth) acrylic acid copolymer, an ethylene/(meth) acrylic acid/n-butyl (meth) acrylate copolymer, an ethylene/(meth) acrylic acid/isobutyl (meth) acrylate copolymer, an ethylene/(meth) acrylic acid/t-butyl (meth) acrylate copolymer, an ethylene/(meth) acrylic acid/methyl (meth) acrylate copolymer, ethylene/(meth) acrylic acid ethyl ester copolymers, ethylene/maleic acid and ethylene/maleic acid monoester copolymers, ethylene/maleic acid monoester/(meth) acrylic acid n-butyl ester copolymers, ethylene/maleic acid monoester/(meth) acrylic acid methyl ester copolymers, ethylene/maleic acid monoester/(meth) acrylic acid ethyl ester copolymers, or combinations of two or more thereof.

One or more, preferably one, grafting compounds are grafted onto the ethylene polymer. Maleic anhydride is the preferred grafting compound. Exemplary unsaturated carboxylic acids are acrylic acid or methacrylic acid. In one embodiment, ethylene/(meth) acrylic acid copolymers are preferred.

The grafting process may be initiated by decomposing the initiator to form free radicals, including azo-containing compounds, carboxylic peroxy acids and esters, alkyl hydroperoxides, and dialkyl and diacyl peroxides, among others. Many of these compounds and their properties have been described (ref: J. Brandrup, E.Immergut, E.Grulke editors, "Handbook of polymers (Polymer Handbook)", 4 th edition, Wiley Press (Wiley), New York (New York),1999, section II, pages 1-76). Alternatively, the grafted compound may be copolymerized with ethylene by typical tubular and autoclave processes.

The grafted ethylene polymer and the ethylene polymer used for grafting are selected from the group consisting of Ultra Low Density Polyethylene (ULDPE), Low Density Polyethylene (LDPE), Linear Low Density Polyethylene (LLDPE), Medium Density Polyethylene (MDPE), High Density Polyethylene (HDPE), high melt strength high density polyethylene (HMS-HDPE), Ultra High Density Polyethylene (UHDPE) or combinations thereof.

In one embodiment, the density of the grafted ethylene polymer and the ethylene polymer used for grafting is preferably at most 0.94g/cm³More preferably 0.850 to 0.935g/cm³Most preferably 0.860 to 0.930g/cm³In particular from 0.865 to 0.930g/cm³. However, it should be understood thatThe polymer density changed slightly upon grafting. In the case of ethylene polymers, it has been found that polymer density is important to provide primers with sufficient mechanical strength and flexibility and to achieve sufficient solubility of the grafted ethylene polymer in organic solvents.

The carboxylated olefin copolymer has a melt index of less than or equal to 5 grams per 10 minutes, preferably less than or equal to 4 grams per 10 minutes and more preferably less than or equal to 3 grams per 10 minutes, when measured at 2.16kg and 190 ℃ according to ASTM D1238. In one embodiment, the carboxylated olefin copolymer has a melt index greater than, or equal to, 1 gram per 10 minutes when measured at 2.16kg and 190 ℃ according to ASTM D1238.

An example of a carboxylated olefin copolymer is PRIMACOR^TMAn ethylene-methacrylic acid copolymer commercially available from Dow chemical company orIt is commercially available from DuPont Chemical Company (DuPont Chemical Company). The carboxylated olefin copolymer used herein is an ethylene methacrylic acid copolymer (E-MAA) in an amount of from 3 to 20 wt%, preferably from 4 to 15 wt% and more preferably from 5 to 10 wt%, based on the total weight of resin in the foamable composition.

The foamable composition also contains a crosslinking agent. The crosslinking agent comprises one or more organic peroxides, comprising dialkyl peroxides, peroxyesters, peroxydicarbonates, peroxyketals, diacyl peroxides, or a combination of two or more thereof. Examples of peroxides include dicumyl peroxide (also known as α, α' -bis (t-butylperoxy) diisopropylbenzene (BIPB)), bis (3,3, 5-trimethylhexanoyl) peroxide, t-butyl peroxypivalate, t-butyl peroxyneodecanoate, di (sec-butyl) peroxydicarbonate, t-amyl peroxyneodecanoate, 1-di-t-butylperoxy-3, 3, 5-trimethylcyclohexane, t-butyl-cumyl peroxide, 2, 5-dimethyl-2, 5-di (t-butyl-peroxy) hexane, 1, 3-bis (t-butyl-peroxy-isopropyl) benzene, or a combination thereof. Exemplary crosslinking agents are under the trade nameCommercially available from Arkema toCommercially available from arkema or under the trade nameDicumyl peroxide, commercially available from Akzo Nobel corporation (Akzo Nobel).

