U.S. patent application number 14/406966 was filed with the patent office on 2015-06-18 for heat-resistant polyolefin compositions suitable for films.
This patent application is currently assigned to Dow Global Technologies LLC. The applicant listed for this patent is DOW GLOBAL TECHNOLOGIES LLC. Invention is credited to Ashish Batra, Andy C. Chang, Charles F. Diehl, Suzanne M. Guerra, Jill M. Martin.
Application Number | 20150166779 14/406966 |
Document ID | / |
Family ID | 49118842 |
Filed Date | 2015-06-18 |
United States Patent
Application |
20150166779 |
Kind Code |
A1 |
Diehl; Charles F. ; et
al. |
June 18, 2015 |
HEAT-RESISTANT POLYOLEFIN COMPOSITIONS SUITABLE FOR FILMS
Abstract
Compositions are provided that comprise: (1) a polymer selected
from the group consisting of: (A) an ethylene/.alpha.-olefin
multiblock interpolymer; (B) a propylene based plastomer or
elastomer; and (C) a mixture of (A) and (B); (2) from about 1 to
about 75 weight percent filler based on the weight of the
composition; and (3) an effective amount of tackifier.
Inventors: |
Diehl; Charles F.; (Durango,
CO) ; Chang; Andy C.; (Houston, TX) ; Batra;
Ashish; (Zionsville, IN) ; Guerra; Suzanne M.;
(Lake Jackson, TX) ; Martin; Jill M.; (Pearland,
TX) |
|
Applicant: |
Name |
City |
State |
Country |
Type |
DOW GLOBAL TECHNOLOGIES LLC |
Midland |
MI |
US |
|
|
Assignee: |
Dow Global Technologies LLC
Midland
MI
|
Family ID: |
49118842 |
Appl. No.: |
14/406966 |
Filed: |
August 29, 2013 |
PCT Filed: |
August 29, 2013 |
PCT NO: |
PCT/US2013/057342 |
371 Date: |
December 10, 2014 |
Related U.S. Patent Documents
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Application
Number |
Filing Date |
Patent Number |
|
|
61695652 |
Aug 31, 2012 |
|
|
|
Current U.S.
Class: |
524/528 ;
524/570; 524/579 |
Current CPC
Class: |
C08L 51/06 20130101;
C08K 5/0008 20130101; C08L 2201/08 20130101; C08L 23/0815 20130101;
C08K 3/013 20180101; C08K 3/20 20130101; C08L 23/16 20130101; C08L
23/142 20130101; C08L 23/0815 20130101; C08K 3/20 20130101; C08L
51/06 20130101; C08L 51/06 20130101; C08L 23/142 20130101; C08L
2203/16 20130101; C08K 3/20 20130101; C08L 23/0815 20130101 |
International
Class: |
C08L 23/16 20060101
C08L023/16; C08K 5/00 20060101 C08K005/00; C08K 3/00 20060101
C08K003/00 |
Claims
1. A composition suitable for a fabricated article comprising: (1)
a polymer selected from the group consisting of: (A) an
ethylene/.alpha.-olefin multiblock interpolymer; (B) a propylene
based plastomer or elastomer; and (C) a mixture of (A) and (B); (2)
from 1 to 75 weight percent filler based on the weight of the
composition; and (3) an effective amount of at least one
tackifier.
2. The composition of claim 1 wherein the composition has a Tg as
measured by DSC of 0.degree. C. to 40.degree. C.
3. The composition of claim 1 wherein the polymer is an
ethylene/.alpha.-olefin multiblock interpolymer which is
characterized by a Mw/Mn from 1.7 to 3.5, at least one melting
point, Tm, in degrees Celsius, and a density, d, in grams/cubic
centimeter, wherein the numerical values of Tm and d correspond to
the relationship: T.sub.m>-6553.3+13735(d)-7051.7(d).sup.2.
4. The composition of claim 3 wherein the ethylene/.alpha.-olefin
multiblock interpolymer is an ethylene-octene interpolymer
comprising at least 50 mole percent ethylene.
5. The composition of claim 1 wherein the polymer is a propylene
based plastomer or elastomer which is a propylene-ethylene
interpolymer comprising at least 80 mole percent propylene.
6. The composition of claim 1 wherein the weight ratio of tackifier
to polymer is from 0.1 to 4.
7. The composition of claim 1 wherein the filler comprises from 40
to 75 weight percent of the composition based on the total weight
of the composition.
8. The composition of claim 1 wherein the tackifier has a Ring and
Ball Softening Point of from 100 to 160.degree. C.
10. The composition of claim 1 wherein the tackifier has a glass
transition temperature of from 40 to 95.degree. C.
11. The composition of claim 1 wherein the tackifier has a density
of from 0.5 to 1.5 g/cm.sup.3.
12. The composition of claim 1 which further comprises low density
polyethylene.
Description
FIELD OF THE INVENTION
[0001] This invention relates to improved polyolefin compositions
which are heat-resistant and often suitable for films.
BACKGROUND
[0002] Polyvinyl chloride (PVC) is a widely used thermoplastic
polymer. It is often used in applications requiring a conformable
and/or flame resistant formulation. Such applications include tapes
suitable for, for example, signage, drapes, and bandages.
Unfortunately, PVC-based formulations often result in fogging and
release HCl when they burn. The released HCl fumes and the
breakdown of the HCl fumes may pose a health hazard. Furthermore,
to achieve soft conformable characteristics of flexible polyvinyl
chloride (f-PVC), current practice is to formulate with phthalates
which are associated with potential health risks. In addition, it
is also unfortunate that polyvinyl chloride production typically
requires a vinyl chloride starting material. The vinyl chloride
production, as well as incineration of waste PVC may create harmful
dioxins. Accordingly, compositions are needed that have
characteristics of PVC-based formulations yet lack PVC and its
inherent disadvantages.
SUMMARY OF THE INVENTION
[0003] Advantageously, compositions have been discovered that are
capable of replacing PVC-based formulations and are often suitable
for, for example, films. In one embodiment, the inventive
compositions comprise: (1) a polymer selected from the group
consisting of: (A) an ethylene/.alpha.-olefin multiblock
interpolymer; (B) a propylene based plastomer or elastomer; and (C)
a mixture of (A) and (B); (2) from about 1 to about 75 weight
percent filler based on the weight of the composition; and (3) an
effective amount of tackifier. In another embodiment the
ethylene/.alpha.-olefin multiblock interpolymers are characterized
before any crosslinking by one or more of the following
characteristics:
[0004] (1) an average block index greater than zero and up to about
1.0 and a molecular weight distribution, Mw/Mn, greater than about
1.3; or
[0005] (2) at least one molecular fraction which elutes between
40.degree. C. and 130.degree. C. when fractionated using TREF,
characterized in that the fraction has a block index of at least
0.5 and up to about 1; or
[0006] (3) an Mw/Mn from about 1.7 to about 3.5, at least one
melting point, Tm, in degrees Celsius, and a density, d, in
grams/cubic centimeter, wherein the numerical values of Tm and d
correspond to the relationship:
T.sub.m>-6553.3+13735(d)-7051.7(d).sup.2; or
[0007] (4) an Mw/Mn from about 1.7 to about 3.5, and a heat of
fusion, .DELTA.H in J/g, and a delta quantity, .DELTA.T, in degrees
Celsius defined as the temperature difference between the tallest
DSC peak and the tallest CRYSTAF peak, wherein the numerical values
of .DELTA.T and .DELTA.H have the following relationships:
.DELTA.T>-0.1299(.DELTA.H)+62.81 for .DELTA.H greater than zero
and up to 130 J/g,
.DELTA.T>48.degree. C. for .DELTA.H greater than 130 J/g,
[0008] wherein the CRYSTAF peak is determined using at least 5
percent of the cumulative polymer, and if less than 5 percent of
the polymer has an identifiable CRYSTAF peak, then the CRYSTAF
temperature is 30.degree. C.; or
[0009] (5) an elastic recovery, Re, in percent at 300 percent
strain and 1 cycle measured with a compression-molded film of the
ethylene/.alpha.-olefin interpolymer, and has a density, d, in
grams/cubic centimeter, wherein the numerical values of Re and d
satisfy the following relationship when ethylene/.alpha.-olefin
interpolymer is substantially free of a cross-linked phase:
Re>1481-1629(d); or
[0010] (6) has a molecular fraction which elutes between 40.degree.
C. and 130.degree. C. when fractionated using TREF, characterized
in that the fraction has a molar comonomer content greater than, or
equal to, the quantity (-0.2013) T+20.07, more preferably greater
than or equal to the quantity (-0.2013) T+21.07, where T is the
numerical value of the peak elution temperature of the TREF
fraction, measured in .degree. C.; or
[0011] (7) a storage modulus at 25.degree. C., G' (25.degree. C.),
and a storage modulus at 100.degree. C., G' (100.degree. C.),
wherein the ratio of G'(25.degree. C.) to G' (100.degree. C.) is in
the range of about 1:1 to about 9:1.
