Polyethylene compositions and films having good permeability, stiffness and sealability

文档序号：834957 发布日期：2021-03-30 浏览：10次中文

阅读说明：本技术 具有良好的渗透性、刚度和密封性的聚乙烯组合物和膜 (Polyethylene compositions and films having good permeability, stiffness and sealability ) 是由 X·王 P·佐里卡克 B·莫洛伊 Q·王 L·瓦纳赛尔唐克 N·奥比于 2019-07-03 设计创作，主要内容包括：一种聚乙烯组合物,其包含：第一聚乙烯,其为乙烯共聚物,重均分子量M-w为70,000至250,000,分子量分布M-w/M-n＜2.3；第二聚乙烯,其为乙烯共聚物或均聚物,重均分子量M-w为15,000至100,000,分子量分布M-w/M-n＜2.3；和第三聚乙烯,其为乙烯共聚物或均聚物,重均分子量M-w为70,000至250,000,分子量分布M-w/M-n＞2.3；其中第一聚乙烯的短链分支多于第二聚乙烯或第三聚乙烯。所述聚乙烯组合物在CEF分析中具有至少为10重量％的可溶性级分。由该聚乙烯组合物制备的膜的纵向1％正割模量≥190 MPa(膜厚约1密耳下)、密封起始温度(SIT)≤100℃(膜厚约2密耳下)、热粘窗口面积(AHTW)≥160牛顿#℃(膜厚约2密耳下)、氧气透过率(OTR)≥650 cm～3/100平方英寸(膜厚约1密耳下)。(A polyethylene composition comprising: a first polyethylene which is an ethylene copolymer having a weight average molecular weight M w Is 70,000 to 250,000, molecular weight distribution M w /M n Less than 2.3; a second polyethylene which is an ethylene copolymer or homopolymer, having a weight average molecular weight M w 15,000 to 100,000, molecular weight distribution M w /M n Less than 2.3; and a third polyethylene which is an ethylene copolymer or homopolymer, having a weight-average molecular weight M w Is 70,000 to 250,000, molecular weight distribution M w /M n Is more than 2.3; wherein the first polymerThe ethylene has more short chain branching than the second or third polyethylene. The polyethylene composition has a soluble fraction of at least 10 wt% in the CEF analysis. Films made from the polyethylene composition have a 1% secant modulus in the machine direction of greater than or equal to 190 MPa (at about 1 mil film thickness), a Seal Initiation Temperature (SIT) of less than or equal to 100 ℃ (at about 2 mil film thickness), a hot tack window Area (AHTW) of greater than or equal to 160 Newton ∙ ℃ (at about 2 mil film thickness), and an Oxygen Transmission Rate (OTR) of greater than or equal to 650 cm 3 100 square inches (film thickness about 1 mil).)

1. A polyethylene composition comprising:

5 to 80% by weight of a first polyethylene which is an ethylene copolymer, the weight-average molecular weight M of the first polyethylene_wIs 70,000 to 250,000, molecular weight distribution M_w/M_n< 2.3 and having 5 to 100 short chain branches per thousand carbon atoms;

5 to 80% by weight of a second polyethyleneWhich is an ethylene copolymer or ethylene homopolymer, the second polyethylene having a weight-average molecular weight M_w15,000 to 100,000, molecular weight distribution M_w/M_n< 2.3 and having 0 to 20 short chain branches per thousand carbon atoms; and

5 to 80% by weight of a third polyethylene which is an ethylene copolymer or an ethylene homopolymer, the third polyethylene having a weight-average molecular weight M_wIs 70,000 to 250,000, molecular weight distribution M_w/M_n> 2.3 and has 0 to 50 short chain branches per thousand carbon atoms; wherein

Number of short chain branches per thousand carbon atoms in the first polyethylene (SCB)_PE-1) Greater than the number of short chain branches per thousand carbon atoms in the second polyethylene (SCB)_PE-2) And the number of short chain branches per thousand carbon atoms in the third polyethylene (SCB)_PE-3)；

Number of short chain branches per thousand carbon atoms in the third polyethylene polymer (SCB)_PE-3) Greater than the number of short chain branches per thousand carbon atoms in the second polyethylene (SCB)_PE-2) (ii) a And is

The weight average molecular weight of the second polyethylene is less than the weight average molecular weight of the first polyethylene and the third polyethylene; wherein the content of the first and second substances,

the polyethylene composition has a density of 0.939 g/cm or less³Melt index I₂0.1 to 10 dg/min, melt flow ratio I₂₁/I₂Less than 40 and having a soluble fraction of at least 10% by weight in a Crystallization Elution Fractionation (CEF) analysis.

2. The polyethylene composition of claim 1, wherein the polyethylene composition has a monomodal distribution in Gel Permeation Chromatography (GPC).

3. The polyethylene composition of claim 1, wherein the polyethylene composition has a solubility fraction in a Crystallization Elution Fraction (CEF) analysis of at least 15 wt%.

4. The polyethylene composition of claim 1, wherein the polyethylene composition has a melting peak temperature in Differential Scanning Calorimetry (DSC) analysis at greater than 125 ℃.

5. The polyethylene composition of claim 1 wherein the first polyethylene has 30 to 75 short chain branches per thousand carbon atoms.

6. The polyethylene composition of claim 1 wherein the second polyethylene is an ethylene homopolymer.

7. The polyethylene composition of claim 1 wherein the third polyethylene is an ethylene copolymer and has 5 to 30 short chain branches per thousand carbon atoms.

8. The polyethylene composition of claim 1, wherein the first polyethylene has a weight average molecular weight M_wFrom 75,000 to 200,000.

9. The polyethylene composition of claim 1 wherein the second polyethylene has a weight average molecular weight, M_wFrom 25,000 to 75,000.

10. The polyethylene composition of claim 1 wherein the third polyethylene has a weight average molecular weight, M_wIs 80,000 to 200,000.

11. The polyethylene composition of claim 1 wherein the first polyethylene has a density of from 0.855 to 0.910 g/cm³。

12. The polyethylene composition of claim 1 wherein the second polyethylene is of a density of from 0.940 to 0.980 g/cm³The ethylene homopolymer of (1).

13. The polyethylene composition of claim 1 wherein the third polyethylene is of a density of from 0.880 to 0.936 g/cm³The ethylene copolymer of (1).

14. The polyethylene composition of claim 1, wherein the first polyethylene is present from 5 to 50 wt%.

15. The polyethylene composition of claim 1 wherein the second polyethylene is present from 5 to 60 weight percent.

16. The polyethylene composition of claim 1 wherein the third polyethylene is present from 15 to 85 weight percent.

17. The polyethylene composition of claim 1, wherein the first polyethylene is present from 10 to 40 wt%.

18. The polyethylene composition of claim 1 wherein the second polyethylene is present from 15 to 45 wt%.

19. The polyethylene composition of claim 1 wherein the third polyethylene is present from 20 to 80 weight percent.

20. The polyethylene composition of claim 1 wherein the CDBI of the first polyethylene₅₀At least 75 wt%.

21. The polyethylene composition of claim 1 wherein the third polyethylene is CDBI₅₀Less than 75wt% of a copolymer.

22. The polyethylene composition of claim 1 wherein the first polyethylene is a homogeneously branched ethylene copolymer.

23. The polyethylene composition of claim 1 wherein the third polyethylene is a heterogeneously branched ethylene copolymer.

24. The polyethylene composition of claim 1 wherein the first polyethylene is produced with a single site catalyst.

25. The polyethylene composition of claim 1 wherein the second polyethylene is produced with a single site catalyst.

26. The polyethylene composition of claim 1, wherein the third polyethylene is produced with a ziegler-natta catalyst.

27. The polyethylene composition of claim 1, wherein the polyethylene composition has a molecular weight distribution, M_w/M_nIs 2.1 to 5.5.

28. The polyethylene composition of claim 1, wherein the polyethylene composition has a molecular weight distribution, M_w/M_nIs 2.1 to 4.5.

29. The polyethylene composition of claim 1, wherein the polyethylene composition has a density of < 0.935 g/cm³。

30. The polyethylene composition of claim 1, wherein the polyethylene composition has a density of from 0.880 to 0.932g/cm³。

31. The polyethylene composition of claim 1, wherein the polyethylene composition has a melt index, I₂Is 0.1 to 3.0 dg/min.

32. The polyethylene composition of claim 1, wherein the M of the polyethylene composition_Z/M_wLess than 3.00.

33. The polyethylene composition of claim 1, wherein the polyethylene composition has a melt index ratio I₂₁/I₂From 20 to 40.

34. A film layer having a thickness of 0.5 to 10 mils comprising the polyethylene composition of claim 1.

35. The film layer of claim 34, wherein the film layer has a 1% secant modulus in the Machine Direction (MD) of greater than or equal to 190 MPa when measured at a film thickness of about 1 mil.

36. The film layer of claim 34, wherein the film layer has a Seal Initiation Temperature (SIT) of 100 ℃ or less when measured at a film thickness of about 2 mils.

37. The film layer of claim 34 wherein said film layer has a hot tack window Area (AHTW) of 160 newtons ∙ ℃ when measured at a film thickness of about 2 mils.

38. The film layer of claim 34 wherein said film layer has an Oxygen Transmission Rate (OTR) of greater than or equal to 650 cm when measured at a film thickness of about 1 mil³100 square inches.

39. The film layer of claim 34, wherein the film layer has a 1% secant modulus in the Machine Direction (MD) of greater than or equal to 190 MPa when measured at a film thickness of about 1 mil, a Seal Initiation Temperature (SIT) of less than or equal to 100 ℃ when measured at a film thickness of about 2 mil, a hot tack window Area (AHTW) of greater than or equal to 160 newtons ∙ ℃ when measured at a film thickness of about 2 mil, and an Oxygen Transmission Rate (OTR) of greater than or equal to 650 cm when measured at a film thickness of about 1 mil³100 square inches.

40. A film layer having a thickness of 0.5 to 10 mils, wherein the film layer has a 1% secant modulus in the Machine Direction (MD) of greater than or equal to 190 MPa when measured at a film thickness of about 1 mil, and a Seal Initiation Temperature (SIT) of less than or equal to 100 ℃ when measured at a film thickness of about 2 mils.

41. A film layer having a thickness of 0.5 to 10 mils, wherein the film layer has a Machine Direction (MD)1% secant modulus ≧ 190 MPa when measured at a film thickness of about 1 mil, and a hot tack window Area (AHTW) of ≧ 160 Newton ∙ ℃ when measured at a film thickness of about 2 mils.

42. A film layer having a thickness of 0.5 to 10 mils, wherein the film layer has a 1% secant modulus in the Machine Direction (MD) of greater than or equal to 190 MPa when measured at a film thickness of about 1 mil, and an Oxygen Transmission Rate (OTR) of greater than or equal to 650 cm when measured at a film thickness of about 1 mil³100 square inches.

43. Thickness of 0.5 to 10 milsWherein the film layer has a Machine Direction (MD)1% secant modulus ≥ 190 MPa when measured at a film thickness of about 1 mil and an Oxygen Transmission Rate (OTR) ≥ 650 cm when measured at a film thickness of about 1 mil³Per 100 square inches, Seal Initiation Temperature (SIT). ltoreq.100 ℃ when measured at a film thickness of about 2 mils, and hot tack window Area (AHTW). gtoreq.160 newtons ∙ ℃ when measured at a film thickness of about 2 mils.

44. A film comprising the polyethylene composition of claim 1, said film satisfying the following relationship:

hot tack Window Area (AHTW) > -2.0981 (1% secant modulus in Machine Direction (MD)) + 564.28;

wherein the AHTW is measured at a film thickness of about 2 mils, and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

45. A film comprising the polyethylene composition of claim 1, said film satisfying the following relationship:

oxygen Transmission Rate (OTR) > -5.4297 (1% secant modulus in Machine Direction (MD)) + 1767.8;

wherein the OTR is measured at a film thickness of about 1 mil, and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

46. A film comprising the polyethylene composition of claim 1, said film satisfying the following relationship:

seal Initiation Temperature (SIT) < 0.366 (1% secant modulus in Machine Direction (MD)) + 22.509;

wherein SIT is measured at a film thickness of about 2 mils, and a Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

47. A film comprising the polyethylene composition of claim 1, said film satisfying the following relationship:

i) hot tack Window Area (AHTW) > -2.0981 (1% secant modulus in Machine Direction (MD)) + 564.28;

wherein the AHTW is measured at a film thickness of about 2 mils, and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil;

ii) Oxygen Transmission Rate (OTR) > -5.4297 (1% secant modulus in Machine Direction (MD) + 1767.8;

wherein the OTR is measured at a film thickness of about 1 mil, and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil; and

iii) Seal Initiation Temperature (SIT) < 0.366 (1% secant modulus in Machine Direction (MD) + 22.509;

wherein SIT is measured at a film thickness of about 2 mils, and a Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

Technical Field

The present disclosure provides polyethylene compositions having good stiffness, good oxygen permeability, and good sealability when blown into a film. The polyethylene composition comprises two polyethylene components produced with a single-site polymerization catalyst and one polyethylene component produced with a multi-site polymerization catalyst.

Background

Multicomponent polyethylene compositions are well known in the art. One way to obtain a multicomponent polyethylene composition is to use two or more different polymerization catalysts in one or more polymerization reactors. For example, it is known to use single-site and Ziegler-Natta type polymerization catalysts in at least two different solution polymerization reactors. Such reactors may be configured in series or in parallel.

The solution polymerization process is typically conducted at a temperature above the melting point of the ethylene homopolymer or copolymer product being produced. In a typical solution polymerization process, the catalyst components, solvent, monomers and hydrogen are fed under pressure to one or more reactors.

For solution phase ethylene polymerization or ethylene copolymerization, the reactor temperature may range from about 80 ℃ to about 300 ℃, while the pressure is typically in the range from about 3MPag to about 45 MPag. The ethylene homopolymer or copolymer produced under reactor conditions remains dissolved in the solvent. The residence time of the solvent in the reactor is relatively short, for example from about 1 second to about 20 minutes. The solution process can be operated under a wide range of process conditions that allow for the production of a variety of ethylene polymers. After the reactor, the polymerization reaction is quenched by the addition of a catalyst deactivator to prevent further polymerization, and optionally deactivated by the addition of an acid scavenger. Once deactivated (and optionally deactivated), the polymer solution is passed to a polymer recovery operation (devolatilization system) wherein the ethylene homopolymer or copolymer is separated from the process solvent, unreacted residual ethylene, and unreacted optional α -olefin.

Regardless of the mode of production, there remains a need to improve the properties of multicomponent polyethylene compositions in film applications.

Disclosure of Invention

The present disclosure provides polyethylene compositions that, when made into films, have a good balance of stiffness, oxygen transmission rate, and sealing performance.

One embodiment of the present disclosure is a polyethylene composition comprising:

5 to 80% by weight of a second polyethylene which is an ethylene copolymer or an ethylene homopolymer, the second polyethylene having a weight-average molecular weight M_w15,000 to 100,000, molecular weight distribution M_w/M_n< 2.3 and having 0 to 20 short chain branches per thousand carbon atoms;and

One embodiment of the present disclosure is a film layer having a thickness of 0.5 to 10 mils comprising a polyethylene composition comprising:

In one embodiment, the film layer has a 1% secant modulus in the Machine Direction (MD) of 190 MPa or greater when measured at a film thickness of about 1 mil.

In one embodiment, the film layer has a Seal Initiation Temperature (SIT) of 100 ℃ or less when measured at a film thickness of about 2 mils.

In one embodiment, the film layer has a hot tack window Area (AHTW) of 160 newtons or more ∙ ℃ when measured at a film thickness of about 2 mils.

In one embodiment, the film layer has an Oxygen Transmission Rate (OTR) of 650 cm or greater when measured at a film thickness of about 1 mil³100 square inches.

One embodiment of the present disclosure is a film layer having a thickness of 0.5 to 10 mils, wherein the film layer has a 1% secant modulus in the Machine Direction (MD) of greater than or equal to 190 MPa when measured at a film thickness of about 1 mil; oxygen Transmission Rate (OTR) of 650 cm or more when measured at a film thickness of about 1 mil³100 square inches; a Seal Initiation Temperature (SIT). ltoreq.100 ℃ when measured at a film thickness of about 2 mils; and when at about 2 milsThe hot tack window Area (AHTW) was 160 Newton ∙ deg.C or more when measured at film thickness.

One embodiment of the present disclosure is a film layer having a thickness of 0.5 to 10 mils, wherein the film layer satisfies at least one of the following relationships:

i) hot tack Window Area (AHTW) > -2.0981 (1% secant modulus in Machine Direction (MD)) + 564.28;

wherein AHTW is measured at a film thickness of about 2 mils, and Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil;

ii) Oxygen Transmission Rate (OTR) > -5.4297 (1% secant modulus in Machine Direction (MD) + 1767.8;

wherein the OTR is measured at a film thickness of about 1 mil and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil; and

iii) Seal Initiation Temperature (SIT) < 0.366 (1% secant modulus in Machine Direction (MD) + 22.509;

wherein SIT is measured at a film thickness of about 2 mils and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

One embodiment of the present disclosure is a film layer having a thickness of 0.5 to 10 mils, wherein the film layer satisfies each of the following relationships:

i) hot tack Window Area (AHTW) > -2.0981 (1% secant modulus in Machine Direction (MD)) + 564.28;

wherein AHTW is measured at a film thickness of about 2 mils, and Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil;

ii) Oxygen Transmission Rate (OTR) > -5.4297 (1% secant modulus in Machine Direction (MD) + 1767.8;

wherein the OTR is measured at a film thickness of about 1 mil and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil; and

iii) Seal Initiation Temperature (SIT) < 0.366 (1% secant modulus in Machine Direction (MD) + 22.509;

wherein SIT is measured at a film thickness of about 2 mils and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

Drawings

Fig. 1 shows Gel Permeation Chromatography (GPC) with refractive index detection for polyethylene compositions made according to the present disclosure, as well as some comparative polyethylenes.

Fig. 2 shows gel permeation chromatography with fourier transform infrared detection (GPC-FTIR) obtained for polyethylene compositions made according to the present disclosure, as well as some comparative polyethylenes. Comonomer content (expressed as number of short chain branches per 1000 carbons) relative to copolymer molecular weight (x-axis) is given (y-axis). The upwardly inclined lines (from left to right) are short chain branches (represented as short chain branches per 1000 carbon atoms) as determined by FTIR. It can be seen from this figure that for inventive examples 1 and 2, the number of short chain branches initially increases at higher molecular weights and then decreases again at still higher molecular weights, and thus comonomer incorporation is considered to be a "partial reversal" of the presence of peaks or maxima.

Fig. 3 shows Differential Scanning Calorimetry (DSC) and characteristics of polyethylene compositions made according to the present disclosure, as well as some comparative polyethylenes.

Fig. 4 shows the hot tack curves of films prepared using polyethylene compositions prepared according to the present disclosure, as well as several comparative polyethylenes.

Fig. 5 shows the cold seal curves of films made using polyethylene compositions made according to the present disclosure, as well as several comparative polyethylenes.

FIG. 6 shows a graph of the following equation: AHTW = -2.0981 (machine direction (MD)1% secant modulus) + 564.28. AHTW values (y-axis) are plotted against corresponding Machine Direction (MD)1% secant modulus values (x-axis) for films made from the polyethylene compositions of the present disclosure and films made from several comparative polyethylenes.

FIG. 7 shows a graph of the following equations: SIT = 0.366 (machine direction (MD)1% secant modulus) + 22.509. The SIT values (y-axis) are plotted against the corresponding Machine Direction (MD)1% secant modulus values (x-axis) for films made from the polyethylene compositions of the present disclosure and films made from several comparative polyethylenes.

FIG. 8 shows a graph of the following equation: OTR = -5.4297 (1% secant modulus in Machine Direction (MD) + 1767.8. OTR values (y-axis) are plotted against corresponding Machine Direction (MD)1% secant modulus values (x-axis) for films made from the polyethylene compositions of the present disclosure and films made from several comparative polyethylenes. "1/2.5 film" refers to a film made at a thickness of 1 mil, with a blow-up ratio (BUR) of 2.5.

Definition of terms

Other than in the examples, or where otherwise indicated, all numbers or expressions referring to quantities of ingredients, extrusion conditions, and the like used in the specification and claims are to be understood as modified in all instances by the term "about". Accordingly, unless indicated to the contrary, the numerical parameters set forth in the following specification and attached claims are approximations that may vary depending upon the desired properties sought to be obtained by the various embodiments. At the very least, and not as an attempt to limit the application of the doctrine of equivalents to the scope of the claims, each numerical parameter should at least be construed in light of the number of reported significant digits and by applying ordinary rounding techniques. The numerical values set forth in the specific examples are reported as precisely as possible. Any numerical value, however, inherently contains certain errors necessarily resulting from the standard deviation found in their respective testing measurements.

It should be understood that any numerical range recited herein is intended to include all sub-ranges subsumed therein. For example, a range of "1 to 10" is intended to include all sub-ranges between the recited minimum value of 1 and the recited maximum value of 10 and includes the recited minimum value of 1 and the recited maximum value of 10; that is, the minimum value is equal to or greater than 1 and the maximum value is equal to or less than 10. Because the disclosed numerical ranges are continuous, they include every value between the minimum and maximum values. Unless expressly indicated otherwise, the various numerical ranges specified in this application are approximations.

Virtually all compositional ranges expressed herein are limited in total and do not exceed 100% (vol% or wt%). Where multiple components may be present in the composition, the sum of the maximum amounts of each component may exceed 100%, with the understanding that: the skilled person will readily understand that the amount of components actually used should correspond to up to 100%.