The cross-linking agent is used in an amount of 0.05 to 10 wt%, preferably 0.3 to 5 wt% and more preferably 0.5 to 3 wt%, based on the total weight of the foamable composition.

The foamable composition may also contain a suitable blowing agent to generate porosity upon heating to form a foam. It is desirable to use a blowing agent that decomposes (to release gas) at about the same temperature at which the crosslinking agent decomposes. This allows the formation of a foam, followed by crosslinking, which facilitates the retention of porosity in the foam. It is generally desirable to use the blowing agent in an amount effective to produce a fairly uniform cell size in the foam. Blowing agents generally work in conjunction with curing agents to promote uniform crosslink density and uniform pore size in the foam. The blowing agent may be a physical blowing agent or a chemical blowing agent. Physical blowing agents are released from the composition as a result of the binodal decomposition and expand during the foaming process to form a foam, while chemical blowing agents decompose during the foaming process to release a gas (e.g., an azo compound) to form a foam.

Physical blowing agents that include a hydrogen atom-containing component can be used alone or as a mixture with each other or another type of blowing agent (e.g., a chemical blowing agent), such as an azo compound. Physical blowing agents may be selected from a wide range of materials, including hydrocarbons, ethers, esters and partially halogenated hydrocarbons (e.g., perfluorinated hydrocarbons), ethers and esters, and the like. The physical blowing agent may also comprise a relatively inert gas such as nitrogen, argon, carbon dioxide, and the like. Typical physical blowing agents have a boiling point between-50 ℃ and 100 ℃ and preferably between-50 ℃ and 50 ℃. Among the hydrogen-containing blowing agents that may be used are HCFCs (halogenated chlorofluorocarbons), such as 1, 1-dichloro-1-fluoroethane, 1-dichloro-2, 2, 2-trifluoroethane, chlorodifluoromethane and 1-chloro-1, 1-difluoroethane; HFC (halofluorocarbon), such as 1,1,1,3,3, 3-hexafluoropropane, 2,2,4, 4-tetrafluorobutane, 1,1,1,3,3, 3-hexafluoro-2-methylpropane, 1,1,1,3, 3-pentafluoropropane, 1,1,1,2, 2-pentafluoropropane, 1,1,1,2, 3-pentafluoropropane, 1,1,2,3, 3-pentafluoropropane, 1,1,2,2, 3-pentafluoropropane, 1,1,3,3, 4-hexafluorobutane, 1,1,1,3, 3-pentafluorobutane, 1,1,1,4, 4-hexafluorobutane, 1,1,4, 4-pentafluorobutane, 1,1,2,2,3, 3-hexafluoropropane, 1,1,1,2,3, 3-hexafluoropropane, 1, 1-difluoroethane, 1,1,1, 2-tetrafluoroethane and pentafluoroethane; HFEs (halofluoroethers), such as methyl-1, 1, 1-trifluoroethyl ether and difluoromethyl-1, 1, 1-trifluoroethyl ether; and hydrocarbons such as n-pentane, isopentane, cyclopentane, and the like.

Gaseous non-CFC or non-HCFC physical blowing agents, e.g. carbon dioxide, nitrogen, dinitroso-pentamethylene-tetramine, SF₆Nitrous oxide, argon, helium, noble gases such as xenon, air (nitrogen and oxygen blends) and blends of these gases. The gas can be used as blowing agent in the gaseous, liquid or supercritical state.

Chemical blowing agents including Azobisisobutyronitrile (AIBN), azodicarbonamide, dinitroso-pentamethylene-tetramine, p-toluenesulfonyl hydrazide, p' -oxy-bis (benzenesulfonyl hydrazide), or combinations thereof may be used to create the foam. An exemplary azo compound is azobisisobutyronitrile. The blowing agent can also be a mixture of blowing agents or a mixture of blowing agent and activator in order to adjust the expansion-decomposition temperature and the foaming process.