[0012] The ethylene/.alpha.-olefin multiblock interpolymer
characteristics (1) through (7) above are given with respect to the
ethylene/.alpha.-olefin interpolymer before any significant
crosslinking, i.e., before crosslinking. The
ethylene/.alpha.-olefin interpolymers useful in the present
invention may or may not be crosslinked depending upon the desired
properties. By using characteristics (1) through (7) as measured
before crosslinking is not meant to suggest that the interpolymer
is required or not required to be crosslinked--only that the
characteristic is measured with respect to the interpolymer without
significant crosslinking. Crosslinking may or may not change each
of these properties depending upon the specific polymer and degree
of crosslinking
BRIEF DESCRIPTION OF THE DRAWINGS
[0013] FIG. 1 shows retained load (fraction) over 5 minutes on
applying 100% strain for control f-PVC and formulations A-D tapes
of Example 1.
[0014] FIG. 2 shows recovery on removing the strain for f-PVC
control and formulations A-D of Example 1.
[0015] FIG. 3 shows stress-strain curve for inventive formulations
A-D and f-PVC control of Example 1.
[0016] FIG. 4 shows 25% Hysteresis for f-PVC and for formulations A
through D of Example 1.
[0017] FIG. 5 shows stress-strain curve for inventive flame
resistance formulations 1-4 of Example 2.
[0018] FIG. 6 shows retained load (fraction) over 5 minutes on
applying 100% strain for formulations 1-4 of Example 2.
[0019] FIG. 7 shows recovery on removing the strain for
formulations 1-4 of Example 2.
[0020] FIG. 8 shows 25% Hysteresis for formulations 1 through 4 of
Example 2.
[0021] FIG. 9 compares the melt strength of formulations 1 and 2 of
Example 2 and formulations 5-10 of Example 3.
[0022] FIG. 10 shows stress-strain curve for flame resistance
formulations of Example 5.
[0023] FIG. 11 shows recovery on removing the strain for
formulations of Example 5.
[0024] FIG. 12 shows recovery on removing the strain for
formulations of Example 5.
[0025] FIG. 13 shows tan.delta. vs. temperature for formulations of
Example 5 that vary the amount of tackifier.
DETAILED DESCRIPTION OF THE INVENTION
[0026] "Polymer" means a polymeric compound prepared by
polymerizing monomers, whether of the same or a different type. The
generic term "polymer" embraces the terms "homopolymer,"
"copolymer," "terpolymer" as well as "interpolymer."
[0027] "Interpolymer" means a polymer prepared by the
polymerization of at least two different types of monomers. The
generic term "interpolymer" includes the term "copolymer" (which is
usually employed to refer to a polymer prepared from two different
monomers) as well as the term "terpolymer" (which is usually
employed to refer to a polymer prepared from three different types
of monomers). It also encompasses polymers made by polymerizing
four or more types of monomers.
[0028] "Composition," as used herein, includes a mixture of
materials which comprise the composition, as well as reaction
products and decomposition products formed from the ingredients or
materials of the composition. Specifically included within the
compositions of the present invention are grafted or coupled
compositions wherein an initiator or coupling agent reacts with at
least a portion of one or more polymers and/or at least a portion
of one or more fillers.
[0029] The compositions of the present invention typically comprise
(1) a polymer selected from the group consisting of: (A) an olefin
block copolymer; (B) a propylene based plastomer or elastomer; and
(C) a mixture of (A) and (B); (2) from about 0, preferably from
about 1 weight percent to about 75 weight percent filler based on
the weight of the composition; and (3) an effective amount of
tackifier.
[0030] The term "olefin block copolymer" or "OBC" means an
ethylene/.alpha.-olefin multi-block copolymer and includes ethylene
and one or more copolymerizable .alpha.-olefin comonomer in
polymerized form, characterized by multiple blocks or segments of
two or more polymerized monomer units differing in chemical or
physical properties. The terms "interpolymer" and "copolymer" are
used interchangeably herein. When referring to amounts of
"ethylene" or "comonomer" in the copolymer, it is understood that
this means polymerized units thereof. In some embodiments, the
multi-block copolymer can be represented by the following
formula:
(AB).sub.n
where n is at least 1, preferably an integer greater than 1, such
as 2, 3, 4, 5, 10, 15, 20, 30, 40, 50, 60, 70, 80, 90, 100, or
higher, "A" represents a hard block or segment and "B" represents a
soft block or segment. Preferably, As and Bs are linked in a
substantially linear fashion, as opposed to a substantially
branched or substantially star-shaped fashion. In other
embodiments, A blocks and B blocks are randomly distributed along
the polymer chain. In other words, the block copolymers usually do
not have a structure as follows.
AAA-AA-BBB-BB
[0031] In still other embodiments, the block copolymers do not
usually have a third type of block, which comprises different
comonomer(s). In yet other embodiments, each of block A and block B
has monomers or comonomers substantially randomly distributed
within the block. In other words, neither block A nor block B
comprises two or more sub-segments (or sub-blocks) of distinct
composition, such as a tip segment, which has a substantially
different composition than the rest of the block. For purposes of
United States patent practice, the contents of PCT Application No.
PCT/US2005/008917 (Dow 63558D), filed on Mar. 17, 2005, which in
turn claims priority to U.S. Provisional Application No.
60/553,906, filed Mar. 17, 2004 as well as WO 2006/115839 published
on Nov. 2, 2006 are herein incorporated by reference in their
entirety.
[0032] Preferably, ethylene comprises the majority mole fraction of
the whole block copolymer, i.e., ethylene comprises at least 50
mole percent of the whole polymer. More preferably ethylene
comprises at least 60 mole percent, at least 70 mole percent, or at
least 80 mole percent, with the substantial remainder of the whole
polymer comprising at least one other comonomer that is preferably
an .alpha.-olefin having 3 or more carbon atoms. In some
embodiments, the olefin block copolymer may comprise 50 mol % to 90
mol % ethylene, preferably 60 mol % to 85 mol %, more preferably 65
mol % to 80 mol %. For many ethylene/octene block copolymers, the
preferred composition comprises an ethylene content greater than 80
mole percent of the whole polymer and an octene content of from 10
to 15, preferably from 15 to 20 mole percent of the whole
polymer.
[0033] The olefin block copolymer includes various amounts of
"hard" and "soft" segments. "Hard" segments are blocks of
polymerized units in which ethylene is present in an amount greater
than 95 weight percent, or greater than 98 weight percent based on
the weight of the polymer, up to 100 weight percent. In other
words, the comonomer content (content of monomers other than
ethylene) in the hard segments is less than 5 weight percent, or
less than 2 weight percent based on the weight of the polymer, and
can be as low as zero. In some embodiments, the hard segments
include all, or substantially all, units derived from ethylene.
"Soft" segments are blocks of polymerized units in which the
comonomer content (content of monomers other than ethylene) is
greater than 5 weight percent, or greater than 8 weight percent,
greater than 10 weight percent, or greater than 15 weight percent
based on the weight of the polymer. In some embodiments, the
comonomer content in the soft segments can be greater than 20
weight percent, greater than 25 weight percent, greater than 30
weight percent, greater than 35 weight percent, greater than 40
weight percent, greater than 45 weight percent, greater than 50
weight percent, or greater than 60 weight percent and can be up to
100 weight percent.
[0034] The soft segments can be present in an OBC from 1 weight
percent to 99 weight percent of the total weight of the OBC, or
from 5 weight percent to 95 weight percent, from 10 weight percent
to 90 weight percent, from 15 weight percent to 85 weight percent,
from 20 weight percent to 80 weight percent, from 25 weight percent
to 75 weight percent, from 30 weight percent to 70 weight percent,
from 35 weight percent to 65 weight percent, from 40 weight percent
to 60 weight percent, or from 45 weight percent to 55 weight
percent of the total weight of the OBC. Conversely, the hard
segments can be present in similar ranges. The soft segment weight
percentage and the hard segment weight percentage can be calculated
based on data obtained from DSC or NMR. Such methods and
calculations are disclosed in, for example, U.S. Pat. No.
7,608,668, entitled "Ethylene/.alpha.-Olefin Block Inter-polymers,"
filed on Mar. 15, 2006, in the name of Colin L. P. Shan, Lonnie
Hazlitt, et. al. and assigned to Dow Global Technologies Inc., the
disclosure of which is incorporated by reference herein in its
entirety. In particular, hard and soft segment weight percentages
and comonomer content may be determined as described in Column 57
to Column 63 of U.S. Pat. No. 7,608,668.