To form a more complete understanding of the present disclosure, the following terms are defined and should be used in conjunction with the accompanying drawings and the description of the various embodiments throughout.

As used herein, the term "monomer" refers to a small molecule that can chemically react with itself or other monomers and chemically bond to form a polymer.

As used herein, the term "alpha-olefin" or "alpha-olefin" is used to describe a monomer having a straight hydrocarbon chain containing from 3 to 20 carbon atoms and having a double bond at one end of the chain; the equivalent term is "linear alpha-olefin".

As used herein, the term "polyethylene" or "ethylene polymer" refers to a macromolecule produced from ethylene monomers and optionally one or more additional monomers; regardless of the particular catalyst or the particular process used to prepare the ethylene polymer. In the field of polyethylene, the one or more additional monomers are referred to as "comonomers" and typically include alpha-olefins. The term "homopolymer" refers to a polymer comprising only one type of monomer. The "ethylene homopolymer" is prepared using only ethylene as a polymerizable monomer. The term "copolymer" refers to a polymer comprising two or more types of monomers. An "ethylene copolymer" is prepared using ethylene and one or more other types of polymerizable monomers. Common polyethylenes include High Density Polyethylene (HDPE), Medium Density Polyethylene (MDPE), Linear Low Density Polyethylene (LLDPE), Very Low Density Polyethylene (VLDPE), Ultra Low Density Polyethylene (ULDPE), plastomers and elastomers. The term polyethylene also includes polyethylene terpolymers that may include two or more comonomers in addition to ethylene. The term polyethylene also includes combinations or blends of the above polyethylenes.

The term "heterogeneously branched polyethylene" refers to a subgroup of polymers in the group of ethylene polymers produced using a heterogeneous catalyst system; non-limiting examples of heterogeneous catalysts include Ziegler-Natta catalysts or chromium catalysts, both of which are well known in the art.

The term "homogeneously branched polyethylene" refers to a subgroup of polymers in the ethylene polymer group produced using a single-site catalyst; non-limiting examples of single-site catalysts include metallocene catalysts, phosphinimine catalysts, and constrained geometry catalysts, all of which are well known in the art.

In general, homogeneously branched polyethylenes have a narrow molecular weight distribution, such as Gel Permeation Chromatography (GPC) M_w/M_nValues of less than 2.8, in particular less than 2.3, although exceptions may occur; m_wAnd M_nRespectively, the weight average molecular weight and the number average molecular weight. In contrast, M of heterogeneously branched ethylene polymers_w/M_nGenerally greater than M for homogeneous polyethylene_w/M_n. In general, homogeneously branched ethylene polymers also have a narrow comonomer distribution, i.e. each macromolecule within the molecular weight distribution has a similar comonomer content. In general, the composition distribution breadth index "CDBI" is used to quantify how the comonomer is distributed within the ethylene polymer, as well as to distinguish ethylene polymers produced with different catalysts or processes. "CDBI₅₀"is defined as the percentage of ethylene polymer whose composition is within 50 weight percent (wt%) of the median comonomer composition; this definition is consistent with that described in WO 93/03093 assigned to Exxon Chemical Patents inc. CDBI of ethylene interpolymers₅₀Can be calculated from a TREF (temperature rising elution fractionation) curve; TREF is described in Wild et al, J. Poly. Sci., Part B, Poly. Phys., Vol. 20(3), page 441-455. In general, CDBI of homogeneously branched ethylene polymers₅₀Greater than about 70% or greater than about 75%. In contrast, CDBI of heterogeneously branched ethylene polymers containing alpha-olefins₅₀CDBI generally lower than homogeneous ethylene polymers₅₀. For example, CDBI of heterogeneously branched ethylene Polymer₅₀And may be less than about 75%, or less than about 70%.

Homogeneously branched ethylene polymers are generally further subdivided into "linear homogeneous ethylene polymers" and "substantially linear homogeneous ethylene polymers" as is well known to those skilled in the art. The amount of long chain branching varies between these two subgroups: more specifically, the linear homogeneous ethylene polymer has less than about 0.01 long chain branches per 1000 carbon atoms; and substantially linear ethylene polymers have greater than about 0.01 to about 3.0 long chain branches per 1000 carbon atoms. The long chain branches are macromolecular in nature, i.e., they are similar in length to the macromolecules to which they are attached. Hereinafter, the term "homogeneously branched polyethylene" or "homogeneously branched ethylene polymer" in the present disclosure refers to both linear homogeneous ethylene polymers and substantially linear homogeneous ethylene polymers.

The term "thermoplastic" refers to a polymer that becomes liquid when heated, flows under pressure, and solidifies when cooled. Thermoplastic polymers include ethylene polymers and other polymers used in the plastics industry; non-limiting examples of other polymers commonly used in film applications include barrier resins (EVOH), tie resins, polyethylene terephthalate (PET), polyamides, and the like.

As used herein, the term "monolayer film" refers to a film comprising a single layer of one or more thermoplastics.

As used herein, the term "hydrocarbyl", "hydrocarbyl group" or "hydrocarbon group" refers to straight or cyclic, aliphatic, olefinic, acetylenic, and aryl (aromatic) groups containing hydrogen and carbon with one less hydrogen.

As used herein, "alkyl" includes straight, branched and cyclic alkanyl radicals having one less hydrogen atom group; non-limiting examples include methyl (-CH)₃) And ethyl (-CH)₂CH₃). The term "alkenyl" refers to straight, branched, and cyclic hydrocarbons containing at least one carbon-carbon double bond with at least one hydrogen atom group.

As used herein, the term "aryl" group includes phenyl, naphthyl, pyridyl and other groups whose molecules have an aromatic ring structure; non-limiting examples include naphthalene, phenanthrene, and anthracene. An "arylalkyl" group is an alkyl group flanked by aryl groups; non-limiting examples include benzyl, phenethyl, and tolylmethyl; "alkylaryl" is an aryl group having one or more alkyl groups pendant therefrom; non-limiting examples include tolyl, xylyl, mesityl, and cumyl.

As used herein, the phrase "heteroatom" includes any atom other than carbon and hydrogen that may be bonded to carbon. A "heteroatom-containing group" is a hydrocarbon group that contains a heteroatom and may contain one or more of the same or different heteroatoms. In one embodiment, the heteroatom-containing group is a hydrocarbyl group containing 1 to 3 atoms selected from boron, aluminum, silicon, germanium, nitrogen, phosphorus, oxygen, and sulfur. Non-limiting examples of heteroatom-containing groups include groups of imines, amines, oxides, phosphines, ethers, ketones, oxazoline heterocycles, oxazolines, thioethers, and the like. The term "heterocycle" refers to a ring system having a carbon backbone comprising 1 to 3 atoms selected from the group consisting of boron, aluminum, silicon, germanium, nitrogen, phosphorus, oxygen, and sulfur.

As used herein, the term "unsubstituted" refers to a hydrogen radical bound to a molecular radical following the term "unsubstituted". The term "substituted" refers to a group following the term having one or more moieties substituted for one or more hydrogen radicals at any position within the group; non-limiting examples of such moieties include halogen groups (F, Cl, Br), hydroxyl, carbonyl, carboxyl, amine groups, phosphine groups, alkoxy, phenyl, naphthyl, C₁To C₃₀Alkyl radical, C₂To C₃₀Alkenyl groups and combinations thereof. Non-limiting examples of substituted alkyl and aryl groups include: acyl, alkylamino, alkoxy, aryloxy, alkylthio, dialkylamino, alkoxycarbonyl, aryloxycarbonyl, carbamoyl, alkyl-and dialkyl-carbamoyl, acyloxy, acylamino, arylamino, and combinations thereof.

Detailed Description

In the present disclosure, the polyethylene composition will comprise at least the following types of polymers: a first polyethylene which is an ethylene copolymer and whose M is_w/M_nLess than about 2.3; a second polyethylene which is an ethylene copolymer or an ethylene homopolymer different from the first polyethylene and whose M_w/M_nLess than about 2.3; and a third polyethylene which is an ethylene copolymer or an ethylene homopolymer and which M is_w/M_nGreater than about 2.3. Each of these polyethylene components, as well as the polyethylene compositions of which each is a part, are further described below.

First polyethylene

In one embodiment of the present disclosure, the first polyethylene is prepared with a single-site catalyst, non-limiting examples of which include phosphinimine catalysts, metallocene catalysts, and constrained geometry catalysts, all of which are well known in the art.

In one embodiment of the present disclosure, the first polyethylene is an ethylene copolymer. Suitable alpha-olefins that may be copolymerized with ethylene to produce ethylene copolymers include 1-propylene, 1-butene, 1-pentene, 1-hexene, and 1-octene.

In one embodiment of the present disclosure, the first polyethylene is a homogeneously branched ethylene copolymer.

In one embodiment of the present disclosure, the first polyethylene is an ethylene/1-octene copolymer.

In one embodiment of the present disclosure, the first polyethylene is made with a phosphinimine catalyst.

In one embodiment of the present disclosure, the phosphinimine catalyst is represented by the formula:

(L^A)_aM(PI)_b(Q)_n

wherein (L)^A) Represents a cyclopentadienyl type ligand; m represents a metal atom selected from Ti, Zr and Hf; PI represents a phosphinimine ligand; q represents an activatable ligand; a is 0 or 1; b is 1 or 2; (a + b) = 2; n is 1 or 2, and; the sum of (a + b + n) is equal to the valence of the metal M.

As used herein, the term "cyclopentadienyl-type" ligand is meant to include ligands comprising at least one five carbocyclic ring bonded to the metal via a η -5 (or in some cases η -3) bond. Thus, the term "cyclopentadienyl-type" includes, for example, unsubstituted cyclopentadienyl, mono-or polysubstituted cyclopentadienyl, unsubstituted indenyl, mono-or polysubstituted indenyl, unsubstituted fluorenyl and mono-or polysubstituted fluorenyl. Hydrogenated versions of indenyl and fluorenyl ligands are also contemplated for use in this disclosure, so long as the five carbon rings bonded to the metal by a η -5 (or in some cases η -3) bond remain intact. The substituents of the cyclopentadienyl ligand, indenyl ligand (or hydrogenated version thereof) and fluorenyl ligand (or hydrogenated version thereof) may be selected from C_1-30Hydrocarbyl (which may be unsubstituted or further substituted, e.g. by halo and/or hydrocarbyl; e.g. suitably substituted C_1-30The hydrocarbon radical being a pentafluorobenzyl radicalSuch as-CH₂C₆F₅) (ii) a A halogen atom; c_1-8An alkoxy group; c_6-10Aryl or aryloxy groups (each of which may be further substituted with, for example, halo and/or hydrocarbyl groups); unsubstituted or substituted by up to two C_1-8An alkyl-substituted amino group; unsubstituted or substituted by up to two C_1-8An alkyl-substituted phosphorus group; formula-Si (R')₃Wherein each R' is independently selected from hydrogen, C_1-8Alkyl or alkoxy, C_6-10Aryl or aryloxy groups; and formula-Ge (R')₃Wherein R' is as defined directly above.

The phosphinimine ligand PI is defined by the formula:

(R^p)₃P = N -

wherein R is^pThe groups are independently selected from: a hydrogen atom; a halogen atom; c unsubstituted or substituted by one or more halogen atoms_1-20A hydrocarbyl group; c_1-8An alkoxy group; c_6-10An aryl group; c_6-10An aryloxy group; an amino group; formula-Si (R)^s)₃In which R is^sThe groups are independently selected from hydrogen atom, C_1-8Alkyl or alkoxy, C_6-10Aryl radical, C_6-10Aryloxy group, or formula-Ge (R)^G)₃Germyl of (a), wherein R^GRadicals as in this paragraph for R^sThe definition of (1).

In one embodiment of the present disclosure, the metal M in the phosphinimine catalyst is titanium Ti.

In one embodiment of the present disclosure, the single-site catalyst used to prepare the first polyethylene is cyclopentadienyl tris (tert-butyl) phosphinimine titanium dichloride Cp ((t-Bu)₃PN)TiCl₂。

In one embodiment of the present disclosure, the first polyethylene is made with a metallocene catalyst.

In one embodiment of the present disclosure, the first polyethylene is made with a bridged metallocene catalyst.

In one embodiment of the present disclosure, the first polyethylene is made with a bridged metallocene catalyst having formula I:

in formula (I): m is a group 4 metal selected from titanium, zirconium or hafnium; g is a group 14 element selected from carbon, silicon, germanium, tin or lead; r₁Is a hydrogen atom, C_1-20Hydrocarbyl radical, C_1-20Alkoxy or C_6-10An aromatic ether group; r₂And R₃Independently selected from hydrogen atom, C_1-20Hydrocarbyl radical, C_1-20Alkoxy or C_6-10An aromatic ether group. R₄And R₅Independently selected from hydrogen atom, C_1-20Hydrocarbyl radical, C_1-20Alkoxy or C_6-10An aromatic ether group; and Q is independently an activatable leaving group ligand.

In the present disclosure, the term "activatable" means that the ligand Q can be cleaved from the metal center M by a protonolysis reaction or abstracted from the metal center M by a suitable acidic or electrophilic catalyst activator compound (also referred to as a "cocatalyst" compound), respectively, examples of which are described below. The activatable ligand Q may also be converted to another ligand which cleaves or abstracts from the metal center M (e.g., a halo group may be converted to an alkyl group). Without wishing to be bound by any single theory, the protonolysis or abstraction reaction generates an active "cationic" metal center that can polymerize olefins.

In embodiments of the present disclosure, the activatable ligands Q are independently selected from hydrogen atoms; a halogen atom; c_1-20Hydrocarbyl radical, C_1-20Alkoxy and C_6-10Aryl or aryloxy groups, wherein each hydrocarbyl, alkoxy, aryl or aromatic ether group may be unsubstituted or further substituted with one or more halogen or other groups; c_1-8An alkyl group; c_1-8An alkoxy group; c_6-10Aryl or aryloxy groups; amino (amidio) or phosphido (phosphinido), but wherein Q is not cyclopentadienyl. Two Q ligands can also be linked to each other and form, for example, a substituted or unsubstituted diene ligand (e.g., 1, 3-butadiene); or a group containing a delocalized heteroatom such as an acetate or acetamidinate group. In one convenient embodiment of the present disclosure, each QIndependently selected from halogen atoms, C_1-4Alkyl and benzyl. Particularly suitable activatable ligands Q are monoanions such as halide ions (e.g. chloride) or hydrocarbyl groups (e.g. methyl, benzyl).

In one embodiment of the disclosure, the single-site catalyst used to prepare the first polyethylene is of the formula [ (2, 7-tBu)₂Flu)Ph₂C(Cp)HfCl₂]Diphenylmethylene (cyclopentadienyl) (2, 7-di-tert-butylfluorenyl) hafnium dichloride.

In one embodiment of the disclosure, the single-site catalyst used to prepare the first polyethylene is of the formula [ (2, 7-tBu)₂Flu)Ph₂C(Cp)HfMe₂]Diphenylmethylene (cyclopentadienyl) (2, 7-di-tert-butylfluorenyl) hafnium dimethyl.

In addition to the single-site catalyst molecule itself, the active single-site catalyst system may comprise one or more of the following: alkylalumoxane cocatalysts and ionic activators. The single-site catalyst system may also optionally comprise a hindered phenol.

Although the exact structure of alkylaluminoxanes is not yet determined, subject matter experts generally agree that it is an oligomeric species containing repeating units of the general formula:

(R)₂AlO-(Al(R)-O)_n-Al(R)₂

wherein the R groups may be the same or different straight, branched or cyclic hydrocarbon groups containing from 1 to 20 carbon atoms and n is from 0 to about 50. A non-limiting example of an alkylaluminoxane is methylaluminoxane (or MAO), wherein each R group is a methyl group.

In one embodiment of the present disclosure, R of the alkylalumoxane is methyl and m is 10 to 40.

In one embodiment of the present disclosure, the cocatalyst is Modified Methylaluminoxane (MMAO).

It is well known in the art that alkylalumoxanes can serve the dual role of an alkylating agent and an activator. Thus, alkylaluminoxane cocatalysts are generally used in combination with activatable ligands such as halogens.

Typically, ionic activators are comprised of cations and bulky anions; wherein the latter is substantially non-coordinating. A non-limiting example of an ionic activator is a tetracoordinated boron ionic activator having four ligands bonded to the boron atom. Non-limiting examples of boron ion activators include the following formulas shown below:

[R⁵]⁺[B(R⁷)₄]^-

wherein B represents a boron atom, R⁵Is an aromatic hydrocarbon radical (e.g. triphenylmethyl cation) and each R⁷Independently selected from C unsubstituted or substituted by 3 to 5 fluorine atoms_1-4Phenyl substituted with a substituent of alkyl or alkoxy; and formula-Si (R)⁹)₃In which each R is⁹Independently selected from hydrogen atom and C_1-4Alkyl, and

[(R⁸)_tZH]⁺[B(R⁷)₄]^-

wherein B is a boron atom, H is a hydrogen atom, Z is a nitrogen or phosphorus atom, t is 2 or 3 and R is⁸Is selected from C_1-8Alkyl, unsubstituted or substituted by up to three C_1-4Alkyl-substituted phenyl, or one R⁸Together with the nitrogen atom may form an anilino group and R⁷As defined above.

In both formulae, R⁷A non-limiting example of (a) is pentafluorophenyl. Generally, the boron ion activators may be described as salts of tetrakis (perfluorophenyl) boron; non-limiting examples include anilinium, carbenium, oxonium, phosphonium and sulfonium salts of tetrakis (perfluorophenyl) boron with anilinium and trityl (or triphenylmethylium). Additional non-limiting examples of ionic activators include: triethylammoniumtetra (phenyl) boron, tripropylammoniumtetra (phenyl) boron, tri (N-butyl) ammoniumtetra (phenyl) boron, trimethylammonium tetrakis (p-tolyl) boron, trimethylammonium tetrakis (o-tolyl) boron, tributylammoniumtetra (pentafluorophenyl) boron, tripropylammoniumtetra (o, p-dimethylphenyl) boron, tributylammoniumtetra (m, m-dimethylphenyl) boron, tributylammoniumtetra (p-trifluoromethylphenyl) boron, tributylammoniumtetra (pentafluorophenyl) boron, tri (N-butyl) ammoniumtetra (o-tolyl) boron, N-dimethylaniliniumtetrakis (phenyl) boron, N-diethylaniliniumtetrakis (phenyl) boron, N-dibutylaniliniumtetrakis (phenyl) boronEthylanilinium tetrakis (phenyl) N-butylboron, N-2,4, 6-pentamethylanilinium tetrakis (phenyl) boron, di (isopropyl) ammonium tetrakis (pentafluorophenyl) boron, dicyclohexylammonium tetrakis (phenyl) boron, triphenylphosphonium tetrakis (phenyl) boron, tri (methylphenyl) phosphonium tetrakis (phenyl) boron, tri (dimethylphenyl) phosphonium tetrakis (phenyl) boron, ylium tetrapentafluorophenylborate, triphenylmethylium tetrapentafluorophenylborate, benzene (diazonium) tetrapentafluorophenylborate, ylium tetrakis (2,3,5, 6-tetrafluorophenyl) borate, triphenylmethylium tetrakis (2,3,5, 6-tetrafluorophenyl) borate, benzene (diazonium) tetrakis (3,4, 5-trifluorophenyl) borate, insulin tetrakis (3,4, 5-trifluorophenyl) borate, benzene (diazonium) tetrakis (3,4, 5-trifluorophenyl) borate, zenithnium tetrakis (1,2, 2-trifluorovinyl) borate, triphenylmethylonium tetrakis (1,2, 2-trifluorovinyl) borate, benzene (diazonium) tetrakis (1,2, 2-trifluorovinyl) borate, ni-ium tetrakis (2,3,4, 5-tetrafluorophenyl) borate, triphenylmethylonium tetrakis (2,3,4, 5-tetrafluorophenyl) borate and benzene (diazonium) tetrakis (2,3,4, 5-tetrafluorophenyl) borate. Readily available commercial ionic activators include N, N-dimethylanilinium tetrapentafluorophenyl borate and triphenylmethyl onium tetrapentafluorophenyl borate.

Non-limiting examples of hindered phenols include butylated phenolic antioxidants, butylated hydroxytoluene, 2, 6-di-tert-butyl-4-ethylphenol, 4 '-methylenebis (2, 6-di-tert-butylphenol), 1,3, 5-trimethyl-2, 4, 6-tris (3, 5-di-tert-butyl-4-hydroxybenzyl) benzene, and octadecyl 3- (3',5 '-di-tert-butyl-4' -hydroxyphenyl) propionate.

To produce an active single-site catalyst system, the three or four components: the amounts and molar ratios of single-site catalyst, alkylaluminoxane, ionic activator and optional hindered phenol are optimized.

In one embodiment of the present disclosure, the single-site catalyst used to prepare the first polyethylene produces no long chain branches, and the first polyethylene will contain no measurable amount of long chain branches.

In one embodiment of the present disclosure, the single site catalyst used to prepare the first polyethylene produces long chain branches, and the first polyethylene will contain long chain branches, hereinafter referred to as "LCBs". LCB is a well-known structural phenomenon in polyethylene and is well known to those of ordinary skill in the art. Traditionally, there are three methods for LCB analysis, namely nuclear magnetic resonance spectroscopy (NMR), see for example J.C. Randall, J Macromol. Sci, Rev. Macromol. chem. Phys. 1989, 29, 201, triple detection SEC equipped with DRI, viscometer and small angle laser scattering detector, see for example W.W. Yau and D.R. Hill, int. J. Polymer. anal. Charact. 1996; 2:151; and rheology, see for example W.W. Graessley, Acc. chem. Res. 1977, 10, 332-339. In the present disclosure, the long chain branches are macromolecular in nature, i.e., long enough to be visible in NMR spectra, triple detector SEC experiments, or rheology experiments.