The blowing agent is used in an amount of 0.1 to 10 wt%, preferably 1 to 5 wt% and more preferably 2 to 4 wt%, based on the total weight of the foamable composition.

The weight ratio of unneutralized carboxylated olefin polymer to blowing agent is generally reduced when compared to the weight ratio of neutralized carboxylated olefin polymer to blowing agent in order to achieve the same foam density at which the mechanical properties can be compared. In one embodiment, the weight ratio of unneutralized carboxylated olefin polymer to blowing agent is from 0.01 to 4.0, preferably from 0.2 to 3.0 and more preferably from 1 to 2.

The foamable composition may also contain 0.1 to 10 wt%, preferably 0.2 to 5 wt% and more preferably 0.3 to 4 wt% of an activator to reduce the decomposition temperature/profile of the blowing agent. The activator may be one or more metal oxides, metal salts, metal hydroxides, or organometallic complexes, or combinations thereof. Examples of activators are zinc oxide, zinc stearate, magnesium hydroxide, calcium carbonate, and the like, or combinations thereof. The activator may facilitate neutralization of the carboxylic acid during the reaction to produce foam. This may improve the compressive strength of the foam.

In one embodiment, the weight ratio of activator to carboxylated olefin copolymer is greater than or equal to 0.3, preferably greater than or equal to 0.4 and more preferably greater than or equal to 0.45. In one embodiment, the weight ratio of activator to carboxylated olefin copolymer is less than 0.8, preferably less than or equal to 0.77 and more preferably less than or equal to 0.75.

Other additives that may be present in the composition at 0.1 to 20 or 2 to 12 weight percent based on the total weight of the composition may comprise pigments (TiO)₂And other compatible color pigments), adhesion promoters (to improve adhesion of the expanded foam to other materials), fillers (e.g., calcium carbonate, barium sulfate, and/or silica), nucleating agents (in pure or concentrated form, e.g., CaCO)₃、SiO₂Or a combination of two or more thereof), rubber (to improve rubber-like elasticity, such as natural rubber, SBR, polybutadiene, and/or ethylene propylene diene terpolymers), stabilizers (e.g., antioxidants, UV absorbers, and/or flame retardants), and processing aids (e.g., Octene R-130 manufactured by octenes Co. The antioxidant (to alter organoleptic properties, such as to reduce odor or taste) may comprise a phenolic antioxidant, such as IRGANOX from babagkis (Ciba Geigy Inc., japan).

In one embodiment, the foamable composition may optionally contain a poly (ethylene vinyl acetate) copolymer. The poly (ethylene vinyl acetate) copolymer may have a melt index of 2 to 3 grams per 10 minutes (grams/10 minutes) as measured according to ASTM D1238 and may contain Vinyl Acetate (VA) in an amount of 8 to 50 weight percent, preferably 9 to 40 weight percent, based on the total weight of poly (ethylene vinyl acetate) copolymer present in the foamable composition.

Specifically, the resin may be an Ethylene Vinyl Acetate (EVA) copolymer. Commercially available poly (ethylene vinyl acetate) copolymers include, for example, AT Polymers 1070C (9 wt% Vinyl Acetate (VA)), AT Polymers 1710(17 wt% VA), AT Polymers 2306(23 wt% VA), AT Polymers2803 (28% VA), AT Polymers 2810(28 wt% VA), Chevron/Ace Plastics TD 3401(9.5 wt% VA), Chevron/Ace Plastics DS 4089-70 (18% VA), DuPont40W(40wt％VA)、DuPont140-W(33wt％VA)、DuPont250-W(28wt％VA)、DuPont260(28wt％VA)、DuPont350(25wt％VA)、DuPont360(25wt％VA)、DuPont450(18wt％VA)、DuPont460(18wt％VA)、DuPont550(15wt％VA)、DuPont560(15wt％VA)、DuPont650(12wt％VA)、DuPont660(12wt％VA)、750(9wt％VA)、DuPont760(9.3wt％VA)、DuPont770(9.5wt％VA)、ExxonLD-740(24.5wt％VA)、ExxonLD-724(18wt％VA)、ExxonLD-721.62(19.3wt％VA)、ExxonLD-721.88(19.3wt％VA)、ExxonLD-721(19.3wt％VA)、ExxonLD-740(24.5wt％VA)、ExxonLD-318(9wt％VA)、ExxonLD-319.92(9wt％VA)、ExxonLD-725、Quantum UE 630-000(17wt％VA)、Quantum 637-000(9wt％VA)、X1903(10wt％VA)、X0901(12wt％VA)、X0911(18wt％VA)、7360M (21 wt% VA), from DuPont chemical company2288(21 wt% VA) andX0915(9wt％VA)。