[0035] The olefin block copolymer is a polymer comprising two or
more chemically distinct regions or segments (referred to as
"blocks") preferably joined in a linear manner, that is, a polymer
comprising chemically differentiated units which are joined
end-to-end with respect to polymerized ethylenic functionality,
rather than in pendent or grafted fashion. In an embodiment, the
blocks differ in the amount or type of incorporated comonomer,
density, amount of crystallinity, crystallite size attributable to
a polymer of such composition, type or degree of tacticity
(isotactic or syndiotactic), regio-regularity or
regio-irregularity, amount of branching (including long chain
branching or hyper-branching), homogeneity or any other chemical or
physical property. Compared to block interpolymers of the prior
art, including interpolymers produced by sequential monomer
addition, fluxional catalysts, or anionic polymerization
techniques, the present OBC is characterized by unique
distributions of both polymer polydispersity (PDI or Mw/Mn or MWD),
block length distribution, and/or block number distribution, due,
in an embodiment, to the effect of the shuttling agent(s) in
combination with multiple catalysts used in their preparation.
[0036] In an embodiment, the OBC is produced in a continuous
process and possesses a polydispersity index, PDI, from 1.7 to 3.5,
or from 1.8 to 3, or from 1.8 to 2.5, or from 1.8 to 2.2. When
produced in a batch or semi-batch process, the OBC possesses PDI
from 1.0 to 3.5, or from 1.3 to 3, or from 1.4 to 2.5, or from 1.4
to 2.
[0037] In addition, the olefin block copolymer possesses a PDI
fitting a Schultz-Flory distribution rather than a Poisson
distribution. The present OBC has both a polydisperse block
distribution as well as a polydisperse distribution of block sizes.
This results in the formation of polymer products having improved
and distinguishable physical properties. The theoretical benefits
of a polydisperse block distribution have been previously modeled
and discussed in Potemkin, Physical Review E (1998) 57 (6), pp.
6902-6912, and Dobrynin, J. Chem. Phvs. (1997) 107 (21), pp
9234-9238.
[0038] In an embodiment, the present olefin block copolymer
possesses a most probable distribution of block lengths. In an
embodiment, the olefin block copolymer is defined as having:
[0039] (A) Mw/Mn from 1.7 to 3.5, at least one melting point, Tm,
in degrees Celsius, and a density, d, in grams/cubic centimeter,
where in the numerical values of Tm and d correspond to the
relationship:
Tm>-2002.9+4538.5(d)-2422.2(d).sup.2, and/or
[0040] (B) Mw/Mn from 1.7 to 3.5, and is characterized by a heat of
fusion, .DELTA.H in J/g, and a delta quantity, .DELTA.T, in degrees
Celsius defined as the temperature difference between the tallest
DSC peak and the tallest Crystallization Analysis Fractionation
("CRYSTAF") peak, wherein the numerical values of .DELTA.T and
.DELTA.H have the following relationships:
.DELTA.T>-0.1299 .DELTA.H+62.81 for .DELTA.H greater than zero
and up to 130 J/g
.DELTA.T.gtoreq.48.degree. C. for .DELTA.H greater than 130 J/g
wherein the CRYSTAF peak is determined using at least 5 percent of
the cumulative polymer, and if less than 5 percent of the polymer
has an identifiable CRYSTAF peak, then the CRYSTAF temperature is
30.degree. C.; and/or
[0041] (C) elastic recovery, Re, in percent at 300 percent strain
and 1 cycle measured with a compression-molded film of the
ethylene/.alpha.-olefin interpolymer, and has a density, d, in
grams/cubic centimeter, wherein the numerical values of Re and d
satisfy the following relationship when ethylene/.alpha.-olefin
interpolymer is substantially free of crosslinked phase:
Re>1481-1629(d); and/or
[0042] (D) has a molecular fraction which elutes between 40.degree.
C. and 130.degree. C. when fractionated using TREF, characterized
in that the fraction has a molar comonomer content greater than, or
equal to, the quantity (-0.2013) T+20.07, more preferably greater
than or equal to the quantity (-0.2013) T+21.07, where T is the
numerical value of the peak elution temperature of the TREF
fraction, measured in .degree. C.; and/or,
[0043] (E) has a storage modulus at 25.degree. C., G' (25.degree.
C.), and a storage modulus at 100.degree. C., G' (100.degree. C.),
wherein the ratio of G' (25.degree. C.) to G' (100.degree. C.) is
in the range of 1:1 to 9:1.
[0044] The olefin block copolymer may also have:
[0045] (F) a molecular fraction which elutes between 40.degree. C.
and 130.degree. C. when fractionated using TREF, characterized in
that the fraction has a block index of at least 0.5 and up to 1 and
a molecular weight distribution, Mw/Mn, greater than 1.3;
and/or
[0046] (G) average block index greater than zero and up to 1.0 and
a molecular weight distribution, Mw/Mn greater than 1.3. It is
understood that the olefin block copolymer may have one, some, all,
or any combination of properties (A)-(G). Block Index can be
determined as described in detail in U.S. Pat. No. 7,608,668 herein
incorporated by reference for that purpose. Analytical methods for
determining properties (A) through (G) are disclosed in, for
example, U.S. Pat. No 7,608,668, Col. 31, line 26 through Col. 35,
line 44, which is herein incorporated by reference for that
purpose.
[0047] Suitable monomers for use in preparing the present OBC
include ethylene and one or more addition polymerizable monomers
other than ethylene. Examples of suitable comonomers include
straight-chain or branched .alpha.-olefins of 3 to 30, preferably 3
to 20, carbon atoms, such as propylene, 1-butene, 1-pentene,
3-methyl-l-butene, 1-hexene, 4-methyl-1-pentene,
3-methyl-l-pentene, 1-octene, 1-decene, 1-dodecene, 1-tetradecene,
1-hexadecene, 1-octadecene and 1-eicosene; cyclo-olefins of 3 to
30, preferably 3 to 20, carbon atoms, such as cyclopentene,
cycloheptene, norbornene, 5-methyl-2-norbornene,
tetracyclododecene, and
2-methyl-1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene;
di-and polyolefins, such as butadiene, isoprene,
4-methyl-1,3-pentadiene, 1,3-pentadiene, 1,4-pentadiene,
1,5-hexadiene, 1,4-hexadiene, 1,3-hexadiene, 1,3-octadiene,
1,4-octadiene, 1,5-octadiene, 1,6-octadiene, 1,7-octadiene,
ethylidenenorbornene, vinyl norbornene, dicyclopentadiene,
7-methyl-1,6-octadiene, 4-ethylidene-8-methyl-1,7-nonadiene, and
5,9-dimethyl-1,4,8-decatriene; and 3-phenylpropene,
4-phenylpropene, 1,2-difluoroethylene, tetrafluoroethylene, and
3,3,3-trifluoro-1-propene.
[0048] The olefin block copolymer has a density of from 0.820 g/cc
to 0.925 g/cc, or from 0.860 g/cc to 0.88 g/cc or from 0.860 g/cc
to 0.879 g/cc. The OBC has a Shore A value of 40 to 70, preferably
from 45 to 65 and more preferably from 50 to 65. In some
embodiments, the olefin block copolymer has a melt index (MI) from
0.1 g/10 min to 30 g/10, or from 0.1 g/10 min to 20 g/10 min, or
from 0.1 g/10 min to 15 g/10 min, as measured by ASTM D 1238
(190.degree. C./2.16 kg). The olefin block copolymer is present in
an amount of 5 wt % to 45 wt %, preferably 10 wt % to 30 wt %, more
preferably 10 wt % to 25 wt %. The composition may comprise more
than one olefin block copolymer.
[0049] The olefin block copolymers can be produced via a chain
shuttling process such as described in U.S. Pat. No. 7,858,706,
which is herein incorporated by reference. In particular, suitable
chain shuttling agents and related information are listed in Col.
16, line 39 through Col. 19, line 44. Suitable catalysts are
described in Col. 19, line 45 through Col. 46, line 19 and suitable
co-catalysts in Col. 46, line 20 through Col. 51 line 28. The
process is described throughout the document, but particularly in
Col. Col 51, line 29 through Col. 54, line 56. The process is also
described, for example, in the following: U.S. Pat. No. 7,608,668;
U.S. Pat. No. 7,893,166; and U.S. Pat. No. 7,947,793.
[0050] The olefin block copolymer may be a reaction product of
ethylene/.alpha.-olefin interpolymer and any suitable cross-linking
agent, i.e., a cross-linked ethylene/.alpha.-olefin interpolymer.
Thus, cross-linking agents may be chemical compounds but are not
necessarily so. Cross-linking agents as used herein also include
electron-beam irradiation, beta irradiation, gamma irradiation,
corona irradiation, silanes, peroxides, allyl compounds and UV
radiation with or without crosslinking catalyst. U.S. Pat. Nos.
6,803,014 and 6,667,351 disclose electron-beam irradiation methods
that can be used in embodiments of the invention. In some
embodiments, the percent of cross-linked polymer is at least 10
percent, preferably at least about 20 percent, more preferably at
least about 25 percent up to about 75 percent, preferably up to
about 50 percent, as measured by the weight percent of gels formed.