In embodiments of the present disclosure, the molecular weight distribution M of the first polyethylene_w/M_nThe upper limit of (d) may be about 2.8, or about 2.5, or about 2.4, or about 2.3, or about 2.2. In embodiments of the present disclosure, the molecular weight distribution M of the first polyethylene_w/M_nThe lower limit of (c) may be about 1.4, or about 1.6, or about 1.7, or about 1.8, or about 1.9.

In embodiments of the present disclosure, the molecular weight distribution M of the first polyethylene_w/M_n< 2.3, or < 2.1, or < 2.0 or about 2.0. In embodiments of the present disclosure, the molecular weight distribution M of the first polyethylene_w/M_nFrom about 1.7 to about 2.2.

In one embodiment of the present disclosure, the first polyethylene has 1 to 200 Short Chain Branches (SCB) per thousand carbon atoms_PE-1). In a further embodiment, the first polyethylene has from 3 to 150 Short Chain Branches (SCB) per thousand carbon atoms_PE-1) Or 5 to 100 short chain branches per thousand carbon atoms (SCB)_PE-1) Or 10 to 100 short chain branches per thousand carbon atoms (SCB)_PE-1) Or 5 to 75 short chain branches per thousand carbon atoms (SCB)_PE-1) Or 10 to 75 short chain branches per thousand carbon atoms (SCB)_PE-1) Or 15 to 75 short chain branches per thousand carbon atoms (SCB)_PE-1) Or 20 to 75 short chain branches per thousand carbon atoms (SCB)_PE-1). In yet a further embodiment, the first polyethylene is every thousandThe carbon atoms having 20 to 100 Short Chain Branches (SCB)_PE-1) Or 25 to 100 short chain branches per thousand carbon atoms (SCB)_PE-1) Or 30 to 100 short chain branches per thousand carbon atoms (SCB)_PE-1) Or 35 to 100 short chain branches per thousand carbon atoms (SCB)_PE-1) Or 35 to 75 short chain branches per thousand carbon atoms (SCB)_PE-1) Or 30 to 75 short chain branches per thousand carbon atoms (SCB)_PE-1) Or 30 to 60 short chain branches per thousand carbon atoms (SCB)_PE-1) Or 30 to 50 Short Chain Branches (SCB) per thousand carbon atoms_PE-1) Or 35 to 60 short chain branches per thousand carbon atoms (SCB)_PE-1) Or 35 to 55 short chain branches per thousand carbon atoms (SCB)_PE-1)。

Short chain branching (i.e. short chain branching per thousand carbon atoms, SCB)_PE-1) Is due to branching in the polyethylene due to the presence of an alpha-olefin comonomer and will for example have two carbon atoms for a 1-butene comonomer, four carbon atoms for a 1-hexene comonomer, or six carbon atoms for a 1-octene comonomer, etc.

In one embodiment of the present disclosure, the number of short chain branches per thousand carbon atoms in the first polyethylene (SCB)_PE-1) Greater than the number of short chain branches per thousand carbon atoms in the third polyethylene polymer (SCB)_PE-3)。

In embodiments of the present disclosure, the upper limit of the density d1 of the first polyethylene may be about 0.975g/cm³(ii) a In some casesUnder the condition of about 0.965g/cm³And; and in other cases about 0.955g/cm³. In embodiments of the present disclosure, the lower limit of the density d1 of the first polyethylene may be about 0.855g/cm³(ii) a In some cases about 0.865g/cm³And; and in other cases about 0.875g/cm³。

In embodiments of the present disclosure, the density d1 of the first polyethylene may be from about 0.855 to about 0.965g/cm³Or 0.865g/cm³To about 0.965g/cm³Or about 0.870 g/cm³To about 0.960 g/cm³Or about 0.865g/cm³To 0.950 g/cm³Or about 0.865g/cm³To about 0.940 g/cm³Or about 0.865g/cm³To about 0.936 g/cm³Or about 0.860 g/cm³To about 0.932g/cm³Or about 0.865g/cm³To about 0.926 g/cm³Or about 0.865g/cm³To about 0.921g/cm³Or about 0.865g/cm³To about 0.918 g/cm³Or about 0.865g/cm³To about 0.916 g/cm³Or about 0.870 g/cm³To about 0.916 g/cm³Or about 0.865g/cm³To about 0.912 g/cm³Or about 0.865g/cm³To about 0.910 g/cm³Or about 0.865g/cm³To about 0.905 g/cm³Or about 0.865g/cm³To about 0.900 g/cm³Or about 0.855g/cm³To about 0.900 g/cm³Or about 0.855g/cm³To about 0.905 g/cm³Or about 0.855g/cm³To about 0.910 g/cm³Or about 0.855g/cm³To about 0.916 g/cm³。

In embodiments of the disclosure, the CDBI of the first polyethylene₅₀The upper limit of (d) can be about 98 wt%, in other cases about 95 wt%, and in still other cases about 90 wt%. In embodiments of the disclosure, the CDBI of the first polyethylene₅₀The lower limit of (b) may be about 70wt%, in other cases about 75wt%, and in still other cases about 80 wt%.

In an embodiment of the present disclosure, the first and second electrodes are,melt index I of the first polyethylene₂ ¹Can be from about 0.01 dg/min to about 1000 dg/min, or from about 0.01 dg/min to about 500 dg/min, or from about 0.01 dg/min to about 100 dg/min, or from about 0.01 dg/min to about 50 dg/min, or from about 0.01 dg/min to about 25 dg/min, or from about 0.01 dg/min to about 10 dg/min, or from about 0.01 dg/min to about 5 dg/min, or from about 0.01 dg/min to about 3 dg/min, or from about 0.01 dg/min to about 1 dg/min, or less than about 5 dg/min, or less than about 3 dg/min, or less than about 1.0 dg/min, or less than about 0.75 dg/min, or less than about 0.50 dg/min.

In one embodiment of the present disclosure, the weight average molecular weight M of the first polyethylene_wFrom about 50,000 to about 300,000, or from about 50,000 to about 250,000, or from about 60,000 to about 250,000, or from about 70,000 to about 250,000 or from about 60,000 to about 220,000, or from about 70,000 to about 200,000, or from about 75,000 to about 175,000; or from about 70,000 to about 175,000, or from about 70,000 to about 150,000.

In one embodiment of the present disclosure, the weight average molecular weight M of the first polyethylene_wGreater than the weight average molecular weight M of the second polyethylene_w。

In one embodiment of the present disclosure, the weight average molecular weight M of the first polyethylene_wGreater than the weight average molecular weight M of the third polyethylene_w。

In one embodiment of the present disclosure, the weight average molecular weight M of the first polyethylene_wIn the third polyethylene polymer weight average molecular weight M_wWithin 30%. For the sake of clarity, this means: the weight average molecular weight M of the first polyethylene_wAnd the weight average molecular weight M of the third polyethylene_wThe absolute difference between the two is divided by the weight average molecular weight M of the third polyethylene_wConverted into percentages (i.e., [ -Mw 1-Mw 3 |/Mw 3)]X 100%) within 25%.

In one embodiment of the present disclosure, the weight average molecular weight M of the first polyethylene_wIn the third polyethylene polymer weight average molecular weight M_wWithin 25%. In one embodiment of the present disclosure, the weight average molecular weight M of the first polyethylene_wIn the third polyethylene polymer weight average molecular weight M_w20% ofAnd (4) the following steps. In one embodiment of the present disclosure, the weight average molecular weight M of the first polyethylene_wIn the third polyethylene polymer weight average molecular weight M_wWithin 15%. In one embodiment of the present disclosure, the weight average molecular weight M of the first polyethylene_wIn the third polyethylene polymer weight average molecular weight M_wWithin 10%.

In embodiments of the present disclosure, the upper limit of the weight percent (wt%) of the first polyethylene in the polyethylene composition (i.e., the weight percent of the first polyethylene based on the total weight of the first, second, and third polyethylenes) may be about 80 wt%, or about 75wt%, or about 70wt%, or about 65wt%, or about 60wt%, or about 55wt%, or about 50wt%, or about 45wt%, or about 40 wt%, or about 35 wt%. In embodiments of the present disclosure, the lower limit of the wt% of the first polyethylene in the polyethylene composition may be about 1 wt%, or about 5wt%, or about 10 wt%, or about 15 wt%, or about 20 wt%, or about 25 wt%, or in other cases about 30 wt%.

Second polyethylene

In one embodiment of the present disclosure, the second polyethylene is prepared with a single-site catalyst, non-limiting examples of which include phosphinimine catalysts, metallocene catalysts, and constrained geometry catalysts, all of which are well known in the art.

In one embodiment of the present disclosure, the second polyethylene is an ethylene homopolymer.

In one embodiment of the present disclosure, the second polyethylene is an ethylene copolymer. Suitable alpha-olefins that may be copolymerized with ethylene to produce ethylene copolymers include 1-propylene, 1-butene, 1-pentene, 1-hexene, and 1-octene.

In one embodiment of the present disclosure, the second polyethylene is a homogeneously branched ethylene copolymer.

In one embodiment of the present disclosure, the second polyethylene is an ethylene/1-octene copolymer.

In one embodiment of the present disclosure, the second polyethylene is made with a phosphinimine catalyst.

In one embodiment of the present disclosure, the phosphinimine catalyst is represented by the formula:

(L^A)_aM(PI)_b(Q)_n

As used herein, the term "cyclopentadienyl-type" ligand is meant to include ligands comprising at least one five carbocyclic ring bonded to the metal via a η -5 (or in some cases η -3) bond. Thus, the term "cyclopentadienyl-type" includes, for example, unsubstituted cyclopentadienyl, mono-or polysubstituted cyclopentadienyl, unsubstituted indenyl, mono-or polysubstituted indenyl, unsubstituted fluorenyl and mono-or polysubstituted fluorenyl. Hydrogenated versions of indenyl and fluorenyl ligands are also contemplated for use in this disclosure, so long as the five carbon rings bonded to the metal by a η -5 (or in some cases η -3) bond remain intact. The substituents of the cyclopentadienyl ligand, indenyl ligand (or hydrogenated version thereof) and fluorenyl ligand (or hydrogenated version thereof) may be selected from C_1-30Hydrocarbyl (which may be unsubstituted or further substituted, e.g. by halo and/or hydrocarbyl; e.g. suitably substituted C_1-30The hydrocarbyl group being a pentafluorobenzyl group such as-CH₂C₆F₅) (ii) a A halogen atom; c_1-8An alkoxy group; c_6-10Aryl or aryloxy groups (each of which may be further substituted with, for example, halo and/or hydrocarbyl groups); unsubstituted or substituted by up to two C_1-8An alkyl-substituted amino group; unsubstituted or substituted by up to two C_1-8An alkyl-substituted phosphorus group; formula-Si (R')₃Wherein each R' is independently selected from hydrogen, C_1-8Alkyl or alkoxy, C_6-10Aryl or aryloxy groups; and formula-Ge (R')₃Wherein R' is as defined directly above.

The phosphinimine ligand PI is defined by the formula:

(R^p)₃P = N -

wherein R is^pRadical aloneThe land is selected from: a hydrogen atom; a halogen atom; c unsubstituted or substituted by one or more halogen atoms_1-20A hydrocarbyl group; c_1-8An alkoxy group; c_6-10An aryl group; c_6-10An aryloxy group; an amino group; formula-Si (R)^s)₃In which R is^sThe groups are independently selected from hydrogen atom, C_1-8Alkyl or alkoxy, C_6-10Aryl radical, C_6-10Aryloxy group, or formula-Ge (R)^G)₃Germyl of (a), wherein R^GRadicals as in this paragraph for R^sThe definition of (1).

In one embodiment of the present disclosure, the metal M in the phosphinimine catalyst is titanium Ti.

In one embodiment of the present disclosure, the single-site catalyst used to prepare the second polyethylene is cyclopentadienyl tris (tert-butyl) phosphinimine titanium dichloride Cp ((t-Bu)₃PN)TiCl₂。

In one embodiment of the present disclosure, the second polyethylene is made with a metallocene catalyst.

In one embodiment of the present disclosure, the second polyethylene is made with a bridged metallocene catalyst.

In one embodiment of the present disclosure, the second polyethylene is made with a bridged metallocene catalyst having formula I:

In embodiments of the present disclosure, the activatable ligands Q are independently selected from hydrogen atoms; a halogen atom; c_1-20Hydrocarbyl radical, C_1-20Alkoxy and C_6-10Aryl or aryloxy groups, wherein each hydrocarbyl, alkoxy, aryl or aromatic ether group may be unsubstituted or further substituted with one or more halogen or other groups; c_1-8An alkyl group; c_1-8An alkoxy group; c_6-10Aryl or aryloxy groups; amino or phosphorus, but wherein Q is not cyclopentadienyl. Two Q ligands can also be linked to each other and form, for example, a substituted or unsubstituted diene ligand (e.g., 1, 3-butadiene); or a group containing a delocalized heteroatom such as an acetate or acetamidinate group. In one convenient embodiment of the present disclosure, each Q is independently selected from halogen atom, C_1-4Alkyl and benzyl. Particularly suitable activatable ligands Q are monoanions such as halide ions (e.g. chloride) or hydrocarbyl groups (e.g. methyl, benzyl).

In one embodiment of the present disclosure, the single-site catalyst used to prepare the second polyethylene is of the formula [ (2, 7-tBu)₂Flu)Ph₂C(Cp)HfCl₂]Diphenylmethylene (cyclopentadienyl) (2, 7-di-tert-butylfluorenyl) hafnium dichloride.

In one embodiment of the present disclosure, the single-site catalyst used to prepare the second polyethylene has the formula [ (2, 7-tBu)₂Flu)Ph₂C(Cp)HfMe₂]Diphenylmethylene (cyclopentadienyl) (2, 7-di-tert-butylfluorenyl) hafnium dimethyl.

Although the exact structure of alkylaluminoxanes is not yet determined, subject matter experts generally agree that it is an oligomeric species containing repeating units of the general formula:

(R)₂AlO-(Al(R)-O)_n-Al(R)₂

In one embodiment of the present disclosure, R of the alkylalumoxane is methyl and m is 10 to 40.

In one embodiment of the present disclosure, the cocatalyst is Modified Methylaluminoxane (MMAO).

[R⁵]⁺[B(R⁷)₄]^-

[(R⁸)_tZH]⁺[B(R⁷)₄]^-

In both formulae, R⁷A non-limiting example of (a) is pentafluorophenyl. Generally, the boron ion activators may be described as salts of tetrakis (perfluorophenyl) boron; non-limiting examples include anilinium, carbenium, oxonium, phosphonium and sulfonium salts of tetrakis (perfluorophenyl) boron with anilinium and trityl (or triphenylmethylium). Additional non-limiting examples of ionic activators include: triethylammoniumtetra (phenyl) boron, tripropylammoniumtetra (phenyl) boron, tri (N-butyl) ammoniumtetra (phenyl) boron, trimethylammonium tetrakis (p-tolyl) boron, trimethylammonium tetrakis (o-tolyl) boron, tributylammoniumtetra (pentafluorophenyl) boron, tripropylammoniumtetra (o, p-dimethylphenyl) boron, tributylammoniumtetra (m, m-dimethylphenyl) boron, tributylammoniumtetra (p-trifluoromethylphenyl) boron, tributylammoniumtetra (pentafluorophenyl) boron, tri (N-butyl) ammoniumtetra (o-tolyl) boron, N-dimethylaniliniumtetrakis (phenyl) boron, N-diethylaniliniumtetrakis (phenyl) boron, N-2,4, 6-pentamethylaniliniumtetrakis (phenyl) boron, di (isopropyl) ammoniumtetra (pentafluorophenyl) boron, N-diethylaniliniumtetrakis (phenyl) boron, N-diethylaniliniumtetrakis, Dicyclohexylammonium tetrakis (phenyl) boron, triphenylphosphonium tetrakis (phenyl) boron, tris (methylphenyl) phosphonium tetrakis (phenyl) boron, tris (dimethylphenyl) phosphonium tetrakis (phenyl) boron, zenium tetrapentafluorophenylborate, triphenylmethyl onium tetrapentafluorophenylborate, benzene (diazonium) tetrapentafluorophenylborate, zenium tetrakis (2,3,5, 6-tetrafluorophenyl) borate, triphenylmethyl onium tetrakis (2,3,5, 6-tetrafluorophenyl) borate, benzene (diazonium) tetrakis (3,4, 5-trifluorophenyl) borate, zenium tetrakis (3,4, 5-trifluorophenyl) borate, benzene (diazonium) tetrakis (3,4, 5-trifluorophenyl) borate, zenium tetrakis (1,2, 2-trifluorovinyl) borate, triphenylmethyl onium tetrakis (1,2, 2-trifluorovinyl) borate, and mixtures thereof, A (diazonium) tetrakis (1,2, 2-trifluorovinyl) borate,-zenithnium tetrakis (2,3,4, 5-tetrafluorophenyl) borate, triphenylmethyl-onium tetrakis (2,3,4, 5-tetrafluorophenyl) borate and benzene (diazonium) tetrakis (2,3,4, 5-tetrafluorophenyl) borate. Readily available commercial ionic activators include N, N-dimethylanilinium tetrapentafluorophenyl borate and triphenylmethyl onium tetrapentafluorophenyl borate.

In one embodiment of the present disclosure, the single-site catalyst used to prepare the second polyethylene produces no long chain branches, and the second polyethylene will contain no measurable amount of long chain branches.

In one embodiment of the present disclosure, the single site catalyst used to prepare the second polyethylene produces long chain branches, and the second polyethylene will contain long chain branches, hereinafter referred to as "LCBs". LCB is a well-known structural phenomenon in polyethylene and is well known to those of ordinary skill in the art. Traditionally, there are three methods for LCB analysis, namely nuclear magnetic resonance spectroscopy (NMR), see for example J.C. Randall, J Macromol. Sci, Rev. Macromol. chem. Phys. 1989, 29, 201, triple detection SEC equipped with DRI, viscometer and small angle laser scattering detector, see for example W.W. Yau and D.R. Hill, int. J. Polymer. anal. Charact. 1996; 2:151; and rheology, see for example W.W. Graessley, Acc. chem. Res. 1977, 10, 332-339. In the present disclosure, the long chain branches are macromolecular in nature, i.e., long enough to be visible in NMR spectra, triple detector SEC experiments, or rheology experiments.

In embodiments of the present disclosure, the molecular weight distribution M of the second polyethylene_w/M_nMay be about2.8, or about 2.5, or about 2.4, or about 2.3, or about 2.2. In embodiments of the present disclosure, the molecular weight distribution M of the second polyethylene_w/M_nThe lower limit of (c) may be about 1.4, or about 1.6, or about 1.7, or about 1.8, or about 1.9.

In embodiments of the present disclosure, the molecular weight distribution M of the second polyethylene_w/M_n< 2.3, or < 2.1, or < 2.0 or about 2.0. In embodiments of the present disclosure, the molecular weight distribution M of the second polyethylene_w/M_nFrom about 1.7 to about 2.2.

In one embodiment of the present disclosure, the second polyethylene has 0 to 100 Short Chain Branches (SCB) per thousand carbon atoms_PE-2). In a further embodiment, the second polyethylene has from 0 to 30 Short Chain Branches (SCB) per thousand carbon atoms_PE-2) Or 0 to 20 Short Chain Branches (SCB) per thousand carbon atoms_PE-2) Or a number of Short Chain Branches (SCB) of 0 to 15 per thousand carbon atoms_PE-2) Or 0 to 10 Short Chain Branches (SCB) per thousand carbon atoms_PE-2) Or 0 to 5 Short Chain Branches (SCB) per thousand carbon atoms_PE-2) Or less than 5 short chain branches per thousand carbon atoms (SCB)_PE-2) Or less than 3 short chain branches per thousand carbon atoms (SCB)_PE-2) Or less than 1 short chain branch per thousand carbon atoms (SCB)_PE-2) Or about zero short chain branches per thousand carbon atoms (SCB)_PE-2)。

Short chain branching (i.e. short chain branching per thousand carbon atoms, SCB)_PE-1) Is branching due to the presence of an alpha-olefin comonomer in the polyethylene and has, for example, two carbon atoms for a 1-butene comonomer, four carbon atoms for a 1-hexene comonomer, or six carbon atoms for a 1-octene comonomer, etc.

In embodiments of the present disclosure, the upper limit of the density d2 of the second polyethylene may be about 0.985g/cm³(ii) a In some cases about 0.975g/cm³And in other cases about 0.965g/cm³. In embodiments of the present disclosure, the lower limit of the density d2 of the second polyethylene may be about 0.921g/cm³And in some cases about 0.932g/cm³And; in other cases about 0.949g/cm³。

In embodiments of the present disclosure, the density d2 of the second polyethylene may be about 0.921g/cm³To about 0.980 g/cm³Or about 0.921g/cm³To about 0.975g/cm³Or about 0.926 g/cm³To about 0.975g/cm³Or about 0.930 g/cm³To about 0.975g/cm³Or about 0.936 g/cm³To about 0.975g/cm³Or about 0.940 g/cm³To about 0.975g/cm³Or about 0.940 g/cm³To about 0.980 g/cm³Or about 0.945 g/cm³To about 0.975g/cm³Or about 0.950 g/cm³To about 0.975g/cm³Or about 0.951 g/cm³To about 0.975g/cm³Or about 0.953 g/cm³To about 0.975g/cm³Or about 0.953 g/cm³To about 0.985g/cm³。

In embodiments of the present disclosure, the second polyethylene has a melt index, I₂ ²Can be from about 0.01 dg/min to about 1000 dg/min, or from about 0.01 dg/min to about 500 dg/min, or from about 0.01 dg/min to about 100 dg/min, or from about 0.01 dg/min to about 50 dg/min, or from about 0.1 dg/min to about 100 dg/min, or from about 0.1 dg/min to about 75 dg/min, or from about 0.1 dg/min to about 50 dg/min, or from about 1 dg/min to about 40 dg/min, or from about 1 dg/min to about 30 dg/min, or from about 1 dg/min to about 25 dg/min, or from about 3 dg/min to about 25 dg/min, or from about 5 dg/min to about 20 dg/min.