the poly (ethylene vinyl acetate) copolymer can optionally be present in the foamable composition in an amount of 20 to 40 wt%, preferably 25 to 35 wt%, and more preferably 27 to 33 wt%, based on the total weight of the foamable composition.

Foams can be produced by a variety of methods, such as compression molding, injection molding, or a combination of extrusion and molding. The foamable composition can be made by blending together the elastomer, the carboxylated olefin copolymer, the crosslinking agent, the blowing agent, and any other desired additives. The blending may be carried out in an extruder or an internal mixer, or alternatively, the ingredients may be extruded in an extruder or pre-blended in a dry mixer prior to mixing in an internal mixer.

In one embodiment, making the foam may include mixing the elastomer, the carboxylated olefin copolymer, the blowing agent, and the crosslinking agent under heat to form a melt. This can be done in a Banbury (Banbury), an intensive mixer, a two-roll mill, or an extruder. The time, temperature, shear rate can be adjusted to ensure optimum dispersion without premature crosslinking or foaming. The high temperature of mixing may lead to premature crosslinking and foaming due to decomposition of the peroxide and blowing agent. Sufficient temperature may be required to ensure good mixing and dispersion of the other ingredients. The upper temperature limit for safe operation may depend on the initial decomposition temperature of the peroxide and blowing agent employed. The ingredients can form a homogeneous mixture when blended at a temperature of 60 ℃ to 150 ℃, preferably 70 ℃ to 140 ℃, and more preferably 80 ℃ to 130 ℃ and even more preferably 90 ℃ to 120 ℃. The polymer may be melt blended prior to compounding with one or more other ingredients.

After mixing, shaping may be performed. Plate rolls or calender rolls are commonly used to make appropriately sized plates for foaming. The composition may be formed into pellets using an extruder.

Foaming can be carried out in a compression or injection mold at a temperature and time to complete decomposition of the peroxide and blowing agent. The pressure, molding temperature and heating time can be controlled. Foaming can be carried out in an injection molding apparatus by using the foamable composition in pellet form. The resulting foam may be further formed into finished dimensions by any means known in the art, such as by thermoforming and compression molding.

The foams produced from the compositions can be substantially closed cell and can be used in a variety of articles, including footwear applications (e.g., midsoles or insoles), automotive seats and interiors, furniture armrests, railroad pads, and other industrial foam material applications.

Foamable compositions and methods of making the same are disclosed by the following non-limiting examples.

Examples of the invention

This example was conducted to demonstrate the preparation of the disclosed foamable compositions and their properties. The materials used in the examples and comparative examples are detailed in table 1 below.

TABLE 1

The ingredients are mixed together by an internal mixer. The formulated compound was then prepared in a two-roll mill and then foamed into plastic blocks. The prepared foam plaques were cut to the appropriate size for further testing. The compounding and plastic block foaming manufacturing operations are detailed below.

The foamable composition was compounded as follows. The polymer pellets (the compositions of which are shown in tables 2 and 3 below) were added to a 1.5 liter banbury mixer. After the polymer melted (about 5 minutes), fillers including zinc oxide (ZnO), zinc stearate (ZnSt), and talc were added to the banbury. The blowing agent and peroxide were finally added, after the filler was homogeneously dispersed, and the contents were mixed for an additional 3 to 5 minutes, for a total mixing time of 15 minutes. Immediately after the compound expulsion, the batch temperature was checked by using a thermal probe detector. The actual temperature of the composition is typically 10 to 15 c higher than the temperature exhibited on the equipment (the actual composition temperature is about 120 c). Therefore, it is desirable to maintain a lower display temperature during the compounding process to ensure that the compound temperature does not exceed the decomposition temperature of the curing agent and the decomposition temperature of the blowing agent. The compounded formulation was then placed between two roll mills (maintained at a temperature of about 120 ℃) and the compounded formulation was formed into a platemaking (or roll-milled blanket) having a thickness of about 5 mm.