Typically, as the amount of crosslinking increases, the ignition
resistance of the composition increases.
[0051] The terms "propylene-ethylene interpolymer",
"propylene-based polymer" or "propylene based plastomers or
elastomers (PBPE)" generally refer to copolymers comprising
propylene and a monomer such as ethylene. Preferably, propylene
comprises the majority mole fraction of the whole polymer, i.e.,
propylene comprises at least about 70, preferably at least about
80, more preferably at least about 90 mole percent of the whole
polymer with a substantial remainder of the whole polymer
comprising at least one other comonomer that is preferably
ethylene. Suitable propylene-ethylene interpolymers are described
in, for example, WO 2006/115839 published on Nov. 2, 2006 and
incorporated herein by reference. Suitable propylene-ethylene
interpolymers are sold commercially by The Dow Chemical Company as
VERSIFY.TM., by Exxon as VISTAMAXX.TM., LICOCENE.TM. polymers
(Clariant), EASTOFLEX.TM. polymers (Eastman Chemical Co.),
REXTAC.TM. polymers (Hunstman), and VESTOPLAST.TM. polymers
(Degussa). Other suitable polymers include
propylene-.alpha.-olefins block copolymers and interpolymers, and
other propylene based block copolymers and interpolymers known in
the art.
[0052] Preferably, the propylene-based polymer has a melt flow rate
(MFR) in the range of 0.01 to 2000 g/10 min, more preferably in
range of 0.1 to 1000 g/10 min, and more preferably 0.5 to 500 g/10
min, and even more preferably 1 to 100 g/10 min, as measured in
accordance with ASTM D 1238 at 230.degree. C./2.16 kg.
[0053] In another embodiment, the propylene-based polymer has a
melt flow rate (MFR) in the range of 0.01 to 300 grams/10 minutes,
more preferably in range of 0.1 to 200 grams/10 minutes, more
preferably from 0.5 to 100 grams/10 min, or from 1 to 50 grams/10
min, as measured in accordance with ASTM D 1238 at 230.degree.
C./2.16 kg. All individual values and subranges from 0.01 to 300
grams/10 min are included herein and disclosed herein.
[0054] The propylene-based polymer used in the present invention
may be of any molecular weight distribution (MWD). Propylene-based
polymers of broad or narrow MWD are formed by means within the
skill in the art. Propylene-based polymers having a narrow MWD can
be advantageously provided by visbreaking or by manufacturing
reactor grades (non visbroken) using single-site catalysis, or by
both methods.
[0055] The propylene-based polymer can be reactor-grade, visbroken,
branched or coupled to provide increased nucleation and
crystallization rates. The term "coupled" is used herein to refer
to propylene-based polymers which are rheology-modified, such that
they exhibit a change in the resistance of the molten polymer to
flow during extrusion (for example, in the extruder immediately
prior to the annular die). Whereas "visbroken" is in the direction
of chain-scission, "coupled" is in the direction of crosslinking or
networking. As an example of coupling, a coupling agent (for
example, an azide compound) is added to a relatively high melt flow
rate polypropylene polymer, such that after extrusion, the
resultant polypropylene polymer composition attains a substantially
lower melt flow rate than the initial melt flow rate. Preferably,
for coupled or branched polypropylene, the ratio of subsequent MFR
to initial MFR is less than, or equal, to 0.7:1, more preferably
less than or equal to 0.2:1.
[0056] Suitable branched propylene-based polymers for use in the
present invention are commercially available, for instance from
Basell, under the trade designations Profax PF-611 and PF-814.
Alternatively, suitable branched or coupled propylene-based
polymers can be prepared by means, within the skill in the art,
such as by peroxide or electron-beam treatment, for instance as
disclosed by DeNicola et al., in U.S. Pat. No. 5,414,027 (the use
of high energy (ionizing) radiation in a reduced oxygen
atmosphere); EP 0 190 889 to Himont (electron beam irradiation of
isotactic polypropylene at lower temperatures); U.S. Pat. No.
5,464,907 (Akzo Nobel NV); EP 0 754 711 Solvay (peroxide
treatment); and U.S. patent application Ser. No. 09/133,576, filed
Aug. 13, 1998 (azide coupling agents). Each of these
patents/applications is incorporated herein by reference.
[0057] Usually, the mixture and amount of components in the
inventive compositions is such that the composition has an
appropriate Tg, as measured by DSC, and appropriate density for the
desired application. For applications such as signage, table
cloths, drapes, medical or surgical drapes, bandages, wound
dressings, etc. a typical Tg, as measured by DSC, is from about
-10.degree. C. to about 50.degree. C. and preferably from about
0.degree. C. to about 40.degree. C. Similarly, the density should
be appropriate for the desired application. For the aforementioned
applications an appropriate density of the composition is often
from about 0.5 g/cm.sup.3 to about 5 g/cm.sup.3, preferably from
about 0.75 g/cm.sup.3 to about 3 g/cm.sup.3, more preferably from
about 1 g/cm.sup.3 to about 2 g/cm.sup.3. The polymers, tackifiers,
and fillers may be mixed in any convenient manner but are typically
compounded in, for example, a Banbury mixer or twin screw extruder.
Alternatively, the components could be mixed using a solvent
suitable for dissolving the polymer and tackifier components.
Combination with fillers prior to removal of solvent would produce
the composition of invention as well.
[0058] The amount of polymer or mixture of polymers varies
depending upon the type of polymer, desired application,
properties, and other components of the application. Typically, the
weight ratio of tackifier to total polymer is at least about 0.1
preferably at least about 0.15, more preferably at least 0.2 to at
most about 4, preferably at most about 3, more preferably at most
about 2. It has been found that often affine deformation may be
achieved with from about 35 weight percent to about 90 weight
percent, more preferably from about 40 to about 85, and more
preferably from about 40 weight percent to about 82 weight percent
polymer based on the weight of the polymer and tackifier. In some
embodiments, the weight ratio of olefin block copolymer (A) to
propylene based polymer (B) is from about 10:1 to about 1:1. In
some embodiments, the composition has a normalized retained load
percentage after stress relaxation (Condition B, at ambient
conditions) above about 20. In some embodiments, the composition is
a thermoplastic composition with a normalized retained load
percentage after stress relaxation (Condition B, ambient
conditions) from about 20 to about 50 and heat resistance as
measured by peak melting point of from about 40.degree. C. to about
120.degree. C. In some embodiments, the filler comprises from about
1 to about 90 weight percent of the composition based on the total
weight of the composition. In some embodiments, the filler
comprises from 40 to about 75 weight percent of the composition
based on the total weight of the composition and the filler is a
flame retardant filler selected from the group consisting of
aluminum hydroxide, magnesium hydroxide, decabromodiphenyl oxide,
tetradecabromo-diphenoxy benzene, ethane-1,2-bis(pentabromophenyl),
ethylene bis-tetrabromophthalimide, and mixtures thereof.
[0059] In certain embodiments, the (A) an ethylene/.alpha.-olefin
multiblock interpolymer; (B) a propylene based plastomer or
elastomer; or (C) a mixture of (A) and (B) further comprises other
polymers, for example, random ethylene copolymers such as
AFFINITY.RTM. or ENGAGE.RTM., traditional polyethylenes such as
HDPE, LLDPE, ULDPE, LDPE and propylene-based polymers such as
homopolymer PP, random copolymer PP or PP-based
plastomers/elastomers or a combination thereof. The amount of such
other polymers differs depending upon the elasticity desired and
compatibility with the specific ethylene/.alpha.-olefin
interpolymer employed.
Tackifiers of the Compositions
[0060] The tackifiers that may be useful in the present invention
vary depending upon the application. However, typically they may be
any tackifier that is compatible with the polymer(s) to achieve the
desired properties, e.g., stress relaxation, conformability, and/or
drapability, to replace PVC in a given formulation. Compatibility
may be determined by routine experimentation but often useful
tackifiers may exhibit one or more of the following properties: a
glass transition temperature of from about 40.degree. C. to about
95.degree. C., a Ring and Ball Softening Point of from about
100.degree. C. to about 160.degree. C., or a density of from about
0.5 g/cm.sup.3 to about 1.5 g/cm.sup.3. Thus, in contrast to PVC
formulations which require plasticizers to lower the composition's
glass transition temperature, suitable tackifiers often raise the
glass transition temperature of the instant inventive compositions.
Suitable tackifiers may be selected from the group consisting of
rosins, modified rosins, rosin esters, aromatic modified
cycloaliphatic hydrocarbon resins, aliphatic petroleum hydrocarbon
resins, partially hydrogenated aliphatic resins, terpene resins and
mixtures thereof. Preferred tackifier resins are chosen from
cycloaliphatic hydrocarbon resins, partially hydrogenated
hydrocarbon resins, and mixtures thereof. Olefin block copolymer
(OBC) compatible tackifiers often have hydrogenated rings, a
Mw<2500 g/mol, low polarity, and/or low aromaticity. A Cloud
point test measures the temperature at which a resin begins to
precipitate from a solvent. Cloud point measurements in different
solvents are used as an indicator of polarity and aromaticity and
therefore as an indicator of compatibility with, for example, OBC.