In one embodiment of the present disclosure, the weight average molecular weight M of the second polyethylene_wFrom about 10,000 to about 150,000, or from about 10,000 to about 125,000, or from about 15,000 to about 100,000, or from about 15,000 to about 90,000, or from about 15,000 to about 80,000, or from about 20,000 to about 75,000, or from about 25,000 to about 90,000, or from about 25,000 to about 80,000, or from about 25,000 to about 75,000.

In one embodiment of the present disclosure, the weight average molecular weight of the second polyethylene is less than the weight average molecular weight of the first polyethylene.

In one embodiment of the present disclosure, the weight average molecular weight of the second polyethylene is less than the weight average molecular weight of the third polyethylene.

In one embodiment of the present disclosure, the weight average molecular weight of the second polyethylene is less than the weight average molecular weight of both the first polyethylene and the third polyethylene.

In embodiments of the present disclosure, the upper limit of the weight percent (wt%) of the second polyethylene in the polyethylene composition (i.e., the weight percent of the second polyethylene based on the total weight of the first, second, and third polyethylenes) may be about 80 wt%, or about 75wt%, or about 70wt%, or about 65wt%, or about 60wt%, or about 55wt%, or about 50wt%, or about 45wt%, or about 40 wt%. In embodiments of the present disclosure, the lower limit of the wt% of the second polyethylene in the polyethylene composition may be about 5wt%, or about 10 wt%, or about 15 wt%, or about 20 wt%.

Third polyethylene

In one embodiment of the present disclosure, the third polyethylene polymer is made with a multi-site catalyst system, non-limiting examples of which include Ziegler-Natta catalysts and chromium catalysts, both of which are well known in the art.

In one embodiment of the present disclosure, the third polyethylene is made with a ziegler-natta catalyst.

Ziegler-Natta catalyst systems are well known to those skilled in the art. The Ziegler-Natta catalyst may be an in-line Ziegler-Natta catalyst system or a batch Ziegler-Natta catalyst system. The term "in-line ziegler-natta catalyst system" refers to the continuous synthesis of a small amount of active ziegler-natta catalyst system and immediately injecting the catalyst into at least one continuously operating reactor, wherein the catalyst polymerizes ethylene with one or more optional alpha-olefins to form an ethylene polymer. The term "batch ziegler-natta catalyst system" or "batch ziegler-natta procatalyst" means that a much larger amount of catalyst or procatalyst is synthesized outside of, or in one or more mixing vessels separate from, a continuously operated solution polymerization process. Once prepared, the batch Ziegler-Natta catalyst system or batch Ziegler-Natta procatalyst is transferred to a catalyst storage tank. The term "procatalyst" refers to an inactive catalyst system (inactive with respect to ethylene polymerization); the procatalyst is converted to the active catalyst by the addition of an aluminum alkyl cocatalyst. If desired, the procatalyst is pumped from the storage tank to at least one continuously operated reactor, where the active catalyst polymerizes ethylene and one or more optional α -olefins to form polyethylene. The procatalyst may be converted to the active catalyst in the reactor or outside the reactor or on its way to the reactor.

A variety of compounds are useful in the synthesis of active ziegler-natta catalyst systems. Various compounds that can be combined to produce an active Ziegler-Natta catalyst system are described below. One skilled in the art will appreciate that embodiments in the present disclosure are not limited to the particular compounds disclosed.

The active ziegler-natta catalyst system may be formed from: magnesium compounds, chloride compounds, metal compounds, aluminum alkyl cocatalysts and aluminum alkyls. As will be appreciated by those skilled in the art, the ziegler-natta catalyst system may comprise additional components; non-limiting examples of additional components are electron donors, such as amines or ethers.

Non-limiting examples of active in-line (or batch) Ziegler-Natta catalyst systems may be prepared as follows. In a first step, a solution of a magnesium compound is reacted with a solution of a chloride compound to form a magnesium chloride support suspended in the solution. Non-limiting examples of magnesium compounds include Mg (R)¹)₂(ii) a Wherein R is¹The groups may be the same or different straight, branched or cyclic hydrocarbon groups containing from 1 to 10 carbon atoms. Non-limiting examples of chloride compounds include R²Cl; wherein R is²Represents a hydrogen atom, or a linear, branched or cyclic hydrocarbon group having 1 to 10 carbon atoms. In the first step, the solution of the magnesium compound may further comprise an aluminum alkyl. Non-limiting examples of aluminum alkyls include Al (R)³)₃Wherein R is³The radicals may be identical or contain from 1 to 10 carbon atomsDifferent straight, branched or cyclic hydrocarbon groups. In the second step, a solution of a metal compound is added to a solution of magnesium chloride, and the metal compound is supported on magnesium chloride. Non-limiting examples of suitable metal compounds include M (X)_nOr MO (X)_n(ii) a Wherein M represents a metal selected from groups 4 to 8 of the periodic Table of the elements, or a mixture of metals selected from groups 4 to 8; o represents oxygen, and; x represents chloride or bromide; n is an integer of 3 to 6 satisfying the oxidation state of the metal. Other non-limiting examples of suitable metal compounds include alkyl compounds of group 4 to 8 metals, metal alkoxides (which can be prepared by reacting a metal alkyl compound with an alcohol), and mixed ligand metal compounds comprising a mixture of halide, alkyl and alkoxide ligands. In the third step, a solution of an aluminum alkyl cocatalyst is added to the metal compound supported on magnesium chloride. A variety of aluminum alkyl cocatalysts may be suitable as shown in the following formula:

Al(R⁴)_p(OR⁹)_q(X)_r

wherein R is⁴The groups may be the same or different hydrocarbyl groups having from 1 to 10 carbon atoms; OR (OR)⁹The radicals may be identical or different alkoxy or aryloxy radicals, in which R⁹Is an oxygen-bonded hydrocarbon group having 1 to 10 carbon atoms; x is chloride or bromide, and; (p + q + r) =3, provided that p is greater than 0. Non-limiting examples of commonly used alkylaluminum cocatalysts include trimethylaluminum, triethylaluminum, tributylaluminum, dimethylaluminum methoxide, diethylaluminum ethoxide, dibutylaluminum butoxide, dimethylaluminum chloride or bromide, diethylaluminum chloride or bromide, dibutylaluminum chloride or bromide, and ethylaluminum dichloride or dibromide.

The process for the synthesis of active in-line (or batch) Ziegler-Natta catalyst systems described in the preceding paragraphs can be carried out in a wide variety of solvents. Non-limiting examples of solvents include straight or branched C₅To C₁₂Alkanes or mixtures thereof.

In one embodiment of the present disclosure, the third polyethylene is an ethylene copolymer. Suitable alpha-olefins that may be copolymerized with ethylene to obtain the third polyethylene polymer include 1-propene, 1-butene, 1-pentene, 1-hexene and 1-octene.

In one embodiment of the present disclosure, the third ethylene polymer is an ethylene homopolymer.

In one embodiment of the present disclosure, the third ethylene polymer is a heterogeneously branched ethylene copolymer.

In one embodiment of the present disclosure, the third polyethylene is an ethylene/1-octene copolymer.

In embodiments of the present disclosure, the molecular weight distribution M of the third polyethylene_w/M_nNot less than 2.3, or not less than 2.5, or not less than 2.7, or not less than 2.9, or not less than 3.0. In embodiments of the present disclosure, the molecular weight distribution M of the third polyethylene_w/M_nIs 2.3 to 6.5, or 2.3 to 6.0, or 2.3 to 5.5, or 2.3 to 5.0, or 2.3 to 4.5, or 2.3 to 4.0, or 2.5 to 6.0, or 2.5 to 5.5, or 2.5 to 5.0, or 2.5 to 4.5, or 2.5 to 4.0, or 2.7 to 6.0, or 2.7 to 5.5, or 2.7 to 5.0, or 2.7 to 4.5, or 2.9 to 6.5, or 2.9 to 6.0, or 2.9 to 5.5, or 2.9 to 5.0, or 2.9 to 4.5.

In one embodiment of the present disclosure, the third polyethylene has 0 to 100 Short Chain Branches (SCB) per thousand carbon atoms_PE-3). In a further embodiment, the third polyethylene has from 0 to 50 Short Chain Branches (SCB) per thousand carbon atoms_PE-3) Or 0 to 35 Short Chain Branches (SCB) per thousand carbon atoms_PE-3) Or 3 to 30 short chain branches per thousand carbon atoms (SCB)_PE-3) Or 5 to 30 short chain branches per thousand carbon atoms (SCB)_PE-3) Or 5 to 25 short chain branches per thousand carbon atoms (SCB)_PE-3) Or 3 to 25 short chain branches per thousand carbon atoms (SCB)_PE-3) Or 1 to 25 Short Chain Branches (SCB) per thousand carbon atoms_PE-3) Or 0.1 to 20 Short Chain Branches (SCB) per thousand carbon atoms_PE-3)。

Short chain branching (i.e. short chain branching per thousand carbon atoms, SCB)_PE-3) If present, it is due to polyethyleneThe branching that results from the presence of an alpha-olefin comonomer in the alkene, and for example has two carbon atoms for a 1-butene comonomer, four carbon atoms for a 1-hexene comonomer, or six carbon atoms for a 1-octene comonomer, etc.

In one embodiment of the present disclosure, the number of short chain branches per thousand carbon atoms in the third polyethylene polymer (SCB)_PE-3) Greater than the number of short chain branches per thousand carbon atoms in the second polyethylene (SCB)_PE-2)。

In embodiments of the present disclosure, the upper limit of the density d3 of the third polyethylene may be about 0.975g/cm³(ii) a In some cases about 0.965g/cm³And in other cases about 0.955g/cm³. In embodiments of the present disclosure, the lower limit of the density d3 of the third polyethylene may be about 0.855g/cm³And in some cases about 0.865g/cm³(ii) a And in other cases about 0.875g/cm³。

In embodiments of the present disclosure, the density d3 of the third polyethylene may be about 0.875g/cm³To about 0.965g/cm³Or about 0.875g/cm³To about 0.960 g/cm³Or about 0.875g/cm³To 0.950 g/cm³Or about 0.865g/cm³To about 0.940 g/cm³Or about 0.865g/cm³To about 0.936 g/cm³Or about 0.865g/cm³To about 0.932g/cm³Or about 0.865g/cm³To about 0.926 g/cm³Or about 0.865g/cm³To about 0.921g/cm³Or about 0.865g/cm³To about 0.918 g/cm³Or about 0.875g/cm³To about 0.916 g/cm³Or about 0.875g/cm³To about 0.916 g/cm³Or about 0.865g/cm³To about 0.912 g/cm³Or about 0.880 g/cm³To about 0.912 g/cm³Or about 0.890 g/cm³To about 0.916 g/cm³Or about 0.900 g/cm³To about 0.916 g/cm³Or about 0.880 g/cm³To about 0.916 g/cm³Or about 0.880 g/cm³To about 0.918 g/cm³Or about 0.880 g/cm³To about 0.921g/cm³Or about 0.880 g/cm³To about 0.926 g/cm³Or about 0.880 g/cm³To about 0.932g/cm³Or about 0.880 g/cm³To about 0.936 g/cm³。

In one embodiment of the present disclosure, the third polyethylene is the composition distribution breadth index, CDBI₅₀Is 75wt% or less, or 70wt% or less of an ethylene copolymer. In a further embodiment of the disclosure, the third polyethylene is CDBI₅₀Is 65wt% or less, or 60wt% or less, or 55wt% or less, or 50wt% or less, or 45wt% or less of an ethylene copolymer.

In embodiments of the present disclosure, the melt index I of the third polyethylene₂ ³Can be from about 0.01 dg/min to about 1000 dg/min, or from about 0.01 dg/min to about 500 dg/min, or from about 0.01 dg/min to about 100 dg/min, or from about 0.01 dg/min to about 50 dg/min, or from about 0.01 dg/min to about 25 dg/min, or from about 0.01 dg/min to about 10 dg/min, or from about 0.01 dg/min to about 5 dg/min, or from about 0.01 dg/min to about 3 dg/min, or from about 0.01 dg/min to about 1 dg/min, or less than about 5 dg/min, or less than about 3 dg/min, or less than about 1.0 dg/min, or less than about 0.75 dg/min, or less than about 0.50 dg/min.

In one embodiment of the present disclosure, the weight average molecular weight M of the third polyethylene_wFrom about 50,000 to about 300,000, or from about 50,000 to about 250,000, or from about 60,000 to about 250,000, or from about 70,000 to about 250,000, or from about 75,000 to about 200,000, or from about 80,000 to about 275,000, or from about 80,000 to about 250,000, or from about 80,000 to about 200,000, or from 70,000 to about 200,000, or from about 80,000 to about 175,000.

In one embodiment of the present disclosure, the weight average molecular weight M of the third polyethylene_wGreater than the weight average molecular weight M of the first polyethylene_w。

In one embodiment of the present disclosure, the weight average molecular weight M of the third polyethylene_wGreater than the weight average molecular weight M of the second polyethylene_w。

In embodiments of the present disclosure, the upper limit of the weight percent (wt%) of the third polyethylene in the polyethylene composition (i.e., the weight percent of the third polyethylene based on the total weight of the first, second, and third polyethylenes) may be about 90 wt%, or about 85 wt%, or about 80 wt%, or about 75wt%, or 65wt%, in other cases about 60wt%, in other cases about 55wt%, or about 50wt%, or about 45 wt%. In embodiments of the present disclosure, the lower limit of the weight% of the third polyethylene in the final polyethylene product may be about 5 weight%, or about 10 weight%, or about 15 weight%, or about 20 weight%, or about 25 weight%, or about 30 weight%, or about 35 weight%, or in other cases about 40 weight%.

In one embodiment of the present disclosure, the third polyethylene is free of long chain branches or does not have any detectable level of long chain branches.

Polyethylene composition

The polyethylene compositions disclosed herein may be prepared using any technique well known in the art, including but not limited to melt blending, solution blending, or in-reactor blending to mix the first, second, and third polyethylenes together.

In one embodiment, the polyethylene composition of the present disclosure is obtained by melt blending or solution blending three different polyethylene components: i) a first polyethylene, ii) a second polyethylene, and iii) a third polyethylene.

In one embodiment, the polyethylene composition of the present disclosure is prepared by melt blending or solution blending two different polyethylene components: i) a first polyethylene component comprising a first polyethylene and a second polyethylene, and ii) a second polyethylene component comprising a third polyethylene.

In one embodiment, the polyethylene composition of the present disclosure is prepared by melt blending or solution blending two different polyethylene components: i) a first polyethylene component comprising a first polyethylene and ii) a second polyethylene component comprising a second polyethylene and a third polyethylene.

In one embodiment, the polyethylene composition of the present disclosure is prepared by melt blending or solution blending two different polyethylene components: i) a first polyethylene component comprising a first polyethylene and a third polyethylene, and ii) a second polyethylene component comprising a second polyethylene.

In one embodiment, the polyethylene composition of the present disclosure is produced using the same single-site catalyst in two different reactors, wherein each reactor is operated under different polymerization conditions to yield a first polyethylene and a second polyethylene, and a multi-site catalyst is used in the other reactor to yield a third polyethylene.

In one embodiment, the polyethylene composition of the present disclosure is produced using different single-site catalysts in two different reactors, wherein each reactor is operated under similar or different polymerization conditions to yield a first polyethylene and a second polyethylene, and a multi-site catalyst in the other reactor to yield a third polyethylene.

The present disclosure also contemplates that polymer compositions comprising first, second, and third polyethylenes can be prepared in one or more polymerization reactors using two different single-site polymerization catalysts and one multi-site polymerization catalyst, wherein each catalyst has a different response to one or more of the following under a given set of polymerization conditions: the hydrogen concentration, ethylene concentration, comonomer concentration and temperature are such that a first polyethylene is produced with a first single-site catalyst, a second polyethylene is produced with a second single-site catalyst and a third polyethylene is produced with a multi-site catalyst.

The present disclosure also contemplates that a polymer composition comprising first, second, and third polyethylenes can be produced in one or more polymerization reactors using one or more single-site polymerization catalysts and one multi-site catalyst, wherein each catalyst has a similar or different response to one or more of the following under a given set of polymerization conditions: hydrogen concentration, ethylene concentration, comonomer concentration and temperature, and wherein one or more of hydrogen concentration, ethylene concentration, comonomer concentration and temperature are cycled over a range such that first, second and third polyethylenes are produced over the one or more single-site catalysts and the one or more multi-site catalysts present in the one or more polymerization reactors.

In one embodiment, a polyethylene composition of the present disclosure is prepared by: forming a first polyethylene by polymerizing ethylene and alpha-olefins with a single-site catalyst in a first reactor; forming a second polyethylene in a second reactor by polymerizing ethylene and optionally an alpha-olefin with a single-site catalyst; and forming a third polyethylene polymer by polymerizing ethylene and optionally an alpha-olefin with a multi-site catalyst in a third reactor, wherein at least two of the first, second and third reactors are configured in series with each other.

In one embodiment, a polyethylene composition of the present disclosure is prepared by: forming a first polyethylene by polymerizing ethylene and alpha-olefins with a single-site catalyst in a first solution phase polymerization reactor; forming a second polyethylene by polymerizing ethylene and optionally an alpha-olefin with a single-site catalyst in a second solution phase polymerization reactor; and forming a third polyethylene polymer by polymerizing ethylene and optionally an alpha-olefin with a multi-site catalyst in a third solution phase polymerization reactor.

In one embodiment, a polyethylene composition of the present disclosure is prepared by: forming a first polyethylene by polymerizing ethylene and alpha-olefins with a single-site catalyst in a first solution phase polymerization reactor; forming a second polyethylene by polymerizing ethylene and optionally an alpha-olefin with a single-site catalyst in a second solution phase polymerization reactor; and forming a third polyethylene polymer by polymerizing ethylene and optionally an alpha-olefin with a multi-site catalyst in a third solution phase polymerization reactor, wherein at least two of the first, second and third solution phase polymerization reactors are configured in series with each other.

In one embodiment, a polyethylene composition of the present disclosure is prepared by: forming a first polyethylene by polymerizing ethylene and alpha-olefins with a single-site catalyst in a first solution phase polymerization reactor; forming a second polyethylene by polymerizing ethylene and optionally an alpha-olefin with a single-site catalyst in a second solution phase polymerization reactor; and forming a third polyethylene polymer by polymerizing ethylene and optionally alpha-olefins with a multi-site catalyst in a third solution phase polymerization reactor, wherein the first and second solution phase polymerization reactors are configured in series with each other.

In one embodiment, a polyethylene composition of the present disclosure is prepared by: forming a first polyethylene by polymerizing ethylene and alpha-olefins with a single-site catalyst in a first reactor; forming a second polyethylene in a second reactor by polymerizing ethylene and optionally an alpha-olefin with a single-site catalyst; and forming a third polyethylene polymer by polymerizing ethylene and optionally an alpha-olefin with a multi-site catalyst in a third reactor, wherein each of the first, second and third reactors are configured in parallel with each other.

In one embodiment, a polyethylene composition of the present disclosure is prepared by: forming a first polyethylene by polymerizing ethylene and alpha-olefins with a single-site catalyst in a first solution phase polymerization reactor; forming a second polyethylene by polymerizing ethylene and optionally an alpha-olefin with a single-site catalyst in a second solution phase polymerization reactor; and forming a third polyethylene polymer by polymerizing ethylene and optionally an alpha-olefin with a multi-site catalyst in a third solution phase polymerization reactor, wherein each of the first, second and third solution phase polymerization reactors are configured in parallel with each other.

In one embodiment, a polyethylene composition of the present disclosure is prepared by: forming a first polyethylene by polymerizing ethylene and alpha-olefins with a single-site catalyst in a first reactor; forming a second polyethylene in a second reactor by polymerizing ethylene and optionally an alpha-olefin with a single-site catalyst; and forming a third polyethylene polymer by polymerizing ethylene and optionally alpha-olefins with a multi-site catalyst in a third reactor, wherein the first and second reactors are configured in series with each other and the third reactor is configured in parallel with the first and second reactors.

In one embodiment, a polyethylene composition of the present disclosure is prepared by: forming a first polyethylene by polymerizing ethylene and an alpha-olefin with a single-site catalyst in a first solution phase reactor; forming a second polyethylene by polymerizing ethylene and optionally an alpha-olefin with a single-site catalyst in a second solution phase reactor; and forming a third polyethylene polymer by polymerizing ethylene and optionally an alpha-olefin with a multi-site catalyst in a third solution phase reactor, wherein the first and second solution phase reactors are configured in series with each other and the third solution phase reactor is configured in parallel with the first and second reactors.

In one embodiment, the solution phase polymerization reactor used as the first solution phase reactor, the second solution phase reactor, or the third solution phase reactor is a continuous stirred tank reactor.

In one embodiment, the solution phase polymerization reactor used as the first solution phase reactor, the second solution phase reactor, or the third solution phase reactor is a tubular reactor.