The plastic bun foam manufacture is detailed below. The roll-milled carpet was cut into squares (three or four "6 inch x 6 inch" squares) and placed in a preheated plastic bun foam mold having dimensions of about 49 square inches. The surface of the die case is sprayed with a release agent to avoid the foam sticking to the die case during demolding. Two compression molding processes are involved: first, a pre-heating process to eliminate air pockets inside the sample and between stacked cover layers prior to curing, and then a second heating step to facilitate the curing/foaming process. Preheating at 110 deg.C (low melting point polymers, e.g. ENGAGE)^TMPOE orEVA) or 120 deg.C (high melting point polymers, e.g. INFUSE)^TMOBC) was performed for 8 minutes and pressed for 4 minutes at 10 tons to form a solid mass in the mold before foaming. The preheated mass was transferred to the foaming press and was at 100kg/cm²And held at 180 ℃ for 8 minutes. Once the pressure was released, the bun foam was quickly removed from the tray and placed in a ventilation hood over several nonstick pallets and the top side length was measured as quickly as possible. The foam surface needs to be isolated from the counter top using a cardboard box. Insulating the surface of the newly formed plastic bun foam prevents uneven cooling on the top and bottom surfaces. The foam was cooled in a fume hood for 40 minutes before it was transferred to a storage vessel and allowed to cool for 24 hours.

The following tests were performed on the foamed compositions.

Foam density: the bun foam was weighed to 0.1g accuracy and the volume determined by measuring length, width and thickness to 0.01 cm. The density can be calculated from weight and volume.

Compression set: compression Set (C-Set) was measured according to ASTM D395 method B at 50 ℃ for 6 hours under 50% compression conditions. Two buttons per foam were tested and the average value reported. The compression set is calculated by using the following equation:

compression set ═ T₁-T₂)/(T₁-T₀)*100％

Wherein T is₀Is the separation distance of the devices, T₁Is the sample thickness before testing, and T₂Is the sample thickness after the test.

Asker C hardness: the Asker C hardness test was performed according to ASTM D2240. Hardness is the average of five readings (5 second wait time) measured across the surface of the sample and measured again after 40 minutes of aging at both 70 ℃ and 100 ℃.

Split tear resistance: the split tear strength was measured according to ASTM D3574 at a test speed of 2 inches/minute by using samples with dimensions 6 "(length) × 1" (width) × 0.4 "(thickness) and a cut depth of 1 to 1.5".

Compressive strength: compressive strength was performed according to ASTM D1621. Round foam samples of 29mm diameter were pressed at a uniform rate of 1 mm/min. The stress required to produce a compressive strain of up to 25% was determined. Where the compressive strength is given by the force per unit area based on the original foam cross-section.

Table 2 lists compositions of Inventive Examples (IE) and Comparative Examples (CE). All values for the corresponding compositions are parts per hundred. The comparative examples (CE-1 to CE-4) did not contain any carboxylated olefin copolymer. Inventive examples (IE-1 through IE-6) all contained carboxylated olefin copolymer in an amount of 5 weight percent or 10 weight percent based on the total weight of resin in the foamable composition.

Table 2 lists inventive examples based on the present invention and corresponding comparative examples. CE-1 to CE-4 are comparative examples based on OBC without any acid-containing polymer. IE-1 through IE-3 and IE-4 through IE-6 are examples of the present invention having a similar composition as CE-1, except that they contain 5(IE-1 through IE-3) and 10phr (IE-4 through IE-6) of the acid-containing polymer. The experimental results of the inventive samples (IE-1 to IE-3 and IE-4 to IE-6) and the comparative samples (CE-1 to CE-4) are shown in Table 3 below.

Table 3 lists other comparative foamable compositions (CE-5 to CE-7) in which polyethylene vinyl acetate was used in place of INFUSE^TMOlefin block copolymers are used as elastomers.