The Mixed Methylcyclohexane-Aniline Point Test measures
aromaticity, with lower values indicating high aromatic content.
The DACP (Diacetone Alcohol Cloud Point) test measures polarity.
Lower values indicate more polarity. For OBC compatibility,
tackifiers with DACP values between about 40.degree. C. and about
80.degree. C. and a MMAP value between about 70.degree. C. and
about 90.degree. C. are often preferred.
[0061] The amount of tackifier varies depending upon the other
components and desired application. Typically, as the amount of
tackifier in the composition increases the tensile strength and/or
elongation of the composition decreases. On the other hand, as the
amount of tackifier decreases the elastic recovery increases and
stress relaxation decreases. Though not intended to be limited by
theory, a parameter that is known to correlate to a variety of
properties is the glass transition temperature (Tg).
[0062] The scientific community has developed theories and
equations that may be used to predict the relationship between
glass transition temperature (Tg) and composition. For example, the
well known the Fox equation below may be useful in predicting the
glass transition temperature of a blend of polymers with different
glass transition temperatures and can be used to predict the amount
of tackifier (with a known glass transition temperature) that may
be employed with a polyolefin (of a known glass transition
temperature) to achieve a desired T.sub.g for the blend:
1 T g = w a T ga + w b T gb ##EQU00001##
[0063] such that T.sub.g is the glass transition temperature of the
blend; T.sub.ga is the glass transition temperature of component A
and w.sub.a is the weight fraction of component A of the total
polymer fraction in the blend; T.sub.gb is the glass transition
temperature of component B and w.sub.b is the weight fraction of
component B of the total resin fraction in the blend.
[0064] Alternatively, other equations such as the Gordon-Taylor
equation may also be used. It is recognized that polymer theory for
describing properties of polymers will undergo further development
and refinement. It is the assertion of the authors that recognition
of theories is not intended to be limiting for the novel
compositions of the present invention.
Fillers of the Compositions
[0065] The type of filler and amount varies depending upon the
other ingredients, amounts, and desired application. For example,
if flame retardancy or high temperature performance is desired then
halogenated fillers may be useful as further described below.
Typically, the filler is selected from the group consisting of
ammonium polyphosphate, magnesium hydroxide, calcium hydroxide,
aluminum trihydrate (also referred to as aluminum trihydroxide),
calcium carbonate, glass fibers, marble dust, cement dust, clay,
feldspar, silica, diatomaceous earth, talc, or glass, fumed silica,
silicates, alumina, magnesium oxide, antimony oxide, zinc oxide,
barium sulfate, aluminum silicate, calcium silicate, titanium
oxides, glass microspheres, mica, clays, wollastonite, and
chalk.
[0066] Suitable flame retardant fillers are materials that inhibit
or resist the spread of fire. Naturally occurring substances such
as asbestos as well as synthetic materials, usually halocarbons
such as polybrominated diphenyl ether (PBDEs), polychlorinated
biphenyls (PCBs) and chlorendic acid derivates, most often dibutyl
chlorendate and dimethyl chlorendate, have been used in this
capacity. Generally, these classes of flame retardant compounds are
the most common: aluminium hydroxide, magnesium hydroxide, and
various hydrates; organobromines and organochlorines; phosphorus,
in the form of organophosphates, halogenated phosphorus compounds,
and red phosphorus; antimony trioxide; and boron compounds, mostly
borates. Tetrakis (hydroxymethyl) phosphonium salts, made by
passing phosphine gas through a solution of formaldehyde and a
mineral acid such as hydrochloric acid, are used as flame
retardants for textiles. Other flame retardants include chlorinated
paraffins, polybrominated biphenyls (PBB), pentabromodiphenyl ether
(pentaBDE), octabromodiphenyl ether (octaBDE), decabromodiphenyl
ether (decaBDE), hexabromocyclododecane (HBCD), tri-o-cresyl
phosphate, tris(2,3-dibromopropyl)phosphate (TRIS),
bis(2,3-dibromopropyl)phosphate, tris(1-aziridinyfi-phosphine oxide
(TEPA), and others. Particularly preferable flame retardant or high
temperature resistant fillers that are often compatible with
polyethylene include aluminum hydroxide, magnesium hydroxide,
decabromodiphenyl oxide, tetradecabromo-diphenoxy benzene,
ethane-1,2-bis(pentabromophenyl), ethylene
bis-tetrabromophthalimide, and mixtures thereof available from
Albemarle Corporation.
[0067] The amount of filler varies depending upon the application.
Typical amounts range from about 0, preferably from 1 weight
percent to about 90 weight percent, preferably from about 5 weight
percent to about 80 weight percent, more preferably from about 15
weight percent to about 70 weight percent, and most preferred from
about 40 to 75 weight percent filler based on the weight of the
total weight of the composition. In some embodiments comprising the
compositions of invention in coextruded structures, at least one
surface layer comprises 1 to 75% filler , more preferably 10 to 50
wt. %, and most preferred 10 to 40 wt. %. In bicomponent fibers, at
least one portion of fiber at the surface comprises 1 to 75%
filler, more preferably 10 to 50 wt. %, and most preferred 10 to 40
wt. %.
Additives
[0068] Other ingredients that may be useful in the instant
compositions include, for example, (1) at least one metal borate
selected from the metal borates of Group IIA, and, optionally,
about 0.5 to about 10 percent by weight of at least one processing
aid selected from the group consisting of polydimethylsiloxane,
organopolysiloxanes, tartaric acid, stearic acid, zinc stearic,
waxes, and high melt flow polyolefins; (2) at least one initiator
or at least one coupling agent selected from the group consisting
of organic peroxides, silanes, titanates, zirconates,
multifunctional vinyl compounds and organic azides; and (3) at
least one hindered amine stabilizer. Yet other additives include
coupling agent(s) such as those selected from the group consisting
of maleic anhydride, hydroxyl amine or epoxy modified polyolefins
and wetting agent(s) such as those selected from the group
consisting of transition metal stearates such as zinc stearate.
Properties of Compositions
[0069] The compositions find wide use in various applications and
the properties of the composition vary depending upon the
application for which it was formulated. In general the
compositions offer such desirable properties as stress relaxation,
conformability, drapability, and/or ignition resistance. The
specifics vary depending upon whether the formulation was designed
for, for example, use as signage, table cloths, drapes, medical or
surgical drapes, bandages, and wound dressings.
[0070] In some embodiments, compositions have one or preferably one
or more of the following properties: conformability with
stress-relaxation and dead-fold character and affine deformation;
processability by one or more fabrication processes including cast
film, blown film, or calendaring processes; ability to tear easily
and cleanly by hand; and film compatibility with adhesive. In fiber
or nonwoven applications, compositions usually have one or
preferably more of the following properties: made with methods know
in the art, the resulting article would have at least one of the
following properties: conformability with stress-relaxation and
dead-fold characteristics ; processability by one or more
fabrication processes including melt spun, solvent spun, staple
fiber, spunbond, melt blown, or combinations thereof; ability to
tear easily and cleanly by hand; and compatibility with
adhesive.
Testing Methods
[0071] In the examples that follow, the following analytical
techniques are employed:
Standard CRYSTAF Method
[0072] Branching distributions are determined by crystallization
analysis fractionation (CRYSTAF) using a CRYSTAF 200 unit
commercially available from PolymerChar, Valencia, Spain. The
samples are dissolved in 1,2,4 trichlorobenzene at 160.degree. C.
(0.66 mg/mL) for 1 hr and stabilized at 95.degree. C. for 45
minutes. The sampling temperatures range from 95 to 30.degree. C.
at a cooling rate of 0.2.degree. C./min. An infrared detector is
used to measure the polymer solution concentrations. The cumulative
soluble concentration is measured as the polymer crystallizes while
the temperature is decreased. The analytical derivative of the
cumulative profile reflects the short chain branching distribution
of the polymer.
[0073] The CRYSTAF peak temperature and area are identified by the
peak analysis module included in the CRYSTAF Software (Version
2001.b, PolymerChar, Valencia, Spain). The CRYSTAF peak finding
routine identifies a peak temperature as a maximum in the dW/dT
curve and the area between the largest positive inflections on
either side of the identified peak in the derivative curve. To
calculate the CRYSTAF curve, the preferred processing parameters
are with a temperature limit of 70.degree. C. and with smoothing
parameters above the temperature limit of 0.1, and below the
temperature limit of 0.3.
DSC Standard Method
[0074] Differential Scanning calorimetry results are determined
using a TAI model Q1000 DSC equipped with an RCS cooling accessory
and an autosampler. A nitrogen purge gas flow of 50 ml/min is used.