In solution phase polymerization reactors, a variety of solvents may be used as process solvents; non-limiting examples include straight, branched or cyclic C₅To C₁₂An alkane. Non-limiting examples of alpha-olefins include 1-propene, 1-butene, 1-pentene, 1-hexene, and 1-octene. Suitable catalyst component solvents include aliphatic and aromatic hydrocarbons. Non-limiting examples of aliphatic catalyst component solvents include straight chain, branched chain or cyclic C_5-12Aliphatic hydrocarbons such as pentane, methylpentane, hexane, heptane, octane, cyclohexane, cyclopentane, methylcyclohexane, hydrogenated naphtha or combinations thereof. Non-limiting examples of aromatic catalyst component solvents include benzene, toluene (methylbenzene), ethylbenzene, ortho-xylene (1, 2-xylene), meta-xylene (1, 3-xylene), para-xylene (1, 4-xylene), xylene isomer mixtures, hemimellites (1,2, 3-trimethylbenzene), hemimellites (1,2, 4-trimethylbenzene), mesitylenes (1,3, 5-trimethylbenzene), trimethylbenzene isomersMixtures of (a), netetratoluene (1,2,3, 4-tetramethylbenzene), durene (1,2,3, 5-tetramethylbenzene), mixtures of tetramethylbenzene isomers, pentamethylbenzene, hexamethylbenzene, and combinations thereof.

In embodiments of the present disclosure, the polyethylene composition may have a density of about 0.880 g/cm³To about 0.965g/cm³Or about 0.885 g/cm³To about 0.960 g/cm³Or about 0.890 g/cm³To 0.950 g/cm³Or about 0.895 g/cm³To about 0.940 g/cm³Or about 0.900 g/cm³To about 0.936 g/cm³Or about 0.905 g/cm³To about 0.934 g/cm³Or about 0.910 g/cm³To about 0.932g/cm³Or about 0.910 g/cm³To about 0.930 g/cm³Or about 0.910 g/cm³To about 0.926 g/cm³Or about 0.890 g/cm³To about 0.924 g/cm³Or about 0.890 g/cm³To about 0.922 g/cm³Or about 0.890 g/cm³To about 0.920 g/cm³Or about 0.890 g/cm³To about 0.918 g/cm³Or about 0.880 g/cm³To about 0.922 g/cm³Or about 0.880 g/cm³To about 0.926 g/cm³Or about 0.880 g/cm³To about 0.932g/cm³Or less than or equal to 0.948 g/cm³Or < 0.948 g/cm³Or less than or equal to 0.945 g/cm³Or < 0.945 g/cm³Or less than or equal to 0.940 g/cm³Or < 0.940 g/cm³Or less than or equal to 0.939 g/cm³Or < 0.939 g/cm³Or less than or equal to 0.935 g/cm³Or < 0.935 g/cm³Or less than or equal to 0.932g/cm³Or < 0.932g/cm³。

In embodiments of the present disclosure, the polyethylene composition has a melt index I₂Can be from about 0.01 dg/min to about 1000 dg/min, or from about 0.01 dg/min to about 500 dg/min, or from about 0.01 dg/min to about 100 dg/min, or from about 0.01 dg/min to about 50 dg/min, or from about 0.01 dg/min to about 25 dg/min, or from about 0.01 dg/min to about 10 dg/min, or from about 0.01 dg/min to about 5 dg/min, or from about 0.01 dg/min to about 3 dg/min, or from about 0.01 dg/min to about 1 dg/min, or about 0.1 dg/min to about 10 dg/min, or about 0.1 dg/min to about 5 dg/min, or about 0.1 dg/min to about 3 dg/min, or about 0.1 dg/min to about 2 dg/min, or about 0.1 dg/min to about 1.5 dg/min, or about 0.1 dg/min to about 1 dg/min, or less than about 5 dg/min, or less than about 3 dg/min, or less than about 1.0 dg/min.

In embodiments of the present disclosure, the high load melt index I of the polyethylene composition₂₁Can be from about 15 dg/min to about 10,000 dg/min, or from about 15 dg/min to about 1000 dg/min, or from about 15 dg/min to about 100 dg/min, or from about 15 dg/min to about 75 dg/min, or from about 15 dg/min to about 50 dg/min, or from about 10 dg/min to about 100 dg/min, or from about 10 dg/min to about 75 dg/min, or from about 10 dg/min to about 50 dg/min, or from about 10 dg/min to about 45 dg/min, or from about 10 dg/min to about 40 dg/min, or from about 10 dg/min to about 35 dg/min, or from about 10 dg/min to about 32 dg/min, or from about 10 dg/min to about 36 dg/min.

In one embodiment of the present disclosure, the polyethylene composition has a melt flow ratio, I₂₁/I₂Less than or equal to 40. In embodiments of the present disclosure, the polyethylene composition has a melt flow ratio, I₂₁/I₂May be from about 15 to about 40, or from about 15 to about 38, or from about 18 to about 40, or from about 20 to about 40, or from about 25 to about 40, or from about 28 to about 40.

In embodiments of the present disclosure, the polyethylene composition has a weight average molecular weight, M_wFrom about 50,000 to about 300,000, or from about 50,000 to about 250,000, or from about 60,000 to about 250,000, or from about 70,000 to about 225,000, or from about 70,000 to about 200,000, or from about 75,000 to about 175,000, or from about 75,000 to about 150,000, or from about 100,000 to about 130,000.

In embodiments of the present disclosure, the polyethylene composition has a molecular weight distribution, M_w/M_nThe lower limit of (b) is 2.0, or 2.1, or 2.3, or 2.5. In embodiments of the present disclosure, the polyethylene composition has a molecular weight distribution, M_w/M_nThe upper limit of (d) is 6.0, or 5.5, or 5.0, or 4.5, or 4.0, or 3.5, or 3.0. In embodiments of the present disclosure, the polyethylene composition has a molecular weight distribution, M_w/M_nIs from 2.1 to 6.0, or from 2.3 to 6.0, or from 2.5 to 6.0, or from 2.1 to 5.5, or from 2.3 to 5.5,or 2.1 to 5.0, or 2.3 to 5.0, or 2.1 to 4.5, or 2.3 to 4.5, or 2.1 to 4.0, or 2.3 to 4.0, or 2.1 to 3.5, or 2.3 to 3.5, or 2.1 to 3.0, or 2.3 to 3.0.

In embodiments of the present disclosure, the Z-average molecular weight distribution M of the polyethylene composition_Z/M_WLess than or equal to 4.0, or less than or equal to 3.5, or less than or equal to 3.0, or less than or equal to 2.75, or less than or equal to 2.50. In embodiments of the present disclosure, the Z-average molecular weight distribution M of the polyethylene composition_Z/M_WIs 1.5 to 4.0, or 1.75 to 3.5, or 1.75 to 3.0, or 2.0 to 4.0, or 2.0 to 3.5, or 2.0 to 3.0, or 2.0 to 2.5.

In one embodiment of the present disclosure, the polyethylene composition has a monomodal distribution in a gel permeation chromatogram generated according to ASTM D6474-99. The term "monomodal" as defined herein means that only one significant peak or maximum is clearly visible in the GPC curve. The monomodal distribution includes a broad monomodal distribution. In contrast, the term "bimodal" is used to mean that in addition to the first peak, there is a minor peak or shoulder which represents a higher or lower molecular weight component (i.e., it can be said that the molecular weight distribution has two maxima in the molecular weight distribution curve). Alternatively, the term "bimodal" means that there are two maxima in the molecular weight distribution curve generated according to ASTM D6474-99. The term "multimodal" means that there are two or more (usually more than two) maxima in the molecular weight distribution curve generated according to the method of ASTM D6474-99.

In one embodiment of the present disclosure, the polyethylene composition may have a multimodal distribution in a Differential Scanning Calorimetry (DSC) diagram. In the context of DSC analysis, the term "multimodal" means that two or more distinct melting peaks are observed in the DSC curve.

In one embodiment of the present disclosure, the polyethylene composition may have a bimodal distribution in a Differential Scanning Calorimetry (DSC) plot. In the context of DSC analysis, the term "bimodal" means that two distinct melting peaks are observed in the DSC curve.

In one embodiment of the present disclosure, the polyethylene composition has a melting peak temperature in Differential Scanning Calorimetry (DSC) analysis at above 120 ℃. For clarity, the phrase "having a melting peak temperature in a DSC analysis" means that at least one such peak occurs above the indicated temperature in the DSC analysis, although one or more distinct melting peaks may be present. In one embodiment of the present disclosure, the polyethylene composition has a melting peak temperature in Differential Scanning Calorimetry (DSC) analysis at greater than 123 ℃. In one embodiment of the present disclosure, the polyethylene composition has a melting peak temperature in Differential Scanning Calorimetry (DSC) analysis at greater than 125 ℃.

In one embodiment of the present disclosure, the polyethylene composition will have a reversed or partially reversed comonomer distribution curve as measured using GPC-FTIR. If the incorporation of comonomer decreases with molecular weight, as measured using GPC-FTIR, this distribution is described as "normal". Such comonomer distribution is described as "flat" or "uniform" if the incorporation of comonomer is approximately constant with molecular weight, as measured using GPC-FTIR. The terms "reverse comonomer distribution" and "partially reverse comonomer distribution" mean that in the obtained GPC-FTIR data of the copolymer, one or more higher molecular weight components have a higher comonomer incorporation than in one or more lower molecular weight components. The term "reverse comonomer distribution" as used herein means that the comonomer content of the various polymer fractions is not substantially uniform and their higher molecular weight fractions proportionally have a higher comonomer content throughout the molecular weight range of the ethylene copolymer (i.e., such distributions are described as "reversed" or "reversed" if comonomer incorporation increases with molecular weight.

In one embodiment of the present disclosure, the polyethylene composition has a reverse comonomer distribution curve as measured using GPC-FTIR.

In one embodiment of the present disclosure, the polyethylene composition has a partial reverse comonomer distribution curve as measured using GPC-FTIR.

In one embodiment of the present disclosure, the polyethylene composition has a solubility fraction of at least 10 wt% in a Crystallization Elution Fraction (CEF) analysis, wherein the solubility fraction is defined as the weight percent (wt%) of material eluting at 30 ℃ and below. In one embodiment of the present disclosure, the polyethylene composition has a soluble fraction of at least 15 wt% in a Crystallization Elution Fraction (CEF) analysis, wherein the soluble fraction is defined as the weight percent (wt%) of material eluting at 30 ℃ and below. In one embodiment of the present disclosure, the polyethylene composition has a solubility fraction of at least 17 wt% in a Crystallization Elution Fraction (CEF) analysis, wherein the solubility fraction is defined as the weight percent (wt%) of material eluting at 30 ℃ and below. In one embodiment of the present disclosure, the polyethylene composition has a solubility fraction of at least 20 wt% in a Crystallization Elution Fraction (CEF) analysis, wherein the solubility fraction is defined as the weight percent (wt%) of material eluting at 30 ℃ and below. In one embodiment of the present disclosure, the polyethylene composition has a solubility fraction of at least 25 wt% in a Crystallization Elution Fraction (CEF) analysis, wherein the solubility fraction is defined as the weight percent (wt%) of material eluting at 30 ℃ and below. In one embodiment of the present disclosure, the polyethylene composition has a soluble fraction in a Crystallization Elution Fraction (CEF) analysis of 10 to 40 wt%, wherein the soluble fraction is defined as the weight percent (wt%) of material eluting at 30 ℃ and below. In one embodiment of the present disclosure, the polyethylene composition has a soluble fraction in a Crystallization Elution Fraction (CEF) analysis of 15 to 35 wt%, wherein the soluble fraction is defined as the weight percent (wt%) of material eluting at 30 ℃ and below.

In one embodiment of the present disclosure, the polyethylene composition is defined as Log₁₀[I₆/I₂]/Log₁₀[6.48/2.16]The stress index is less than or equal to 1.50. In further embodiments of the present disclosureStress index Log of polyethylene composition₁₀[I₆/I₂]/Log₁₀[6.48/2.16]Less than 1.48, or less than 1.45, or less than 1.43.

In one embodiment of the disclosure, the polyethylene composition has a hexane extractables value of 5.0 wt.% or less, or less than 4.0 wt.%, or less than 3.0 wt.%, or less than 2.0 wt.%, or less than 1.0 wt.%.

The polyethylene compositions disclosed herein may be converted into flexible articles such as monolayer or multilayer films. Such membranes are well known to those skilled in the art; non-limiting examples of methods of making such films include blown film and cast film methods.

In the blown film extrusion process, an extruder heats, melts, mixes, and conveys a thermoplastic or thermoplastic blend. Once melted, the thermoplastic is forced through an annular die to produce a thermoplastic tube. In the case of coextrusion, a plurality of extruders are used to produce the multilayer thermoplastic tube. The temperature of the extrusion process is determined primarily by the thermoplastic or thermoplastic blend being processed, for example the melting temperature or glass transition temperature of the thermoplastic and the desired melt viscosity. In the case of polyolefins, typical extrusion temperatures are 330 ° f to 550 ° f (166 ℃ to 288 ℃). After exiting the annular die, the thermoplastic tube is inflated, cooled, solidified, and drawn through a pair of rolls. As a result of the inflation, the diameter of the tube increases, forming bubbles of the desired size. The bubbles stretch in the longitudinal direction due to the drawing action of the rolls. Thus, the bubbles stretch in two directions: transverse Direction (TD), where the inflation of air increases the diameter of the bubbles; and a Machine Direction (MD) where the nip rolls stretch the bubbles. Thus, the physical properties of blown films are generally anisotropic, i.e., the physical properties in the MD and TD directions differ; for example, film tear strength and tensile properties are typically different in the MD and TD directions. In some prior art documents, the term "cross direction" or "CD" is used; these terms are equivalent to the terms "transverse direction" or "TD" as used in this disclosure. During blown film, air is also blown on the outer bubble perimeter to cool the thermoplastic as it exits the annular die. The final width of the membrane is determined by controlling the pressure of the air charge or internal bubbles; in other words, by increasing or decreasing the bubble diameter. Film thickness is controlled primarily by increasing or decreasing the speed of the nip rolls to control the draw-down rate. Upon exiting the rolls, the bubble or tube collapses and can be slit longitudinally to form a sheet. Each sheet may be wound into a roll. Each roll may be further slit to produce a film of the desired width. Each roll of film is further processed into various consumer products as described below.

Cast film processes are similar in that a single or multiple extruders may be used; however, various thermoplastics are metered into flat dies and extruded into single or multilayer sheets, rather than tubes. In the cast film method, the extruded sheet is solidified on a cooling roll.

The disclosed polyethylene compositions can be converted into films spanning a wide range of thicknesses depending on the end use application. Non-limiting examples include food packaging films, wherein the thickness may be in a range of about 0.5 mils (13 μm) to about 4 mils (102 μm); and; in heavy bag applications, the film thickness may range from about 2 mils (51 μm) to about 10 mils (254 μm).

The polyethylene compositions disclosed herein may be used in monolayer films; wherein the monolayer may comprise more than one polyethylene composition and/or other thermoplastic; non-limiting examples of thermoplastics include polyethylene polymers and propylene polymers. The lower limit of the weight percent of the polyethylene composition in the monolayer film may be about 3 wt%, in other cases about 10 wt%, and in still other cases about 30 wt%. The upper limit of the weight percent of the polyethylene composition in the monolayer film may be 100 wt%, in other cases about 90 wt%, and in still other cases about 70 wt%.

The polyethylene compositions disclosed herein may also be used in one or more layers of a multilayer film; non-limiting examples of multilayer films include three, five, seven, nine, eleven, or more layers. The thickness of a particular layer (including the polyethylene composition) within the multilayer film may be about 5%, in other cases about 15%, and in still other cases about 30% of the total thickness of the multilayer film. In other embodiments, the thickness of a particular layer (including the polyethylene composition) within a multilayer film may be about 95%, in other cases about 80%, and in still other cases about 65% of the total thickness of the multilayer film. Each individual layer of the multilayer film may comprise more than one polyethylene composition and/or other thermoplastic.

Other embodiments include laminates and coatings wherein the single or multilayer film comprising the disclosed polyethylene composition is extrusion laminated or adhesive laminated or extrusion coated. In extrusion lamination or adhesive lamination, two or more substrates are bonded together with a thermoplastic or adhesive, respectively. In extrusion coating, a thermoplastic is applied to the surface of a substrate. These methods are well known to those skilled in the art. Typically, adhesive lamination or extrusion lamination is used to bond different materials, non-limiting examples include bonding a paper web to a thermoplastic web, or bonding a web containing aluminum foil to a thermoplastic web, or bonding two chemically incompatible thermoplastic webs, such as bonding a web containing a polyethylene composition to a polyester or polyamide web. Prior to lamination, the webs containing the disclosed polyethylene compositions may be monolayer or multilayer. Prior to lamination, the individual webs may be surface treated to improve adhesion, a non-limiting example of which is corona treatment. The first web or film may have laminated to it on its upper surface, its lower surface, and its upper and lower surfaces a second web. The second and third webs may be laminated to the first web; wherein the second web and the third web are chemically different. As non-limiting examples, the second or third web may comprise: polyamide, polyester and polypropylene, or webs containing layers of barrier resins such as EVOH. Such webs may also contain a vapor deposition barrier layer; such as thin silicon oxide (SiO)_x) Or aluminum oxide (AlO)_x) And (3) a layer. The multi-layer web (or film) may comprise three, five, seven, nine, eleven or more layers.

The polyethylene compositions disclosed herein may be used in a wide range of articles comprising one or more films or film layers (monolayer or multilayer). Non-limiting examples of such articles include: food packaging films (fresh and frozen foods, liquid and granular foods), stand up bags, retortable packages and lined pouch packages; barrier films (oxygen, moisture, aroma, oil, etc.) and modified atmosphere packaging (modified atmosphere packaging); light and heavy shrink films and packaging, collation shrink films, pallet shrink films, shrink bags, shrink strapping and shrink hoods; light and heavy duty stretch films, hand stretch packaging, mechanical stretch packaging, and stretch hood films; a highly transparent film; a heavy duty bag; household wrappage, outer wrapping film and sandwich bag; industrial and institutional films, trash bags, can liners, magazine skins, newspaper bags, mailbags, sacks and envelopes, blister packs, carpet films, furniture bags, garment bags, coin bags, automotive panel films; medical applications such as gowns, drapes, and surgical gowns; building films and boards, asphalt films, heat-insulating bags, shielding films, landscaping films and bags; geomembrane liners for municipal waste treatment and mining applications; packaging bags in batches; agricultural films, mulching films and greenhouse films; in-store packaging, self-service bags, top-quality bags, grocery bags, take-out bags and T-shirt bags; functional film layers, such as sealants and/or toughness layers, in oriented films, longitudinally and biaxially oriented films, and oriented polypropylene (OPP) films. Other articles comprising one or more films comprising at least one polyethylene composition include laminates and/or multilayer films; sealants and tie layers in multilayer films and composites; a laminate with paper; an aluminum foil laminate or a laminate containing vacuum deposited aluminum; a polyamide laminate; a polyester laminate; extrusion coating the laminate, and; a hot melt adhesive formulation. The articles outlined in this paragraph comprise at least one layer (monolayer or multilayer) of a film comprising at least one embodiment of the disclosed polyethylene composition.

The desired film physical properties (single or multiple layers) generally depend on the application of interest. Non-limiting examples of desirable film physical properties include: optical properties (gloss, haze and clarity), dart impact, Elmendorf tear, modulus (1% and 2% secant modulus), puncture-propagation tear resistance (puncture-propagation tear resistance), tensile properties (yield strength, breaking strength, elongation at break, toughness, etc.), and heat seal properties (heat seal initiation temperature and hot tack strength). Specific hot tack and heat seal properties are required in high speed vertical and horizontal form-fill-seal processes for loading and sealing commercial products (liquids, solids, pastes, parts, etc.) inside pouch-like packages.

In addition to the desired film physical properties, it is also desirable that the disclosed polyethylene compositions be easily processed on a film line. The term "processibility" is often used by those skilled in the art to distinguish polymers with improved processibility over less processible polymers. One common measure to quantify processability is extrusion pressure; more specifically, polymers with improved processability have lower extrusion pressures (on blown film or cast film extrusion lines) relative to less processable polymers.

In one embodiment of the present disclosure, the film or film layer comprises the polyethylene composition described above.

In embodiments of the present disclosure, the film or film layer comprises the polyethylene composition described above and has a thickness of from 0.5 to 10 mils.

In embodiments of the present disclosure, the film or film layer has a thickness of 0.5 to 10 mils.

In embodiments of the present disclosure, the films have a dart impact strength of ≥ 400 g/mil, or ≥ 450 g/mil, or ≥ 500 g/mil, or ≥ 600 g/mil, or ≥ 700 g/mil. In another embodiment of the present disclosure, the film has a dart impact strength of from 400 g/mil to 950 g/mil. In another embodiment of the present disclosure, the film has a dart impact strength of from 400 g/mil to 850 g/mil. In another embodiment of the present disclosure, the film has a dart impact strength of from 500 g/mil to 900 g/mil. In yet another embodiment of the present disclosure, the film has a dart impact strength of 550 g/mil to 850 g/mil. In yet another embodiment of the present disclosure, the film has a dart impact strength of from 600 g/mil to 850 g/mil. In yet another embodiment of the present disclosure, the film has a dart impact strength of from 600 g/mil to 800 g/mil.