TABLE 2 (formulations of inventive and comparative foam examples)

TABLE 3 (formulation of EVA and EVA/E-MAA blend based foam)

Composition (I)	CE-5	CE-6	CE-7
				EVA	100	95	90
E-MAA		5	10
				R103(TiO2)	2.5	2.5	2.5
RB510 (Talc)	5	5	5
				ZnSt	1	1	1
ZnO	1.5	1.5	1.5
				AC 6000HG	2.6	2.2	1.8
F40P(BIPB)	1.375	1.375	1.375
				Density, g/cc	0.199	0.197	0.201

FIG. 2 depicts the cure profile measured by a Moving Die Rheometer (MDR) at the same peroxide level for Olefin Block Copolymer (OBC) systems with or without ethylene-methacrylic acid (E-MAA) copolymers. FIG. 2 is a graph depicting the MDR cure torque of OBC systems with (IE-1 and IE-4) or without (CE-3) E-MAA copolymer. The addition of E-MAA significantly improved the level of cure. In contrast, in the EVA system (see fig. 3), the curing behavior is quite different from that observed in the OBC system. FIG. 3 is a graph depicting the MDR cure torque of EVA systems with and without (CE-5 to CE-7) E-MAA copolymers. The EVA/E-MAA system showed a lower cure level at the start and then exceeded the EVA cure curve after 5 minutes.

FIG. 4 is a graph of foam hardness for OBC foams with and without E-MAA at different foam densities. At the same density, the addition of 5 or 10phr of E-MAA significantly improved the foam hardness (fig. 4), which is particularly useful for lightweight foams where the hardness should still not be compromised (i.e., not reduced).

FIG. 5 compares the compression force of OBC foam with and without E-MAA copolymer at different foam densities. FIG. 5 is a graph of foam compressive strength of OBC foams with and without E-MAA. Foams based on OBC/E-MAA exhibit higher compressive forces across the entire density range (0.15g/cc to 0.2 g/cc). The increased compressive strength indicates a better support capability of the foamed midsole for the human body. The lower the foam density, the more difficult it is for the foam to exhibit any supporting ability. The increase in compressive force means that at the same rate of foam deformation, the midsole can support a higher weight or the foam can deform less at the same compressive force.

The property that reflects the durability of the foam is compression set recovery. FIG. 6 is a graph of compression set versus cross-sectional tear at different foam densities for OBC foams with and without E-MAA. In general, compression set resistance (better durability) will be improved, but split tear will be compromised with increasing level of cure and it is difficult to achieve balance in light weight foams. In the present invention, the plot of compression set versus section tear indicates that the addition of E-MAA can produce lower compression set at a given section tear strength.

FIG. 7 is a graph of compression set versus foam density for OBC and EVA foams with or without E-MAA. FIG. 7 summarizes the compression set of OBC or EVA systems with or without E-MAA at different foam densities. In OBC systems, the addition of E-MAA significantly improves compression set resistance (i.e., it exhibits a lower percentage of compression set) compared to pure OBC foam (without E-MAA). However, in EVA systems, the compression set values are high and even increase due to the reduced cure level.

FIG. 8 is a spider graph comparing the foam performance of CE-2 and IE-6. It is clear that IE-6 provides higher tear resistance at much lower densities while still maintaining other performance characteristics.

These experiments indicate that as the amount of ethylene methacrylic acid in the foamable composition increases and the ratio of activator to carboxylic acid copolymer is higher, the foam expansion ratio remains similar and the corresponding foam density can remain less than or equal to 0.23g/cc, preferably less than or equal to 0.22g/cc or more preferably less than or equal to 0.20 g/cc.

As can be seen from the figure, the Asker C hardness of the disclosed foams is 40 to 60. In one embodiment, the Asker C hardness of the disclosed foam, measured according to ASTM D2240, is greater than 42, preferably greater than 43 and more preferably greater than 44.

The foam also exhibits a compression set of less than 50% as measured according to ASTM D395 method B. The foam was shown to have a split tear of greater than 2.4N/mm as measured by ASTM D3574.

The foam has a density of greater than or equal to about 0.15g/cc, preferably greater than or equal to about 0.16g/cc, preferably greater than or equal to about 0.17g/cc, preferably greater than or equal to about 0.18 g/cc. The foam can have a density of less than or equal to 0.23g/cc and less than or equal to 0.22 g/cc. These properties make the foam suitable for footwear for use as a sole.