The sample is pressed into a thin film and melted in the press at
about 175.degree. C. and then air-cooled to room temperature
(25.degree. C.). 3-10 mg of material is then cut into a 6 mm
diameter disk, accurately weighed, placed in a light aluminum pan
(ca 50 mg), and then crimped shut. The thermal behavior of the
sample is investigated with the following temperature profile. The
sample is rapidly heated to 180.degree. C. and held isothermal for
3 minutes in order to remove any previous thermal history. The
sample is then cooled to -40.degree. C. at 10.degree. C./min.
cooling rate and held at -40.degree. C. for 3 minutes. The sample
is then heated to 150.degree. C. at 10.degree. C./min heating rate.
The cooling and second heating curves are recorded.
[0075] The DSC melting peak is measured as the maximum in heat flow
rate (W/g) with respect to the linear baseline drawn between
-30.degree. C. and end of melting. The heat of fusion is measured
as the area under the melting curve between -30.degree. C. and the
end of melting using a linear baseline.
GPC Method
[0076] The gel permeation chromatographic system consists of either
a Polymer Laboratories Model PL-210 or a Polymer Laboratories Model
PL-220 instrument. The column and carousel compartments are
operated at 140.degree. C. Three Polymer Laboratories 10-micron
Mixed-B columns are used. The solvent is 1,2,4 trichlorobenzene.
The samples are prepared at a concentration of 0.1 grams of polymer
in 50 milliliters of solvent containing 200 ppm of butylated
hydroxytoluene (BHT). Samples are prepared by agitating lightly for
2 hours at 160.degree. C. The injection volume used is 100
microliters and the flow rate is 1.0 ml/minute.
[0077] Calibration of the GPC column set is performed with 21
narrow molecular weight distribution polystyrene standards with
molecular weights ranging from 580 to 8,400,000, arranged in 6
"cocktail" mixtures with at least a decade of separation between
individual molecular weights. The standards are purchased from
Polymer Laboratories (Shropshire, UK). The polystyrene standards
are prepared at 0.025 grams in 50 milliliters of solvent for
molecular weights equal to or greater than 1,000,000, and 0.05
grams in 50 milliliters of solvent for molecular weights less than
1,000,000. The polystyrene standards are dissolved at 80.degree. C.
with gentle agitation for 30 minutes. The narrow standards mixtures
are run first and in order of decreasing highest molecular weight
component to minimize degradation. The polystyrene standard peak
molecular weights are converted to polyethylene molecular weights
using the following equation (as described in Williams and Ward, J.
Polym. Sci., Polym. Let., 6, 621 (1968)): M.sub.polyethylene=0.431
(M.sub.polystyrene).
[0078] Polyethylene equivalent molecular weight calculations are
performed using Viscotek TriSEC software Version 3.0.
Compression Set
[0079] Compression set is measured according to ASTM D 395. The
sample is prepared by stacking 25.4 mm diameter round discs of 3.2
mm, 2 0 mm, and 0.25 mm thickness until a total thickness of 12.7
mm is reached. The discs are cut from 12.7 cm.times.12.7 cm
compression molded plaques molded with a hot press under the
following conditions: zero pressure for 3 min at 190.degree. C.,
followed by 86 MPa for 2 min at 190.degree. C., followed by cooling
inside the press with cold running water at 86 MPa.
Density
[0080] Samples for density measurement are prepared according to
ASTM D 1928. Measurements are made within one hour of sample
pressing using ASTM D792, Method B.
Flexural/Secant Modulus/Storage Modulus
[0081] Samples are compression molded using ASTM D 1928. Flexural
and 2 percent secant moduli are measured according to ASTM D-790.
Storage modulus is measured according to ASTM D 5026-01 or
equivalent technique.
Mechanical Properties--Tensile, Hysteresis, Stress-Relaxation, Dead
Fold, and Tear
[0082] Stress-strain behavior in uniaxial tension is measured using
ASTM D 1708 microtensile specimens. Samples are stretched with an
Instron at 500% min.sup.-1 at 21.degree. C. Tensile strength and
elongation at break are reported from an average of 5
specimens.
[0083] 100% and 300% Hysteresis is determined from cyclic loading
to 100% and 300% strains using ASTM D 1708 microtensile specimens
with an Instron.TM. instrument. The sample is loaded and unloaded
at 267% min.sup.-1 for 3 cycles at 21.degree. C. Cyclic experiments
at 300% and 80.degree. C. are conducted using an environmental
chamber. In the 80.degree. C. experiment, the sample is allowed to
equilibrate for 45 minutes at the test temperature before testing.
In the 21.degree. C., 300% strain cyclic experiment, the retractive
stress at 150% strain from the first unloading cycle is recorded.
Percent recovery for all experiments are calculated from the first
unloading cycle using the strain at which the load returned to the
base line. The percent recovery is defined as:
% Recovery = f - s f .times. 100 ##EQU00002##
where .epsilon..sub.f is the strain taken for cyclic loading and
.epsilon..sub.s is the strain where the load returns to the
baseline during the 1.sup.st unloading cycle.
[0084] Stress relaxation is measured at 50 percent strain and
38.degree. C. for 12 hours using an Instron.TM. instrument equipped
with an environmental chamber. The gauge geometry is 76 mm.times.25
mm.times.0.4 mm After equilibrating at the temperature of interest
to the application (i.e. ambient, 37.degree. C., or other) for 45
min in the environmental chamber, the sample was stretched to a
target strain and rate of interest to the application (i.e.
Condition A: 50% strain at 333% min.sup.-1, Condition B: 100%
strain at 500% min.sup.-1) Stress was recorded as a function of
time for the duration of the test specific to the application which
is defined as the end of the test (i.e. 5 minutes, 12 hours). The
percent stress relaxation was calculated using the formula:
Stress Relaxation ( % ) = L o - L end L o .times. 100
##EQU00003##
where L.sub.o is the load at the target strain at 0 time and
L.sub.end is the load at the end of the test.
[0085] A simple test for dead fold property is performed by
stamping a 180.degree. fold in the film at ambient temperature and
then measuring the angle to which the fold opens thereafter. The
lower or smaller angles are desirable because this indicates
greater dead fold retention.
[0086] Tensile notched tear experiments are carried out on samples
having a density of 0.88 g/cc or less using an Instron.TM.
instrument. The geometry consists of a gauge section of 76
mm.times.13 mm.times.0 4 mm with a 2 mm notch cut into the sample
at half the specimen length. The sample is stretched at 508 mm
min.sup.-1 at 21.degree. C. until it breaks. The tear energy is
calculated as the area under the stress-elongation curve up to
strain at maximum load. An average of at least 3 specimens are
reported.
TMA
[0087] Thermal Mechanical Analysis (Penetration Temperature) is
conducted on 30 mm diameter.times.3.3 mm thick, compression molded
discs, formed at 180.degree. C. and 10 MPa molding pressure for 5
minutes and then air quenched. The instrument used is a TMA 7,
brand available from Perkin-Elmer. In the test, a probe with 1.5 mm
radius tip (P/N N519-0416) is applied to the surface of the sample
disc with 1N force. The temperature is raised at 5.degree. C./min
from 25.degree. C. The probe penetration distance is measured as a
function of temperature. The experiment ends when the probe has
penetrated 1 mm into the sample.
DMA
[0088] Dynamic Mechanical Analysis (DMA) is measured on compression
molded disks formed in a hot press at 180.degree. C. at 10 MPa
pressure for 5 minutes and then water cooled in the press at
90.degree. C./min. Testing is conducted using an ARES controlled
strain rheometer (TA instruments) equipped with dual cantilever
fixtures for torsion testing.
[0089] A 1.5 mm plaque is pressed and cut in a bar of dimensions
32.times.12 mm. The sample is clamped at both ends between fixtures
separated by 10 mm (grip separation .DELTA.L) and subjected to
successive temperature steps from -100.degree. C. to 200.degree. C.
(5.degree. C. per step). At each temperature the torsion modulus G'
is measured at an angular frequency of 10 rad/s, the strain
amplitude being maintained between 0.1 percent and 4 percent to
ensure that the torque is sufficient and that the measurement
remains in the linear regime.
[0090] An initial static force of 10 g is maintained (auto-tension
mode) to prevent slack in the sample when thermal expansion occurs.
As a consequence, the grip separation .DELTA.L increases with the
temperature, particularly above the melting or softening point of
the polymer sample. The test stops at the maximum temperature or
when the gap between the fixtures reaches 65 mm.
Melt Index
[0091] Melt index, or I.sub.2, is measured in accordance with ASTM
D 1238, Condition 190.degree. C./2.16 kg. Melt index, or I.sub.10
is also measured in accordance with ASTM D 1238, Condition
190.degree. C./10 kg.
ATREF
[0092] Analytical temperature rising elution fractionation (ATREF)
analysis is conducted according to the method described in U.S.