In embodiments of the present disclosure, the 1 mil film has a Machine Direction (MD) secant modulus at 1% strain of 150 MPa or greater, or 160 MPa or greater, or 170 MPa or greater, or 180 MPa or greater, or 190 MPa or greater, or 200 MPa or greater. In another embodiment of the present disclosure, the 1 mil film has a Machine Direction (MD) secant modulus at 1% strain of from 150 MPa to 280 MPa. In one embodiment of the present disclosure, the Machine Direction (MD) secant modulus of a 1 mil film at 1% strain is from 160 MPa to 260 MPa. In one embodiment of the present disclosure, the Machine Direction (MD) secant modulus of a 1 mil film at 1% strain is from 170 MPa to 250 MPa. In another embodiment of the present disclosure, the Machine Direction (MD) secant modulus of a 1 mil film at 1% strain is from 180 MPa to 240 MPa. In another embodiment of the present disclosure, the 1 mil film has a Machine Direction (MD) secant modulus at 1% strain of 180 MPa to 230 MPa.

In one embodiment of the present disclosure, the 1 mil film has a Transverse Direction (TD) secant modulus of 190 MPa or greater, or 200 MPa or greater, or 210 MPa or greater, or 220 MPa or greater, or 230 MPa or greater at 1% strain. In one embodiment of the present disclosure, the Transverse Direction (TD) secant modulus of a 1 mil film at 1% strain is from 160 MPa to 300 MPa. In another embodiment of the present disclosure, the Transverse Direction (TD) secant modulus of a 1 mil film at 1% strain is from 160 MPa to 280 MPa. In another embodiment of the present disclosure, the Transverse Direction (TD) secant modulus of the 1 mil film at 1% strain is from 170 MPa to 290 MPa. In another embodiment of the present disclosure, the Transverse Direction (TD) secant modulus of a 1 mil film at 1% strain is from 180 MPa to 290 MPa. In another embodiment of the present disclosure, the Transverse Direction (TD) secant modulus of the 1 mil film at 1% strain is from 190 MPa to 280 MPa. In another embodiment of the present disclosure, the Transverse Direction (TD) secant modulus of a 1 mil film at 1% strain is from 190 MPa to 270 MPa.

In embodiments of the present disclosure, the 1 mil film has a tensile strength at break in the Machine Direction (MD) of 40 MPa or greater, or 45MPa or greater, or 50 MPa or greater. In one embodiment of the present disclosure, the 1 mil film has a tensile strength at break in the machine direction of 30 MPa to 70 MPa. In one embodiment of the present disclosure, the 1 mil film has a Machine Direction (MD) tensile strength at break of from 35 MPa to 70 MPa. In another embodiment of the present disclosure, the 1 mil film has a Machine Direction (MD) tensile strength at break of 40 MPa to 70 MPa.

In embodiments of the present disclosure, the film has a Machine Direction (MD) tear strength of 160 g/mil or greater, or 170 g/mil or greater, or 180 g/mil or greater, or 190 g/mil or greater, or 200 g/mil or greater, or 210 g/mil or greater, or 220 g/mil or greater, or 230 g/mil or greater, or 240 g/mil or greater, or 250 g/mil. In one embodiment of the present disclosure, the film has a Machine Direction (MD) tear strength of from 150 g/mil to 320 g/mil. In one embodiment of the present disclosure, the film has a Machine Direction (MD) tear strength of from 160 g/mil to 320 g/mil. In one embodiment of the present disclosure, the film has a Machine Direction (MD) tear strength of from 160 g/mil to 310 g/mil. In one embodiment of the present disclosure, the film has a Machine Direction (MD) tear strength of from 170 g/mil to 300 g/mil.

In embodiments of the present disclosure, the 1 mil film has a slow puncture resistance value of 45J/mm or greater, or 50J/mm or greater, or 55J/mm or greater. In embodiments of the present disclosure, a 1 mil film has a slow puncture resistance value of 40J/mm to 90J/mm, or 50J/mm to 80J/mm.

In embodiments of the present disclosure, the haze of a 1 mil film is 25% or less, or 23% or less, 20% or less, or 15% or less. In embodiments of the present disclosure, the 1 mil film has a haze of 7% to 25%, or 8% to 23%.

In embodiments of the present disclosure, a 2 mil film has a Seal Initiation Temperature (SIT) of 100 ℃ or less, or 95 ℃ or less, or 90 ℃ or less, or 85 ℃ or less. In one embodiment of the present disclosure, the Seal Initiation Temperature (SIT) of a 2 mil film is between 65 ℃ and 100 ℃. In one embodiment of the present disclosure, the Seal Initiation Temperature (SIT) of a 2 mil film is between 75 ℃ and 100 ℃. In one embodiment of the present disclosure, the Seal Initiation Temperature (SIT) of a 2 mil film is between 75 ℃ and 95 ℃. In one embodiment of the present disclosure, the Seal Initiation Temperature (SIT) of a 2 mil film is between 80 ℃ and 95 ℃.

In one embodiment of the present disclosure, the Oxygen Transmission Rate (OTR) of a 1 mil film is ≧ 600 cm³100 square inches. In one embodiment of the present disclosure, the Oxygen Transmission Rate (OTR) of a 1 mil film is ≧ 650 cm³100 square inches. In one embodiment of the present disclosure,the Oxygen Transmission Rate (OTR) of the 1 mil film is not less than 700 cm³100 square inches. In one embodiment of the present disclosure, the Oxygen Transmission Rate (OTR) of a 1 mil film is > 740 cm³100 square inches. In one embodiment of the present disclosure, the Oxygen Transmission Rate (OTR) of a 1 mil film is ≧ 800 cm³100 square inches. In one embodiment of the present disclosure, a 1 mil film has an Oxygen Transmission Rate (OTR) of 600 to 900 cm³100 square inches. In one embodiment of the present disclosure, a 1 mil film has an Oxygen Transmission Rate (OTR) of 650 to 900 cm³100 square inches. In one embodiment of the present disclosure, a 1 mil film has an Oxygen Transmission Rate (OTR) of 700 to 900 cm³100 square inches.

In one embodiment of the present disclosure, the hot tack window Area (AHTW) of a 2 mil film is 160 Newton ∙ ℃. In one embodiment of the present disclosure, the hot tack window Area (AHTW) of a 2 mil film is 170 Newton ∙ deg.C. In one embodiment of the present disclosure, the hot tack window Area (AHTW) of a 2 mil film is 180 Newton ∙ deg.C or more. In one embodiment of the present disclosure, the hot tack window Area (AHTW) of a 2 mil film is 160 to 260 newtons ∙ ℃. In one embodiment of the present disclosure, the hot tack window Area (AHTW) of a 2 mil film is 160 to 240 newtons ∙ ℃. In one embodiment of the present disclosure, the hot tack window Area (AHTW) of a 2 mil film is 160 to 230 newtons ∙ ℃. In one embodiment of the present disclosure, the hot tack window Area (AHTW) of a 2 mil film is from 170 to 220 newtons ∙ ℃. In one embodiment of the present disclosure, the hot tack window Area (AHTW) of a 2 mil film is from 170 to 200 newtons ∙ ℃.

Some embodiments of the present disclosure provide films having improvements in Machine Direction (MD) modulus (1% and/or 2%) and seal initiation temperature relative to films formed from comparative polyethylenes. Thus, in one embodiment of the present disclosure, a film layer having a thickness of 0.5 to 10 mils has a 1% secant modulus in the Machine Direction (MD) of ≧ 180 MPa when measured at a film thickness of about 1 mil, and a Seal Initiation Temperature (SIT) of ≦ 100 ℃ when measured at a film thickness of about 2 mils. In another embodiment of the present disclosure, a film layer having a thickness of 0.5 to 10 mils has a Machine Direction (MD)1% secant modulus ≧ 190 MPa, and a Seal Initiation Temperature (SIT) of ≦ 95 ℃ when measured at a film thickness of about 2 mils. In another embodiment of the present disclosure, a film layer having a thickness of 0.5 to 10 mils has a Machine Direction (MD)1% secant modulus ≧ 200 MPa, and a Seal Initiation Temperature (SIT) of ≦ 95 ℃ when measured at a film thickness of about 2 mils.

Some embodiments of the present disclosure provide films having improvements in Machine Direction (MD) modulus (1% and/or 2%) and Oxygen Transmission Rate (OTR) relative to films formed from comparative polyethylenes. Thus, in one embodiment of the present disclosure, a film layer having a thickness of 0.5 to 10 mils has a Machine Direction (MD)1% secant modulus ≧ 190 MPa when measured at a film thickness of about 1 mil, and an Oxygen Transmission Rate (OTR) ≧ 650 cm when measured at a film thickness of about 1 mil³100 square inches.

In one embodiment of the present disclosure, films made using the polyethylene composition have good hot tack properties. Good hot tack properties are generally associated with good film properties in bag or pocket packaging lines, such as vertical-form-fill-seal (VFFS) application lines. Without wishing to be bound by theory, in the hot tack curve (sealing temperature versus force), good hot tack performance is represented by an early (or low) hot tack initiation temperature followed by a relatively high force over a wide sealing temperature range.

Some embodiments of the present disclosure provide films having improvements in Machine Direction (MD) modulus (1% and/or 2%) and hot tack window Area (AHTW) relative to films formed from comparative polyethylenes. Thus, in one embodiment of the present disclosure, a film layer having a thickness of 0.5 to 10 mils has a Machine Direction (MD)1% secant modulus ≧ 190 MPa when measured at a film thickness of about 1 mil, and a hot tack window Area (AHTW) ≧ 160 Newton ∙ ℃ when measured at a film thickness of about 2 mils.

Some embodiments of the present disclosure provide films having improved Machine Direction (MD) modulus (1% and/or 2%), oxygen transmission rate, seal initiation temperature, and hot tack window Area (AHTW) relative to films formed from comparative polyethylenes. Thus, in one embodiment of the present disclosure, when measured at a film thickness of about 1 milA film layer having a thickness of 0.5 to 10 mils has a Machine Direction (MD)1% secant modulus ≥ 190 MPa, and an Oxygen Transmission Rate (OTR) ≥ 650 cm when measured at a film thickness of about 1 mil³Per 100 square inches, Seal Initiation Temperature (SIT). ltoreq.100 ℃ when measured at a film thickness of about 2 mils, and hot tack window Area (AHTW). gtoreq.160 newtons ∙ ℃ when measured at a film thickness of about 2 mils.

In one embodiment of the present disclosure, the membrane satisfies the following relationship: hot tack Window Area (AHTW) > -2.0981 (1% secant modulus in Machine Direction (MD)) + 564.28; wherein the AHTW is measured at a film thickness of about 2 mils, and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

In one embodiment of the present disclosure, the membrane satisfies the following relationship: oxygen Transmission Rate (OTR) > -5.4297 (1% secant modulus in Machine Direction (MD)) + 1767.8; wherein the OTR is measured at a film thickness of about 1 mil, and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

In one embodiment of the present disclosure, the membrane satisfies the following relationship: seal Initiation Temperature (SIT) < 0.366 (1% secant modulus in Machine Direction (MD)) + 22.509; where SIT is measured at a film thickness of about 2 mils, and Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

In one embodiment of the present disclosure, the film satisfies each of the following relationships: i) hot tack Window Area (AHTW) > -2.0981 (1% secant modulus in Machine Direction (MD)) +564.28, wherein AHTW is measured at a film thickness of about 2 mils and 1% secant modulus in Machine Direction (MD) is measured at a film thickness of about 1 mil; ii) Oxygen Transmission Rate (OTR) > -5.4297 (machine direction (MD)1% secant modulus) + 1767.8, wherein OTR is measured at a film thickness of about 1 mil and Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil; and iii) Seal Initiation Temperature (SIT) < 0.366 (machine direction (MD)1% secant modulus) + 22.509, wherein SIT is measured at a film thickness of about 2 mils and Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

In embodiments of the present disclosure, a film layer having a thickness of 0.5 to 10 mils satisfies at least one of the following relationships: i) hot tack Window Area (AHTW) > -2.0981 (1% secant modulus in Machine Direction (MD)) +564.28, wherein AHTW is measured at a film thickness of about 2 mils and 1% secant modulus in Machine Direction (MD) is measured at a film thickness of about 1 mil; ii) Oxygen Transmission Rate (OTR) > -5.4297 (machine direction (MD)1% secant modulus) + 1767.8, wherein OTR is measured at a film thickness of about 1 mil and Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil; and iii) Seal Initiation Temperature (SIT) < 0.366 (machine direction (MD)1% secant modulus) + 22.509, wherein SIT is measured at a film thickness of about 2 mils and Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

In embodiments of the present disclosure, the film layer having a thickness of 0.5 to 10 mils satisfies each of the following relationships: i) hot tack Window Area (AHTW) > -2.0981 (1% secant modulus in Machine Direction (MD)) +564.28, wherein AHTW is measured at a film thickness of about 2 mils and 1% secant modulus in Machine Direction (MD) is measured at a film thickness of about 1 mil; ii) Oxygen Transmission Rate (OTR) > -5.4297 (machine direction (MD)1% secant modulus) + 1767.8, wherein OTR is measured at a film thickness of about 1 mil and Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil; and iii) Seal Initiation Temperature (SIT) < 0.366 (machine direction (MD)1% secant modulus) + 22.509, wherein SIT is measured at a film thickness of about 2 mils and Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

The films used in the articles described in this section may optionally contain additives and adjuvants depending on their intended use. Non-limiting examples of additives and adjuvants include antiblocking agents, antioxidants, heat stabilizers, slip agents, processing aids, antistatic additives, colorants, dyes, fillers, light stabilizers, light absorbers, lubricants, pigments, plasticizers, nucleating agents, and combinations thereof.

The following examples are given for the purpose of illustrating selected embodiments of the present disclosure; it should be understood that the embodiments provided do not limit the claims presented.

Examples

Test method

Prior to testing, each sample was conditioned at 23 + -2 deg.C and 50 + -10% relative humidity for at least 24 hours, and subsequent testing was conducted at 23 + -2 deg.C and 50 + -10% relative humidity. Herein, the term "ASTM conditions" refers to a laboratory maintained at 23 ± 2 ℃ and 50 ± 10% relative humidity; the samples to be tested were conditioned in the laboratory for at least 24 hours prior to testing. ASTM refers to the American Society for Testing and Materials.

Density was determined using ASTM D792-13 (11 months and 1 day 2013).

Melt index was determined using ASTM D1238 (8 months and 1 day 2013). Melt index I₂、I₆、I₁₀And I₂₁Measured at 190 ℃ using weights of 2.16kg, 6.48kg, 10kg and 21.6kg, respectively. Herein, the term "stress index" or its abbreviation "s.ex." is defined by the following relationship: s.ex. = log (I)₆/I₂) Log (6480/2160); wherein I₆And I₂Melt flow rates were measured at 190 ℃ using 6.48kg and 2.16kg loads, respectively.

M_n、M_wAnd M_z(g/mol) is determined by high temperature Gel Permeation Chromatography (GPC) with Differential Refractive Index (DRI) detection using a general calibration (e.g., ASTM-D6474-99). GPC data was obtained at 140 ℃ using 1,2, 4-trichlorobenzene as the mobile phase using an instrument sold under the trade name "Waters 150 c". Samples were prepared by dissolving the polymer in this solvent and run without filtration. Molecular weight is expressed as polyethylene equivalent, number average molecular weight ("M_n") had a relative standard deviation of 2.9% and a weight average molecular weight (" M_w") had a relative standard deviation of 5.0%. Molecular Weight Distribution (MWD) is the weight average molecular weight divided by the number average molecular weight, M_W/M_n. Z-average molecular weight distribution of M_z/M_n. Polymer sample solutions (1 to 2 mg/mL) were prepared by heating the polymer in 1,2, 4-Trichlorobenzene (TCB) and spinning on a wheel for 4 hours in an oven at 150 ℃. The antioxidant 2, 6-di-tert-butyl-4-methylphenol (BHT) was added to the mixture to stabilize the polymer against oxidative degradation. The BHT concentration was 250 ppm. Chromatographic analysis was performed at 140 ℃ on a PL 220 high temperature chromatography device equipped with four Shodex columns (HT803, HT804, HT805 and HT806) with Differential Refractive Index (DRI) as concentration detector using TCB as flow contrast sample solution at a flow rate of 1.0 mL/min. At a concentration of 250ppmBHT was added to the mobile phase to protect the column from oxidative degradation. The sample injection volume was 200 mL. Raw data were processed using Cirrus GPC software. The column was calibrated with narrow distribution polystyrene standards. Polystyrene molecular weight was converted to polyethylene molecular weight using the Mark-Houwink equation as described in ASTM standard test method D6474.

The short chain branching frequency (e.g., short chain branching per thousand backbone carbon atoms, or SCB/1000C) of the ethylene copolymer samples was determined by Fourier transform Infrared Spectroscopy (FTIR) according to the ASTM D6645-01 method. Measurements were made using a Thermo-Nicolet 750 Magna-IR spectrophotometer equipped with OMNIC version 7.2a software. Unsaturation in the polyethylene composition was also determined by fourier transform infrared spectroscopy (FTIR) according to astm d 3124-98.

Comonomer content as a function of molecular weight was determined using high temperature GPC (GPC-FTIR) equipped with an in-line FRIR detector.

Crystallization Elution Fractionation (CEF): polymer samples (20 to 25 mg) were weighed into sample vials and loaded on an autosampler of a Polymer CEF apparatus. The vials were filled with 6 to 7 ml of 1,2, 4-Trichlorobenzene (TCB) and heated to the desired dissolution temperature (e.g. 160 ℃) for 2 hours at a 3-step shaking rate level. The solution (0.5 ml) was then loaded onto a CEF column (two CEF columns purchased from Polymer Char and installed in series). After 5 minutes of equilibration at a given stabilization temperature (e.g., 115 ℃), the polymer solution is allowed to crystallize as the temperature is reduced from the stabilization temperature to 30 ℃. After equilibration at 30 ℃ for 10 minutes, the soluble fraction was eluted at 30 ℃ for 10 minutes, then the crystallized sample was eluted with TCB as the temperature was ramped from 30 ℃ to 110 ℃. The CEF column was cleaned at the end of the run at 150 ℃ for 5 minutes. Other CEF operating conditions were as follows: the cooling rate is 0.5 ℃/min, the crystallization flow rate is 0.02 mL/min, the heating rate is 1.0 ℃/min and the elution flow rate is 2.0 mL/min. Data was processed using Excel spreadsheets. "CDBI₅₀"is defined as the weight percent of an ethylene polymer having a composition that is within 50% of the median comonomer composition (50% on each side of the median comonomer composition). "CDBI₅₀"Can be as described in U.S. Pat. No. 5,376,439 or WO 93/03093 from the group determined by the above CEF procedureAnd (4) calculating a composition distribution curve and a normalized cumulative integral of the composition distribution curve.

The "composition distribution branching index" or "CDBI" can alternatively be determined by using a crystal-TREF apparatus commercially available from Polymer chrar (Valencia, spain). The abbreviation "TREF" refers to temperature rising elution fractionation. A sample of polyethylene composition (80 to 100 mg) was placed in the reactor of a Crystal-TREF apparatus from Polymer CHAR, the reactor was filled with 35 ml of 1,2, 4-Trichlorobenzene (TCB), heated to 150 ℃ and held at this temperature for 2 hours to dissolve the sample. An aliquot of the TCB solution (1.5 mL) was then loaded onto a Polymer CHAR TREF column packed with stainless steel beads and the column was equilibrated at 110 ℃ for 45 minutes. The polyethylene composition was then crystallized from the TCB solution in a TREF column by slowly cooling the column from 110 ℃ to 30 ℃ using a cooling rate of 0.09 ℃ per minute. The TREF column was then equilibrated at 30 ℃ for 30 minutes. The crystalline polyethylene composition was then eluted from the TREF column by passing pure TCB solvent through the column at a flow rate of 0.75 mL/min while slowly increasing the column temperature from 30 ℃ to 120 ℃ using a heating rate of 0.25 ℃ per minute. The Polymer CHAR software was used to generate a TREF profile as the polyethylene composition eluted from the TREF column, i.e. the TREF profile is a plot of the amount (or strength) of polyethylene composition eluted from the column as a function of TREF elution temperature. The CDBI can be calculated from the TREF distribution curves of each polyethylene composition analyzed₅₀。“CDBI₅₀"is defined as the weight percent of an ethylene polymer having a composition within 50% of the median comonomer composition (50% on each side of the median comonomer composition); it is calculated from the TREF composition distribution curve and the normalized cumulative integral of the TREF composition distribution curve. The skilled person will understand that a calibration curve is required to convert the TREF elution temperature into comonomer content, i.e. the amount of comonomer in the polyethylene composition fraction eluting at a specific temperature. The generation of such calibration curves is described in the prior art, for example Wild et al, j. poly. sci., Part B, poly. phys., volume 20(3), page 441-455: this document is incorporated by reference herein in its entirety. Please note that: "CDBI₂₅By "is meant a composition within 25% of the median comonomer composition (median comonomer composition)25% per side) of polyethylene composition.

Dynamic mechanical analysis was performed on compression molded samples using a rheometer (i.e., Rheometrics Dynamic Spectrometers (RDS-II) or Rheometrics SR5 or ATS Strestech) at 190 ℃ under nitrogen atmosphere using a cone plate geometry with a diameter of 25 mm. Oscillatory shear experiments were performed at frequencies from 0.05 to 100rad/s in the linear viscoelastic range of strain (10% strain). The storage modulus (G'), loss modulus (G "), complex modulus (G) and complex viscosity (η) are obtained as a function of frequency. The same rheological data can also be obtained by using a parallel plate geometry with a diameter of 25 mm at 190 ℃ under nitrogen. Using Ellis model, i.e. eta (omega) = eta₀/(1 + τ/τ_1/2)^α-1Estimating zero shear viscosity, wherein₀Is a zero shear viscosity. Tau is_1/2Is η = η₀Shear stress value at/2, and α is one of the adjustable parameters. Assume that the Cox-Merz rule applies to this disclosure.