Pat. No. 4,798,081 and Wilde, L.; Ryle, T. R.; Knobeloch, D. C.;
Peat, I. R.; Determination of Branching Distributions in
Polyethylene and Ethylene Copolymers, J. Polym. Sci., 20, 441-455
(1982), which are incorporated by reference herein in their
entirety. The composition to be analyzed is dissolved in
trichlorobenzene and allowed to crystallize in a column containing
an inert support (stainless steel shot) by slowly reducing the
temperature to 20.degree. C. at a cooling rate of 0.1.degree.
C./min. The column is equipped with an infrared detector. An ATREF
chromatogram curve is then generated by eluting the crystallized
polymer sample from the column by slowly increasing the temperature
of the eluting solvent (trichlorobenzene) from 20 to 120.degree. C.
at a rate of 1.5.degree. C./min.
.sup.13C NMR Analysis
[0093] The samples are prepared by adding approximately 3 g of a
50/50 mixture of tetrachloroethane-d.sup.2/orthodichlorobenzene to
0.4 g sample in a 10 mm NMR tube. The samples are dissolved and
homogenized by heating the tube and its contents to 150.degree. C.
The data are collected using a JEOL Eclipse.TM. 400 MHz
spectrometer or a Varian Unity Plus.TM. 400 MHz spectrometer,
corresponding to a .sup.13C resonance frequency of 100.5 MHz. The
data are acquired using 4000 transients per data file with a 6
second pulse repetition delay. To achieve minimum signal-to-noise
for quantitative analysis, multiple data files are added together.
The spectral width is 25,000 Hz with a minimum file size of 32K
data points. The samples are analyzed at 130.degree. C. in a 10 mm
broad band probe. The comonomer incorporation is determined using
Randall's triad method (Randall, J. C.; JMS-Rev. Macromol. Chem.
Phys., C29, 201-317 (1989), which is incorporated by reference
herein in its entirety.
Polymer Fractionation by TREF
[0094] Large-scale TREF fractionation is carried by dissolving
15-20 g of polymer in 2 liters of 1,2,4-trichlorobenzene (TCB) by
stirring for 4 hours at 160.degree. C. The polymer solution is
forced by 15 psig (100 kPa) nitrogen onto a 3 inch by 4 foot (7.6
cm.times.12 cm) steel column packed with a 60:40 (v:v) mix of 30-40
mesh (600-425 nm) spherical, technical quality glass beads
(available from Potters Industries, HC 30 Box 20, Brownwood, Tex.,
76801) and stainless steel, 0.028'' (0.7 mm) diameter cut wire shot
(available from Pellets, Inc. 63 Industrial Drive, North Tonawanda,
N.Y., 14120). The column is immersed in a thermally controlled oil
jacket, set initially to 160.degree. C. The column is first cooled
ballistically to 125.degree. C., then slow cooled to 20.degree. C.
at 0.04.degree. C. per minute and held for one hour. Fresh TCB is
introduced at about 65 ml/min while the temperature is increased at
0.167.degree. C. per minute.
[0095] Approximately 2000 ml portions of eluant from the
preparative TREF column are collected in a 16 station, heated
fraction collector. The polymer is concentrated in each fraction
using a rotary evaporator until about 50 to 100 ml of the polymer
solution remains. The concentrated solutions are allowed to stand
overnight before adding excess methanol, filtering, and rinsing
(approx. 300-500 ml of methanol including the final rinse). The
filtration step is performed on a 3 position vacuum assisted
filtering station using 5.0 .mu.m polytetrafluoroethylene coated
filter paper (available from Osmonics Inc., Cat #Z50WP04750). The
filtrated fractions are dried overnight in a vacuum oven at
60.degree. C. and weighed on an analytical balance before further
testing.
Melt Strength
[0096] Melt Strength (MS) is measured by using a capillary
rheometer fitted with a 2.1 mm diameter, 20:1 die with an entrance
angle of approximately 45 degrees. After equilibrating the samples
at 190.degree. C. for 10 minutes, the piston is run at a speed of 1
inch/minute (2.54 cm/minute). The standard test temperature is
190.degree. C. The sample is drawn uniaxially to a set of
accelerating nips located 100 mm below the die with an acceleration
of 2.4 mm/sec.sup.2. The required tensile force is recorded as a
function of the take-up speed of the nip rolls. The maximum tensile
force attained during the test is defined as the melt strength. In
the case of polymer melt exhibiting draw resonance, the tensile
force before the onset of draw resonance was taken as melt
strength. The melt strength is recorded in centiNewtons ("cN").
Stress-Relaxation-Recovery Behavior for Compositions at 100%
Applied Strain
[0097] This test is taught in WO 1992/020534 A1 and W02002/064674
A2 and has been used previously as a measure of conformability of
films. In this test, an ASTM D1708 dog-bone micro-tensile sample is
cut from the compression molded sheet or the extruded sheet. In
step 1 of this test, the sample is stretched to 100% strain at the
rate of 500%/min on an Instron. In step 2 it is held in place at
the 100% strain for 5 minutes during which the stress relaxes. At
the end of 5 minutes, in step 3 the cross-head is reversed to allow
the film to retract to measure the recovery or the permanent set.
The stress at a time t is normalized by the stress at the beginning
of the stress-relaxation step and is plotted as a function of time
over 5 minutes to monitor the fraction of retained load.
Tensile Strength and Elongation
[0098] Tensile strength and elongation at break was measured per
ASTM D 1708 using an Instron 5564 fitted with a 1 kN capacity load
cell and pneumatically actuated grips. A strain rate of 500%/minute
was used.
25% Hysteresis Testing
[0099] Hysteresis testing was performed using ASTM D1708
micro-tensile samples. Specimens were stretched to 25% strain and
returned to 0% strain for two cycles at 100%/min. Permanent set was
defined as the onset of positive load during extension in the
second cycle. This method has been adapted from the test method
described in WO9220534A1.
EXAMPLE 1
Compositions Suitable for Tapes
[0100] Formulations A-D are made by compounding the components in
the amounts shown in the below table. A Banbury mixer is employed
for the compounding. After compounding the formulations are
extruded as tapes on a 3/4'' single screw Haake extruder with a 4''
wide coat hanger die.
TABLE-US-00001 TABLE 1 Formulations A-D Density Tg (g/cc) (.degree.
C.) A B C D Escorez** 5637 1.1 78 32.10 36.40 37.80 33.30 VERSIFY
.TM. 0.876 -25 47.1 2200 VERSIFY .TM. 0.866 -28 42.8 2300 DE
2400.01 0.858 -31 40.7 OBC 1 0.877 -60 39.3 Calcium 2.83 -- 19.8
19.7 20.4 26.4 carbonate FilmLink 400 Ampacet Blue 0.87 221 0.9 1.1
1.1 1.0 Masterbatch Total 100 100 100 100 Fraction of 0.59 0.54
0.52 0.54 Polymer/ (Tackifier + Polymer)
[0101] VERSIFY 2200, VERSIFY 2300 and DE2400.01 are P/E elastomers
and plastomers available from The Dow Chemical Company. Escorez
5600 series tackifiers available from Exxon Mobil are very light
colored aromatic modified cycloaliphatic hydrocarbon resins.
Escorez 5637 was selected for its high softening point and its
known compatibility with polyethylene polymers.
[0102] OBC1 is INFUSE 9100 olefin block copolymer available from
The Dow Chemical Company and has a melt index of 1.0.
[0103] The retained load vs. time, recovery on retraction as
measured via the stress-relaxation recovery method discussed above,
stress vs. strain and hysteresis were measured for formulations A-D
above. These were compared to a 3M Super 88 f-PVC tape. The results
are shown in FIGS. 1, 2, 3 and 4 respectively. The results indicate
that the formulations exhibit comparable or better performance to
tapes made with materials such as f-PVC.
[0104] Specifically FIG. 1 shows the normalized stress over 5
minutes for the incumbent f-PVC control (3M Super 88) on ambient
conditions (about 21.degree. C., 50% relative humidity) stretching
the samples to 100% strain at 500%/min and monitoring the stress
relaxation over the next 5 minutes. All four inventive formulations
(A-D) show similar stress-relaxation characteristics to the
control. The fraction of retained load at 5 minutes for the four
formulations is 0.4 which is nearly identical to the f-PVC control.
The crosshead is reversed to allow the film to retract and FIG. 2
shows the set. The higher the set, the lower the recovery and lower
the tendency to debond. In contrast, neat polyethylene copolymers
often have 65%, 35% and 20% set for the 9, 12 and 15 wt % ethylene
content samples and usually show a retained load fraction close to
0.6.
[0105] In addition, f-PVC films undergo affine deformation and do
not show a necking and yielding behavior in their stress-strain
curves. FIG. 3 shows that the formulations A and B that are based
on DP 2200.01 and DE 2300.01 respectively have a yield point and
undergo non-uniform deformation. Some applications that use f-PVC
may be able to tolerate a yield point and additional information
should be gathered when using formulations that show a yield point
in the stress-strain curve. However, formulations based on OBC and
DE 2400.01 do not exhibit a yield point and undergo uniform affine
deformation, often a key performance criteria in some applications.