DRI is the "dow rheology index" and is defined by the following equation:DRI = [365000(τ₀/η₀)−1]10; wherein tau is₀Is the characteristic relaxation time and η of polyethylene₀Is the zero shear viscosity of the material. The following generalized Cross equation, i.e., η (ω) = η, is used as described in U.S. Pat. No. 6,114,486₀/[1+(ωτ₀)ⁿ]Calculating the DRI by least squares fit of the rheological curve (dynamic complex viscosity versus applied frequency, e.g. 0.01-100 rads/s); where n is the power law exponent of the material and η (ω) and ω are the measured complex viscosity and applied frequency data, respectively. Zero shear viscosity η used in the determination of DRI₀Is estimated using the Ellis model instead of the Cross model.

The crossover frequency refers to the frequency at which the curves of storage modulus (G ') and loss modulus (G ") cross each other, and G' @ G" =500Pa is the storage modulus at which the loss modulus (G ") is 500 Pa.

The main melting peak (. degree. C.), melting peak temperature (. degree. C.), heat of melting (J/g) and crystallinity (%), were measured using Differential Scanning Calorimetry (DSC) as follows: firstly, calibrating an instrument by using indium; after calibration, the polymer sample was equilibrated at 0 ℃ and then the temperature was raised to 200 ℃ at a ramp rate of 10 ℃/min; then keeping the melt at 200 ℃ for 5 minutes at the same temperature; then cooling the melt to 0 ℃ at a cooling rate of 10 ℃/min and holding at 0 ℃ for 5 minutes; the sample was then heated to 200 ℃ at a heating rate of 10 ℃/min. The Tm, heat of fusion and crystallinity of the DSC were recorded from the second heating cycle.

The dart impact strength of the films was determined using ASTM D1709-09 method A (5 months and 1 day 2009). In the present disclosure, dart drop impact tests use a dart having a hemispherical head with a diameter of 1.5 inches (38 mm).

Film "ASTM puncture" refers to the energy (J/mm) required to rupture a film as determined using ASTM D5748-95 (originally adopted in 1995, re-approved in 2012). The puncture test was performed on a mechanical testing machine in which a puncture probe was attached to a load cell mounted on a moving crosshead. The membrane was clamped in a clamping mechanism having an opening of 4 inches (102 mm) in diameter. The clamping mechanism is attached to the fixed plate. The crosshead speed was set at 10 inches/min (255 mm/min). The maximum force and energy to puncture the membrane were recorded.

The "slow puncture" or "lubricated puncture" test was performed as follows: the energy (J/mm) of the membrane-piercing sample was measured using a 0.75 inch (1.9 cm) diameter pear-shaped fluorocarbon-coated probe moving at 10 inches (25.4 cm/min) per minute. ASTM conditions were used. Prior to testing the specimens, the probe tips were manually lubricated with a Muko lubricating jelly to reduce friction. Muko lubricating jelly is a water-soluble personal lubricant available from Cardinal Health Inc., 1000 Tesma Way, Vaughan, ON L4K 5R8 Canada. The probe was mounted on an Instron model 5 SL universal tester and a 1000-N load cell was used. Film samples (1.0 mil (25 μm) thick, 5.5 inches (14 cm) wide, 6 inches (15 cm) long) were mounted in an Instron and punctured. The following film tensile properties were determined using ASTM D882-12 (8/1/2012): tensile breaking strength (MPa), elongation at break (%), tensile yield strength (MPa), tensile elongation at yield (%), and film toughness or total energy to break (ft. lb/in)³). The blown films were tested for tensile properties in the Machine Direction (MD) and Transverse Direction (TD).

Secant modulus is a measure of the stiffness of a film. Secant modulus is the slope of a line drawn between two points on the stress-strain curve, i.e., the secant line. The first point on the stress-strain curve is the origin, i.e., the point corresponding to the origin (point of 0% strain and zero stress), and; the second point on the stress-strain curve is the point corresponding to 1% strain; given these two points, the 1% secant modulus was calculated and expressed as force per unit area (MPa). Similar calculation of 2% secant modulus. Since the stress-strain relationship of polyethylene does not follow Hooke's Law, i.e., the stress-strain behavior of polyethylene is non-linear due to its viscoelastic properties, the film modulus was calculated using this method. Secant modulus was measured using a conventional Instron tensile tester equipped with a 200 pound force load cell. Strips of monolayer film samples having the following dimensions were cut for testing: 14 inches long, 1 inch wide and 1 mil thick; ensure that the edges of the sample are not scored or notched. Film samples were cut in the Machine Direction (MD) and Transverse Direction (TD) and tested. The samples were adapted using ASTM conditions. The thickness of each film was accurately measured with a hand-held micrometer and entered into the Instron software along with the sample name. The sample was loaded in an Instron with a jaw spacing of 10 inches and pulled at a rate of 1 inch/minute to generate a strain-strain curve. The 1% and 2% secant moduli were calculated using Instron software.

The Oxygen Transmission Rate (OTR) of the blown film was tested using an Oxtran 2/20 instrument manufactured by MOCON Inc, Minneapolis, Minnesota, USA. The instrument has two test chambers (a and B) and each membrane sample is analyzed in duplicate. The reported OTR results are the average of the results from the two test chambers (a and B). The test was carried out at a temperature of 23 ℃ and a relative humidity of 0%. The area of the film sample used for the test was 100cm². The carrier gas used was 2% hydrogen balanced with nitrogen and the test gas was ultra high purity oxygen. The blown films tested were all 1 mil thick.

The puncture-extension tear resistance of the blown film was measured using ASTM D2582-09 (5 months and 1 day 2009). This test measures the resistance of the blown film to snagging, or more precisely to dynamic puncture leading to tearing and the propagation of this puncture. Puncture-propagation tear resistance was measured in the Machine Direction (MD) and the Transverse Direction (TD) of the blown film.

Film tear properties were determined by ASTM D1922-09 (5 months and 1 day 2009); the equivalent term for tear is "Elmendorf tear". Film tear was measured in the Machine Direction (MD) and Transverse Direction (TD) of the blown film.

The optical properties of the films were measured as follows: haze, ASTM D1003-13 (11 months and 15 days 2013), and; gloss ASTM D2457-13 (4 months and 1 day 2013).

In the present disclosure, the "hot tack test" is performed using ASTM conditions as follows. Hot Tack data used was J available from Jbi Hot Tack, Geloeslaan 30, B-3630 Maamechelen, Belgium&B, hot bonding test machine generation. In the hot tack test, the strength of the polyolefin to polyolefin seal is measured immediately after heat sealing two film samples together cut from the same roll of 2.0 mil (51 μm) thick film, i.e., when the polyolefin macromolecules that make up the film are in a semi-molten state. This test simulates the heat sealing of polyethylene films on high speed automatic packaging machines such as vertical or horizontal form-fill-seal equipment. At J&The following parameters were used in the hot tack test B: film sample width, 1 inch (25.4 mm); film sealing time, 0.5 seconds; film sealing pressure, 0.27N/mm²(ii) a Delay time, 0.5 seconds; film peel speed, 7.9 inches/second (200 mm/second); test temperature range, 131 ° F to 293 ° F (55 ℃ to 145 ℃); temperature increase, 9 ° f (5 ℃); and five film samples were tested at each temperature increment to calculate the average value at each temperature. In this way, a hot tack curve of the drawing force versus the sealing temperature is generated. From this hot tack curve the following data can be calculated: "sticking onset @ 1.0N (. degree. C.)" is the temperature at which a thermal tack of 1N is observed (average of five film samples); "maximum hot tack strength (N)" is the maximum hot tack force (average of five film samples) observed over the test temperature range; "temperature-maximum hot tack (. degree. C.)" is the temperature at which maximum hot tack is observed. Finally, the hot tack (strength) window area ("hot tack window area" or "AHTW") is an estimate of the area under the hot tack curve from the hot tack initiation temperature to the temperature of the sample immediately before melting. The latter temperature before melting of the sample is typically 130 c, but not necessarily 130 c. Piecewise regression (linear or polynomial regression) was performed on different segments of the hot tack curve,to obtain a mathematical relationship between sealing temperature and drawing force. The area of that portion of each temperature-force segment is then calculated. The total Area (AHTW) is the sum of the partial areas of each segment of the hot tack curve within the specified range (i.e., from the hot tack initiation temperature to the temperature of the sample immediately prior to melting).

In the present disclosure, the "heat seal strength test" (also referred to as "cold seal test") is performed as follows. ASTM conditions were used. Heat seal data was generated using a conventional Instron tensile tester. In this test, two film samples (both cut from the same roll of 2.0 mil (51 μm) thick film) were sealed over a range of temperatures. The following parameters were used in the heat seal strength (or cold seal) test: film sample width, 1 inch (25.4 mm); film sealing time, 0.5 seconds; membrane seal pressure, 40 psi (0.28N/mm)²) (ii) a Temperature range: 212 DEG F to 302 DEG F (100 ℃ to 150 ℃) and a temperature increase of 9 DEG F (5 ℃). After aging for at least 24 hours under ASTM conditions, seal strength was determined using the following tensile parameters: drawing (cross head) speed, 12 inches/minute (2.54 cm/min); the drawing direction is 90 degrees from the sealing direction; 5 film samples were tested at each temperature increment. The seal initiation temperature (hereinafter referred to as s.i.t.) is defined as the temperature required to form a commercially available seal; the seal strength of the commercially available seal was 2.0 lb/in seal (8.8N/25.4 mm seal).

Determining the hexane extractables content of the polymer samples according to Code of Federal Registration 21 CFR § 177.1520 para (c)3.1 and 3.2; wherein the amount of hexane extractables in the membrane is determined gravimetrically. In detail, 2.5 grams of a 3.5 mil (89 μm) single layer film was placed in a stainless steel basket, and the film and basket were weighed (w)ⁱ) While extracting the membrane with n-hexane in a basket at 49.5 ℃ for 2 hours; drying in a vacuum oven at 80 ℃ for 2 hours; cooling in a desiccator for 30 minutes; and weighed (w)^f). Percent weight loss is the percent hexane extractables (w)^C6)：(w^C6): w^C6 = 100 x (wⁱ-w^f)/wⁱ。

Polyethylene composition

The polyethylene composition comprising the first, second and third polyethylenes is prepared by melt blending polyethylene composition a and polyethylene B.

Polyethylene composition a was prepared in a dual parallel reactor solution polymerization process using two different single-site catalysts. As a result, polyethylene composition a comprises a first polyethylene made with a first single-site catalyst (metallocene) and a second polyethylene made with a second single-site catalyst (phosphinimine catalyst). A parallel mode solution phase polymerization reactor process is described in U.S. patent application 15/491,264 (co-pending with the present application). Essentially, in parallel mode, the exit streams from each of the first reactor (R1) and the second reactor (R2) are combined downstream of each reactor and a polymer product is obtained after devolatilization.

The following example illustrates the continuous solution copolymerization of ethylene and 1-octene at medium pressure in a parallel two reactor system. The first and second reactor pressures were about 16000 kPa (about 2.3X 10)³psi). The first reactor is operated at a lower temperature than the second reactor. The volume of the first reactor was 12 litres and the volume of the second reactor was 24 litres. Both reactors were agitated to ensure good mixing of the reactor contents. The process is continuous in all feed streams (i.e., solvent, which is methylpentane and xylene; monomer and catalyst and co-catalyst components) and product removal. The monomer (ethylene) and comonomer (1-octene) are purified prior to addition to the reactor using conventional feed preparation systems, such as contact with various absorption media to remove impurities such as water, oxygen, and polar contaminants. The reactor feed was pumped into the reactor at the ratio shown in table 1. The average residence time of the reactor was calculated by dividing the average flow rate by the reactor volume. For all experiments of the invention, the residence time in each reactor was less than 10 minutes and the reactors were well mixed. The catalyst deactivator used is octanoic acid (caprylic acid), which can be recovered from P&G Chemicals, Cincinnati, OH, u.s.a.

The following Single Site Catalyst (SSC) components were used in the preparation of the first polyethylene in a first reactor (R1) configured in parallel with a second reactor (R2): diphenylmethylene (cyclopentadienyl) (2, 7-di-tert-butyl)Butylfluorenyl) hafnium dimethyl [ (2, 7-tBu)₂Flu)Ph₂C(Cp)HfMe₂](ii) a Methylaluminoxane (MMAO-07); triphenylmethylium tetrakis (pentafluorophenyl) borate (triphenylmethylium borate), and 2, 6-di-tert-butyl-4-ethylphenol (BHEB). Methylalumoxane (MMAO-07) and 2, 6-di-tert-butyl-4-ethylphenol were premixed in-line and then combined with diphenylmethylene (cyclopentadienyl) (2, 7-di-tert-butylfluorenyl) hafnium dimethyl and triphenylmethylium tetrakis (pentafluorophenyl) borate just prior to entering the polymerization reactor (R1).

The following Single Site Catalyst (SSC) components were used to prepare the first polyethylene in a second reactor (R2) configured in parallel with the first reactor (R1): cyclopentadienyl tris (tert-butyl) phosphinimine titanium dichloride [ Cp ((t-Bu)₃PN)TiCl₂](ii) a Methylaluminoxane (MMAO-07); triphenylmethylium tetrakis (pentafluorophenyl) borate (triphenylmethylium borate), and 2, 6-di-tert-butyl-4-ethylphenol (BHEB). Methylaluminoxane (MMAO-07) and 2, 6-di-tert-butyl-4-ethylphenol were premixed in-line and then with cyclopentadienyl tris (tert-butyl) phosphinimine titanium dichloride [ Cp ((t-Bu) ]just before entering the polymerization reactor (R2)₃PN)TiCl₂]And triphenylmethylium tetrakis (pentafluorophenyl) borate.

Polyethylene C, on the other hand, was prepared in a single solution polymerization reactor using a ziegler-natta catalyst as described below; however, in this example, the in-line formed ziegler-natta catalyst was fed only to the first reactor (R1) to produce polyethylene C in a single reactor. For clarity, polyethylene C becomes the third polyethylene in the final polyethylene composition. The following ziegler-natta (ZN) catalyst component was used to prepare the third polyethylene: butyl ethyl magnesium; tert-butyl chloride; titanium tetrachloride; diethyl aluminum ethoxide; and triethylaluminum. An in-line ziegler-natta catalyst formulation was prepared using methylpentane as the catalyst component solvent and the following procedure. In step one, a solution of triethylaluminum and butylethylmagnesium (Mg: Al = 20, mol: mol) is combined with a solution of tert-butyl chloride and allowed to react for about 30 seconds to form MgCl₂And (3) a carrier. In step two, a titanium tetrachloride solution is added to the mixture formed in step oneAnd allowed to react for about 14 seconds and then injected into the reactor (R1). The in-line ziegler-natta catalyst was activated in the reactor by injecting a solution of diethylaluminium ethoxide into R1. The amount of titanium tetrachloride added to the reactor is shown in table 1. The efficiency of the in-line ziegler-natta catalyst formulation is optimized by adjusting the molar ratio of the catalyst components.

Table 1 shows the reactor conditions for producing polyethylene composition a as well as polyethylene B. The properties of polyethylene composition a and polyethylene B are shown in table 2.

TABLE 1

Reactor operating conditions

TABLE 2

Properties of the blend Components

The properties of two different polyethylene compositions obtained from melt blending polyethylene composition a and polyethylene B at two different weight fractions are provided in table 3 as examples 1 and 2 of the invention. The materials were melt blended using a Coperion ZSK 26 co-rotating twin screw extruder with an L/D of 32: 1. The extruder was equipped with an underwater pelletizer and a Gala rotary dryer. Materials were co-fed to the extruder using a gravimetric feeder to achieve the desired ratio of polyethylene composition a to polyethylene B. The blend was compounded using a screw speed of 200 rpm at an output rate of 15-20 kg/h and a melting temperature of 225-230 ℃.

Table 3 also includes data for comparative polyethylene compositions, comparative examples 1-9. Comparative example 1 is ELITE^®5400G, a resin commercially available from the Dow Chemical Company. ELITE 5400G had a density of about 0.916G/cm³Melt index I₂Is about 1 dg/min. Comparative example 2 is SURPASS^®FP117-C, a resin available from NOVA Chemicals Corporation. The density of SURPASS FP117-C is0.917 g/cm³Melt index I₂Is 1 dg/min. Comparative examples 3 and 4 are resins prepared according to U.S. patent application publication No. 2016/0108221. Comparative example 3 is an ethylene/1-octene copolymer having a density of about 0.917 g/cm³Melt index I₂About 0.96 dg/min and is prepared in a multiple reactor solution process in which a first reactor and a second reactor are configured in series with each other. Comparative example 4 is an ethylene/1-octene copolymer having a density of about 0.913 g/cm³Melt index I₂About 0.85 dg/min and is prepared in a multiple reactor solution process in which a first reactor and a second reactor are configured in series with each other. Comparative example 5 is SCLAIR^®FP112-A, a resin available from NOVA Chemicals Corporation. SCLAIR FP112-A density of 0.912 g/cm³Melt index I₂It was 0.9 dg/min. Comparative example 6 is EXCEED^®1018CA, a resin commercially available from ExxonMobil. EXCEED 1018CA has a density of about 0.918 g/cm³Melt index I₂Is about 0.94 dg/min. Comparative example 7 is MARLEX^®D139, a resin available from chevron phillips. The density of MARLEX D139 was about 0.918 g/cm³Melt index I₂Is about 0.9 dg/min. Comparative example 8 is SCLAIR^®FP120-A, a resin available from NOVA Chemicals Corporation. FP120-A has a density of 0.920 g/cm³Melt index I₂Is 1 dg/min. Comparative example 9 is SCLAIR^®FP026-F, a resin available from NOVA Chemicals Corporation. The density of FP026-F is 0.926 g/cm³Melt index I₂Is 0.75 dg/min.

TABLE 3

Polyethylene composition Properties

TABLE 3 continuation

Polyethylene composition Properties

The polyethylene composition of the invention comprises: details of the first polyethylene, the second polyethylene, and the third polyethylene are provided in table 4. In addition to the weight percentages w1 and w2 (obtained by adjusting the deconvolution values w1 'and w2', as discussed further below), the data in table 4 includes the mathematical deconvolution component properties of polyethylene composition a (which includes a first polyethylene made with a single-site metallocene catalyst and a second polyethylene made with a single-site phosphinimine catalyst) and the experimentally measured properties of polyethylene B (a third polyethylene made with a ziegler-natta catalyst).

Comonomer content as a function of molecular weight was determined using high temperature GPC (GPC-FTIR) equipped with an in-line FTIR detector. To deconvolute polyethylene composition a, which was produced in parallel mode polymerization using SSC in R1 and R2, into components, a mathematical deconvolution model described in U.S. patent No. 8,022,143 was used. As described in U.S. Pat. No. 8,022,143, a single Schultz Flory distribution was used (assuming Mw/Mn of 2; Mn of Mw/2 and Mz of 1.5 XM)_W) GPC and GPC-FTIR data, the molecular weight distribution of the first polyethylene (SSC component made in R1, considered a catalyst site) and the second polyethylene (SSC component made in R2, considered a catalyst site) were modeled. To improve deconvolution accuracy and consistency, as a constraint, the melt index I of the modeled composition (i.e., the dual reactor polyethylene composition A) was set₂And during deconvolution the following relationship is satisfied:

Log₁₀(I₂) = 22.326528 + 0.003467*[Log₁₀(M_n)]³ - 4.322582*Log₁₀(M_w) - 0.180061*[Log₁₀(M_z)]²+ 0.026478*[Log₁₀(M_z)]³

wherein the overall melt index (i.e. the melt index of polyethylene composition a) I, measured experimentally, is used to the left of the equation₂. Thus, a total of two centres (one for each SSC) were used to deconvolute the polyethylene composition a. W (i) and Mn (i), i =1 to 2, are obtained with each centerM of (A)_w(i) And Mz (i) calculated using the Mn (i) for each center using the relationship described above. Bulk M of polyethylene composition A during deconvolution_n、M_wAnd M_zCalculated using the following relationship: m_n = 1/Sum(w_i/M_n(i)), M_w= Sum(w_i×M_w(i)), M_z = Sum(w_i×M_z(i)²) Wherein i represents the ith component and w_iRepresents the relative weight fraction of the ith component in the composition from the 2-center deconvolution described above. The GPC-FTIR chromatogram was then deconvoluted using the w (i) results to give scb (i), i =1 to 2.

Then, the Mn (i), M of each catalyst center in the above relationship are used_w(i) Mz (i), SCB (i) data Mn, M for first and second polyethylenes prepared in SSC in each of R1 and R2_wMz and SCB/1000C.

When the polymer prepared with the single-site catalyst in R2 was an ethylene homopolymer, as was the case in the examples of this application, the SCB/1000C of the modeled SSC sites was set to zero during the deconvolution analysis. However, if the polymer prepared with the SSC is a copolymer, then the SCB value for the center of the SSC will be determined using the deconvolution model given above.

To calculate the melt index I of each of the first and second polyethylenes in polyethylene composition A₂Using the following melt index I₂Model:

Log₁₀(melt index, I)₂)= 22.326528 + 0.003467*[Log₁₀(M_n)]³ - 4.322582*Log₁₀(M_w)- 0.180061*[Log₁₀(M_z)]² + 0.026478*[Log₁₀(M_z)]³

Wherein Mn and M_wAnd Mz is the deconvolution value of the first or second polyethylene component present in polyethylene composition a, as obtained from the GPC deconvolution results described above.

The density of the first polyethylene, which is an ethylene copolymer made using a single-site catalyst in R1, was calculated using the following density model:

density of the first polyethylene made with SSC = 0.979863-0.00594808 (FTIR SCB/1000C)^0.65 – 0.000383133*[Log₁₀(M_n)]³– 0.00000577986*(M_w/M_n)³+0.00557395*(M_z/M_w)^0.25

Wherein M is_n、M_wAnd M_zIs the deconvoluted value of the first polyethylene from the result of the GPC deconvolution described above, SCB/1000C was obtained by GPC-FTIR deconvolution. The density of the second polyethylene, which is an ethylene homopolymer made with a single-site catalyst in R2, was determined using the same equation used above to find the density of the first polyethylene, but with the short chain branching set to a value of zero to offset the corresponding term:

density of second polyethylene made with SSC = 0.979863-0.000383133 [ Log [ ]₁₀(M_n)]³ –0.00000577986*(M_w/M_n)³+0.00557395*(M_z/M_w)^0.25。

Deconvolution provided the densities (d1 and d2), melt indices (I) of the first and second polyethylenes₂ ¹And I₂ ²) Short chain branches (SCB1, and SCB2 set to zero for ethylene homopolymer), weight and number average molecular weights (Mw1, Mn1, Mw2, and Mn2), and weight fractions (w1 'and w 2'). The resulting deconvolution properties as well as the relative weight percentages w1, w2 (which were ascertained by varying the deconvolved weight fractions w1 'and w2' for the first and second polyethylenes, respectively, to match the amount of polyethylene composition a in the final melt blended polyethylene composition, as determined by the blending rules discussed further below) are provided in table 4.

The following basic blending rules are used to obtain the desired polyethylene composition comprising the first, second and third polyethylenes:

w1 = weight percent of the first polyethylene in the final polyethylene composition;

w2 = weight percent of the second polyethylene in the final polyethylene composition;

w3 = weight percent of the third polyethylene in the final polyethylene composition;

w1 = weight percent of polyethylene composition a in the molten blend;

w2 = weight percent of polyethylene B in the molten blend;

w1 '= weight percent of the first polyethylene in polyethylene composition a (i.e. w1' as determined by mathematical deconvolution of polyethylene composition a);

w2 '= weight percentage of second polyethylene in polyethylene composition a (i.e. w2' as determined by mathematical deconvolution of polyethylene composition a);

wherein the content of the first and second substances,

w1 + w2 + w3 = 1;

w1 + w2 =1, and

w1’ + w2’ = 1;

so that

w1 = w1* × w1’;

w2 = w1 × w 2'; and

w3 = w2*。

TABLE 4

Properties of polyethylene composition Components

Referring to fig. 1, one skilled in the art will recognize that the polyethylene composition of the present invention has a monomodal GPC curve.

Referring to fig. 2, one skilled in the art will recognize that the inventive polyethylene composition has a partial reverse comonomer incorporation, wherein comonomer incorporation first increases with increasing molecular weight and then decreases with further increasing molecular weight.

Referring to fig. 3, one skilled in the art will recognize that the inventive polyethylene compositions each exhibit a melting peak above 125 ℃. For inventive example 1, the DSC curve was monomodal. For inventive example 2, the DSC curve was bimodal.

The data in table 3 clearly show that the inventive polyethylene composition has a significant amount of material eluting at lower temperatures in the Crystallization Elution Fraction (CEF) analysis compared to each of the comparative resins. Inventive examples 1 and 2 each had a soluble fraction of greater than 10% by weight in the Crystallization Elution Fractionation (CEF) analysis (30.3% by weight for inventive example 1 and 19.4% by weight for inventive example 2), while all comparative examples 1-9 had a soluble fraction of less than 10% by weight in the Crystallization Elution Fractionation (CEF) analysis (i.e., a fraction eluting at 30 ℃ or less).

Blown film was produced by using a 2.5 inch Gloucester blown film line (L/D =24) with a 4 inch diameter die. The Polymer Processing Aid (PPA) was coated on the die by adding a high concentration of PPA masterbatch in the line to avoid melt fracture. The set conditions were a die gap of 35 mils (0.0889 cm), a frost line height of about 17 inches, and a throughput of 100 pounds per hour. The films were collected under different orientation conditions. A 1 mil monolayer film was produced at a blow-up ratio (BUR) of 2.5 and the physical properties of the film were obtained with the 1 mil film. A 2 mil monolayer film (BUR =2.5) was used to obtain cold seal and hot tack curves. Table 5 provides data from blown films of the polyethylene compositions of the present disclosure, as well as data from films made from various comparative resins.

Comparative example 1 is prepared from ELITE^®5400G film, ELITE^®5400G is a resin commercially available from the Dow Chemical Company. The density of ELITE 5400G was about 0.916G/cm³Melt index I₂About 1 dg/min. Comparative example 2 is a composition prepared from SURPASS^®Membrane made of FP117-C, SURPASS^®FP117-C resin is a resin commercially available from NOVA Chemicals Corporation. The density of SURPASS FP117-C is 0.917 g/cm³Melt index I₂Is 1 dg/min. Comparative examples 3 and 4 are films made from resins prepared according to U.S. patent application publication No. 2016/0108221. Comparative example 3 is a film made from an ethylene/1-octene copolymer having a density of about 0.917 g/cm³Melt index I₂About 0.96 dg/min and is prepared in a multiple reactor solution process in which a first reactor and a second reactor are configured in series with each other. Comparative example 4 is a film made of an ethylene/1-octene copolymer having a density of about 0.913 g/cm³Melt index I₂About 0.85 dg/min, and it is prepared in a multiple reactor solution process, wherein a first reactor and a second reactor are configured in series with each other. Comparative example 5 is a composition prepared from SCLAIR^®FP112-A membrane, SCLAIR^®FP112-A is a resin available from NOVA Chemicals Corporation. SCLAIR FP112-A density of 0.912 g/cm³Melt index I₂It was 0.9 dg/min. Comparative example 6 is a test run from EXCEED^®1018CA, EXCEED^®1018CA is a resin available from ExxonMobil. The density of EXCEED 1018CA is about 0.918 g/cm³Melt index I₂About 0.94 dg/min. Comparative example 7 is a compound prepared from MARLEX^®D139 film, MARLEX^®D139 is a resin commercially available from chevron phillips. The density of MARLEX D139 was about 0.918 g/cm³Melt index I₂About 0.9 dg/min. Comparative example 8 is a composition prepared from SCLAIR^®FP120-A membrane, SCLAIR^®FP120-A is a resin available from NOVA Chemicals Corporation. FP120-A has a density of 0.920 g/cm³Melt index I₂Is 1 dg/min. Comparative example 9 is a composition prepared from SCLAIR^®FP026-F membrane, SCLAIR^®FP026-F is a resin commercially available from NOVA Chemicals Corporation. The density of FP026-F is 0.926 g/cm³Melt index I₂Is 0.75 dg/min. In table 5 inventive examples 1 and 2 are films made from inventive polyethylene compositions of inventive examples 1 and 2.

TABLE 5

Film Properties

TABLE 5 continuation

Film Properties

TABLE 5 continuation

Film Properties

The data provided in table 5, together with the data in fig. 4-8, demonstrate that the inventive polyethylene composition can be made into films with a good balance of film properties, including good stiffness, good oxygen transmission rate, and good sealing performance. For example, referring to fig. 4-8, films made from the inventive polyethylene composition have good hot tack and cold seal properties.

Without wishing to be bound by theory, in the hot tack (or cold seal) curve (sealing temperature versus sealing force), good hot tack (or cold seal) performance is indicated by an early (or low) hot tack (or cold seal) onset temperature followed by a relatively high sealing force over a wide hot tack sealing temperature range. See, for example, the shape of the curves in fig. 4 and 5 for inventive examples 1 and 2 versus comparative examples 1-7. The hot tack curves of inventive examples 1 and 2 are particularly well shaped and combine an early hot tack seal initiation temperature and a high sealing force over a wide hot tack seal temperature range. To provide a more quantitative measure of this improved hot tack seal performance, a new parameter "hot tack (strength) window area" ("hot tack window area" or "AHTW") is defined herein. The AHTW is simply an estimate of the area under the hot tack curve from the hot tack initiation temperature to the temperature of the sample immediately before melting. As shown in fig. 4, the temperature before the sample melts is typically 130 ℃, but not necessarily 130 ℃. As shown in Table 5 and FIG. 4, the AHTW of inventive examples 1 and 2 were each greater than 160 newtons ∙ deg.C, while the AHTW of each of comparative examples 1-7 was less than 160 newtons ∙ deg.C.

The curves given in fig. 5 demonstrate the good cold seal performance of inventive examples 1 and 2. For comparison, FIG. 5 also shows the cold seal performance of comparative examples 1-7. Those skilled in the art will recognize from fig. 5 that inventive examples 1 and 2 each combine an early cold seal initiation temperature with a relatively high sealing force over a wide cold seal temperature range. In contrast, comparative examples 1-7 had a late cold seal initiation temperature and a narrow cold seal temperature range, in which relatively high sealing forces occurred.

Figure 6 shows that inventive examples 1 and 2 have a better balance of AHTW and stiffness (as determined by Machine Direction (MD) secant modulus at 1% strain) than comparative examples 2-9. Indeed, fig. 6 depicts a plot of the value of AHTW (in newtons ∙ ℃) (y-axis) versus the value of Machine Direction (MD) secant modulus at 1% strain (in MPa) (x-axis), and a plot of the equation AHTW = -2.0981 (machine direction (MD)1% secant modulus) +564.28, indicating that inventive examples 1 and 2 satisfy the following conditions: AHTW > -2.0981 (1% secant modulus in Machine Direction (MD)) +564.28, whereas comparative examples 2-9 did not.

Figure 7 shows that inventive examples 1 and 2 have a better balance of SIT and stiffness (determined by Machine Direction (MD) secant modulus at 1% strain) than comparative examples 2-9. Fig. 7 depicts a graph of SIT (in degrees c) value (y-axis) versus Machine Direction (MD) secant modulus (in MPa) value (x-axis) at 1% strain, and a graph of equation SIT = 0.366 (machine direction (MD)1% secant modulus) + 22.509, indicating that inventive examples 1 and 2 satisfy the following conditions: SIT < 0.366 (1% secant modulus in Machine Direction (MD)) + 22.509, whereas comparative examples 2-9 were not satisfied.

Figure 8 shows that inventive examples 1 and 2 have a better balance of OTR and stiffness (as determined by Machine Direction (MD) secant modulus at 1% strain) than comparative examples 2-9. FIG. 8 depicts OTR (in cm)³A plot of the/100 square inch) value (y-axis) against the Machine Direction (MD) secant modulus at 1% strain (in MPa) value (x-axis), and a plot of the equation OTR = -5.4297 (machine direction (MD)1% secant modulus) + 1767.8, show that inventive examples 1 and 2 satisfy the following conditions: OTR > -5.4297 (1% secant modulus in Machine Direction (MD) + 1767.8, whereas comparative examples 2-9 did not.

Non-limiting embodiments of the present disclosure include the following:

embodiment a. a polyethylene composition comprising:

5 to 80% by weight of a second polyethylene which is an ethylene copolymer or an ethylene homopolymer, of the second polyethyleneWeight average molecular weight M_w15,000 to 100,000, molecular weight distribution M_w/M_n< 2.3 and having 0 to 20 short chain branches per thousand carbon atoms; and

The polyethylene composition of embodiment a, wherein the polyethylene composition has a monomodal distribution in Gel Permeation Chromatography (GPC).

Embodiment c. the polyethylene composition of embodiment a or B, wherein the polyethylene composition has a solubility fraction in a Crystallization Elution Fraction (CEF) analysis of at least 15 wt%.

The polyethylene composition of embodiment A, B or C, wherein the polyethylene composition has a melting peak temperature in Differential Scanning Calorimetry (DSC) analysis at greater than 125 ℃.

The polyethylene composition of embodiment A, B, C or D, wherein the first polyethylene has 30 to 75 short chain branches per thousand carbon atoms.

The polyethylene composition of embodiment f. embodiment A, B, C, D or E, wherein the second polyethylene is an ethylene homopolymer.

The polyethylene composition of embodiment g, embodiment A, B, C, D, E or F, wherein the third polyethylene is an ethylene copolymer and has 5 to 30 short chain branches per thousand carbon atoms.

The polyethylene composition of embodiment h, embodiment A, B, C, D, E, F or G, wherein the first polyethylene has a weight average molecular weight M_wFrom 75,000 to 200,000.

The polyethylene composition of embodiment i, embodiment A, B, C, D, E, F, G or H, wherein the second polyethylene has a weight average molecular weight M_wFrom 25,000 to 75,000.

The polyethylene composition of embodiment A, B, C, D, E, F, G, H or I, wherein the third polyethylene has a weight average molecular weight M_wIs 80,000 to 200,000.

The polyethylene composition of embodiment k, embodiment A, B, C, D, E, F, G, H, I or J, wherein the first polyethylene has a density from 0.855 to 0.910 g/cm³。

The polyethylene composition of embodiment l. embodiment A, B, C, D, E, F, G, H, I, J or K, wherein the second polyethylene is of a density from 0.940 to 0.980 g/cm³The ethylene homopolymer of (1).

Embodiment m. the polyethylene composition of embodiment A, B, C, D, E, F, G, H, I, J, K or L, wherein the third polyethylene is a polyethylene having a density of from 0.880 to 0.936 g/cm³The ethylene copolymer of (1).

The polyethylene composition of embodiment n. A, B, C, D, E, F, G, H, I, J, K, L or M, wherein the first polyethylene is present from 5 to 50 weight percent.

The polyethylene composition of embodiment A, B, C, D, E, F, G, H, I, J, K, L, M or N, wherein the second polyethylene is present from 5 to 60 weight percent.

The polyethylene composition of embodiment p. embodiment A, B, C, D, E, F, G, H, I, J, K, L, M, N or O, wherein the third polyethylene is present from 15 to 85 weight percent.

The polyethylene composition of embodiment A, B, C, D, E, F, G, H, I, J, K, L or M, wherein the first polyethylene is present from 10 to 40 weight percent.

The polyethylene composition of embodiment r. embodiment A, B, C, D, E, F, G, H, I, J, K, L, M or Q, wherein the second polyethylene is present from 15 to 45 weight percent.

The polyethylene composition of embodiment s. A, B, C, D, E, F, G, H, I, J, K, L, M, Q or R, wherein the third polyethylene is present from 20 to 80 weight percent.

The polyethylene composition of embodiment t, embodiment A, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R or S, wherein the CDBI of the first polyethylene₅₀At least 75 wt%.

Embodiment u. embodiment A, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S or T wherein the third polyethylene is CDBI₅₀Less than 75wt% of a copolymer.

The polyethylene composition of embodiment v. embodiment A, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T or U, wherein the first polyethylene is a homogeneously branched ethylene copolymer.

The polyethylene composition of embodiment A, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U or V, wherein the third ethylene polymer is a heterogeneously branched ethylene copolymer.

The polyethylene composition of embodiment A, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V or W, wherein the first polyethylene is produced with a single-site catalyst.

The polyethylene composition of embodiment A, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W or X, wherein the second polyethylene is produced with a single-site catalyst.

The polyethylene composition of embodiment z, embodiment A, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W, X or Y, wherein the third polyethylene is produced with a ziegler-natta catalyst.

The polyethylene composition of embodiment A, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W, X, Y or Z, wherein the polyethylene composition has a molecular weight distribution, M, of_w/M_nIs 2.1 to 5.5.

The polyethylene composition of embodiment BB. embodiment A, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W, X, Y or Z, wherein the polyethylene composition has a molecular weight distribution, M_w/M_nIs 2.1 to 4.5.

The polyethylene composition of embodiment cc, embodiment A, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W, X, Y, Z, AA or BB, wherein the polyethylene composition has a density < 0.935 g/cm³。

The polyethylene composition of embodiment DD. embodiment A, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W, X, Y, Z, AA or BB wherein the polyethylene composition has a density of from 0.880 to 0.932g/cm³。

Embodiment ee, embodiment a, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W, X, Y, Z, AA, BB, CC, or DD, wherein the polyethylene composition has a melt index I, I₂Is 0.1 to 3.0 dg/min.

Embodiment FF. polyethylene composition of embodiments a, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W, X, Y, Z, AA, BB, CC, DD, or EE, wherein the M of the polyethylene composition_Z/M_wLess than 3.00.

Embodiment GG. embodiment A, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W,X, Y, Z, AA, BB, CC, DD, EE or FF, wherein the polyethylene composition has a melt index ratio I₂₁/I₂From 20 to 40.

Embodiment HH. film layer having a thickness of 0.5 to 10 mils comprising the polyethylene composition of embodiment a, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W, X, Y, Z, AA, BB, CC, DD, EE, FF, or GG.

The film layer of embodiment HH, wherein the film layer has a 1% secant modulus in the Machine Direction (MD) of 190 MPa or greater when measured at a film thickness of about 1 mil.

The film layer of embodiment HH or II wherein the film layer has a Seal Initiation Temperature (SIT) ≦ 100 ℃ when measured at a film thickness of about 2 mils.

Embodiment KK. the film layer of embodiment HH, II, or JJ, wherein the film layer has a hot tack window Area (AHTW) of greater than or equal to 160 Newton ∙ C when measured at a film thickness of about 2 mils.

Embodiment LL. film layer of embodiment HH, II, JJ, or KK, wherein the film layer has an Oxygen Transmission Rate (OTR) of 650 cm or greater when measured at a film thickness of about 1 mil³100 square inches.

Embodiment MM. the film layer of embodiment HH wherein the film layer has a Machine Direction (MD)1% secant modulus ≥ 190 MPa when measured at a film thickness of about 1 mil, a Seal Initiation Temperature (SIT) ≤ 100 ℃ when measured at a film thickness of about 2 mils, a hot tack window Area (AHTW) ≥ 160 Newton ∙ ℃ when measured at a film thickness of about 2 mils, and an Oxygen Transmission Rate (OTR) ≥ 650 cm when measured at a film thickness of about 1 mil³100 square inches.

Embodiment NN. film layer having a thickness of 0.5 to 10 mils, wherein the film layer has a 1% secant modulus in the Machine Direction (MD) of greater than or equal to 190 MPa when measured at a film thickness of about 1 mil and a Seal Initiation Temperature (SIT) of less than or equal to 100 ℃ when measured at a film thickness of about 2 mils.

Embodiment OO. film layer having a thickness of 0.5 to 10 mils, wherein the film layer has a 1% secant modulus in the Machine Direction (MD) of 190 MPa or greater when measured at a film thickness of about 1 mil and a hot tack window Area (AHTW) of 160 Newton ∙ ℃ or greater when measured at a film thickness of about 2 mils.

Embodiment PP. film layer having a thickness of 0.5 to 10 mils, wherein the film layer has a 1% secant modulus in the Machine Direction (MD) of 190 MPa or greater when measured at a film thickness of about 1 mil and an Oxygen Transmission Rate (OTR) of 650 cm or greater when measured at a film thickness of about 1 mil³100 square inches.

Embodiment QQ. film layer having a thickness of 0.5 to 10 mils, wherein the film layer has a 1% secant modulus in the Machine Direction (MD) of 190 MPa or greater when measured at a film thickness of about 1 mil and an Oxygen Transmission Rate (OTR) of 650 cm or greater when measured at a film thickness of about 1 mil³Per 100 square inches, Seal Initiation Temperature (SIT). ltoreq.100 ℃ when measured at a film thickness of about 2 mils, and hot tack window Area (AHTW). gtoreq.160 newtons ∙ ℃ when measured at a film thickness of about 2 mils.

Embodiment RR. includes a film of the polyethylene composition of embodiments a, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W, X, Y, Z, AA, BB, CC, DD, EE, FF, or GG that satisfies the following relationship:

hot tack Window Area (AHTW) > -2.0981 (1% secant modulus in Machine Direction (MD)) + 564.28;

wherein the AHTW is measured at a film thickness of about 2 mils and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

Embodiment SS. includes a film of the polyethylene composition of embodiments a, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W, X, Y, Z, AA, BB, CC, DD, EE, FF, or GG that satisfies the following relationship:

oxygen Transmission Rate (OTR) > -5.4297 (1% secant modulus in Machine Direction (MD)) + 1767.8;

wherein the OTR is measured at a film thickness of about 1 mil and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

Embodiment TT. includes a film of the polyethylene composition of embodiments a, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W, X, Y, Z, AA, BB, CC, DD, EE, FF, or GG that satisfies the following relationship:

seal Initiation Temperature (SIT) < 0.366 (1% secant modulus in Machine Direction (MD)) + 22.509;

wherein SIT is measured at a film thickness of about 2 mils and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

A film comprising a polyethylene composition of embodiments a, B, C, D, E, F, G, H, I, J, K, L, M, N, O, P, Q, R, S, T, U, V, W, X, Y, Z, AA, BB, CC, DD, EE, FF, or GG, the film satisfying the following relationship:

i) hot tack Window Area (AHTW) > -2.0981 (1% secant modulus in Machine Direction (MD)) + 564.28;

wherein AHTW is measured at a film thickness of about 2 mils, and Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil;

ii) Oxygen Transmission Rate (OTR) > -5.4297 (1% secant modulus in Machine Direction (MD) + 1767.8;

wherein the OTR is measured at a film thickness of about 1 mil and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil; and

iii) Seal Initiation Temperature (SIT) < 0.366 (1% secant modulus in Machine Direction (MD) + 22.509;

wherein SIT is measured at a film thickness of about 2 mils and the Machine Direction (MD)1% secant modulus is measured at a film thickness of about 1 mil.

INDUSTRIAL APPLICABILITY

Plastic films made from ethylene copolymers are often used in food packaging applications. The present disclosure provides polyethylene compositions having good stiffness, permeability, and sealability when blown into a film.

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Polyethylene compositions and films having good permeability, stiffness and sealability

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