Permanent set measures in the 25% Hysteresis test for f-PVC tapes
is 4% whereas for formulations with DE 2400.01 and OBC it is 5-6%.
This difference is within the typical uncertainty of the
measurement and may be statistically insignificant. Unlike neat
polyethylene copolymer resins that show nearly overlapping
extension and retraction curves implying lower hysteresis and hence
lower conformability, formulations of polyethylene copolymers and
OBC with tackifier and filler advantageously show significant
hysteresis similar to f-PVC based tapes.
[0106] Higher stress relaxation means that the polymer exhibits
greater decrease in force over time. This is desirable in
applications requiring greater comformability. Typical examples
include but are not limited to signage, drapes, bandages,
protective covers, pouches, intravenous liquid containing bags,
floor covering, and tiles.
EXAMPLE 2
Compositions Suitable for Ignition Resistance Applications
[0107] Formulations 1-4 are made by compounding the components in
the weight percentages shown in the below table. A Banbury mixer is
employed for the compounding. After compounding the formulations
are pelletized using an under-water pelletizer and compression
molded down to a thickness of 5-7 mil. The compression molder is
set to 175.degree. C., a pressure of 2000 psi for 3 minutes,
followed by 50,000 psi for 8 minutes, and 50,000 psi @ 15.degree.
C. to cool for 1-2 minutes. Regions of this sheet with a consistent
thickness of .about.6 mil are used for physical testing.
TABLE-US-00002 TABLE 2 Formulations 1-4 Density 1 2 3 4 (g/cc) (wt.
%) (wt. %) (wt. %) (wt. %) OBC 1 0.877 16.45 14.45 20.35 OBC 2
0.877 16.45 Eastotac H100 R 1.04 17.55 17.55 17.55 13.65 Magnesium
2.42 60.00 60.00 60.00 60.00 Hydroxide FR20S10 Zinc stearate 1.09
0.40 0.40 0.40 0.40 Fusabond MN 493 0.87 5.00 5.00 5.00 5.00
MB50-002 0.94 2.00 Irganox 1010 1.15 0.60 0.60 0.60 0.60 Density of
1.49 1.49 1.49 1.48 formulation
[0108] Fusabond MN493, is a .about.1 wt % maleic anhydride grafted
ethylene-octene copolymer from DuPont with a density of 0.87
g/cm.sup.3 and Melt Index of 1.0 g/10 min Zinc Stearate is supplied
by Alfa Aesar. MB50-002, supplied by Dow Corning, in pellet form
comprises of 50% of an ultra-high molecular weight
polydimethylsiloxane polymer dispersed in low-density polyethylene
(PE). Eastotac* H100R from Eastman Chemicals is used as the
tackifier. This resin is a partially hydrogenated aliphatic resin
and is chosen for its compatibility to OBCs. Eastotac* H100R has a
glass transition temperature of 44.degree. C., a ring and ball
softening temperature of 100.degree. C., a density of 1.04 g/cc,
M.sub.n 450 g/mol, and M.sub.w 1050 g/mol. OBC2 is INFUSE 9100
olefin block copolymer available from The Dow Chemical Company and
has a 0.5 Melt Index.
[0109] The stress vs. strain curves, retained load fraction,
recovery on retraction and hysteresis are measured for formulations
1-4 using similar method as above. The results are shown in FIGS.
5-8 respectively. The results indicate that the formulations 1 and
2 exhibit better stress relaxation, similar recovery and permanent
set while having acceptable tensile strength and elongation for
most applications disclosed.
EXAMPLE 3
Compositions Suitable for Ignition Resistance Applications
Comprising LDPE or Modified Olefin Multi-Block Interpolymer
[0110] Formulations 5-10 are made by compounding the components in
the weight percentages shown in the below table. A Banbury mixer is
employed for the compounding. After compounding the formulations
are pelletized using an under-water pelletizer.
TABLE-US-00003 TABLE 3 Formulations 5-10 Density Tg (g/cc) (K) 5 6
7 8 9 10 Eastotac 1.04 317 15.05 15.05 15.05 15.05 14.3 17.55 H100
R OBC 1 0.877 213 16.45 16.45 16.45 OBC 2 0.877 213 16.45 16.45
13.95 LDPE 662i 0.919 242 2.5 2.5 2.5 3.25 2.5 Magnesium 2.42 -- 60
60 60 60 60 60 Hydroxide FR20S10 Zinc stearate 1.09 -- 0.4 0.4 0.4
0.4 0.4 0.4 Fusabond 0.87 221 5 MN 493 Amplify 0.87 221 5 0 5 5 5 5
GR216 Irganox 1010 1.15 -- 0.6 0.6 0.6 0.6 0.6 0.6 70/30 0.881 212
2.5 OBC/PP 1500/1500 (rheology modified OBC) Density of 1.48 1.48
1.48 1.48 1.48 1.49 formulation
[0111] The rheology modified OBC sample is prepared by first
blending a 0.5 MI OBC OBC 2 and a high melt strength random
copolymer polypropylene DOW DS6D82 with 5.7 wt % ethylene and a MFR
of 7 (2.16 kg, 230 C) in 70:30 ratio and then chemically modifying
the blend using 1500 ppm of peroxide Trigonox 101 and 1500 ppm of
coagent SR350. This rheology modified OBC is found to have a melt
strength of 21 cN at 190.degree. C.
[0112] AMPLIFY GR 216 is .about.0.8 wt % maleic anhydride grafted
ethylene-octene copolymer available from Dow with a density of 0.87
g/cm.sup.3 and Melt Index of 1.0 g/10 min.
[0113] All formulations 5-10 of Example 3 have similar
stress-relaxation, tensile and hysteresis properties as formulation
1 of Example 2 described earlier. FIG. 9 compares the melt strength
of formulations 1 and 2 of Example 2 and formulations 5-10. As
compared to formulation 1 of Example 2 with OBC 1 that has a melt
strength of 4 cN, formulation 5, 6 and 8 with LDPE/rheology
modified OBC compounds yield melt strength values of 5 cN, 7 cN,
and 9 cN, respectively. Formulations 7 and 9 demonstrate melt
strength values of 9 cN and 10 cN, respectively, as compared to
formulation 2 of Example 2 with OBC 2 that has a melt strength of 7
cN. Based on the 1.7.times. improvement in melt strength of
formulation 6 versus formulation 1 of Example 2 and the
.about.1.5.times. improvement in formulation 9 versus formulation 2
of Example 2, Formulation 6 and 9 are expected to be better for
applications that require higher melt strengths. These results
indicate that further melt strength improvements can be made if
needed by addition of more LDPE and/or modified olefin multiblock
interpolymer.
EXAMPLE 4
Flame Performance
[0114] The flame performance of Formulations 1, 3, and 4 of Example
2 and Formulations 5, 7, 9, and 10 of Example 3 is measured using a
cone calorimeter. The cone calorimeter is one of the commonly used
types of fire testing equipment which provides quantitative data
for the flammability of a material under constant external heat
flux. The flammability is measured by the heat release rate (HRR).
As HRR increases, flame spread and flashover increase. Time to
ignition, extinguishment time, total heat release, CO/CO.sub.2
production, and smoke release are some of the critical data that
can be collected from a single cone calorimeter test. A Fire
Testing Technology (FTT) Cone calorimeter at a heat flux of 35
kW/m.sup.2 is used to test flammability of plaques that were
compression molded to a thickness of 0.125'' and measuring 10 cm by
10 cm. In this study, no duplicate or triplicate measurements are
done. Single burn data are obtained for each sample for comparison
purposes. Once the material ignites, the time it takes to reach the
peak heat release (is a good indicator for comparing samples in
terms of burning rate. In this case, the sample with the least
amount of tackifier formulation 4 shows the longest time to peak
heat release rate. The sample also burns the longest before
extinguishment. Addition of the silicone masterbatch in formulation
3 has a minimal effect on the flammability characteristics. A
comparison of formulation 1 with formulations 5, 7, and 9 indicates
that the presence of the LDPE in the latter formulations seems to
slightly reduce the peak heat release rate by stabilizing the char
structure. This is evident by the extinguishment times for these
samples as compared to the control 1 formulation. The table below
lists the time to ignition, time to peak heat release, time for
extinguishment, and the peak heat release rate. Advantageously,
these results are comparable to non-halogen flame retardant
formulations based on polyolefins, known to those skilled in the
art.
TABLE-US-00004 TABLE 4 Heat Release t(ignition) t(end) Tpeak Rate
(peak) (sec) (sec) (sec) (kW/m2) Formulation 1 46 271 100 318
Formulation 3 50 197 90 284 Formulation 4 69 419 130 306
Formulation 5 38 196 80 299 Formulation 7 37 186 76 296 Formulation
9 42 188 82 288 Formulation 10 35 200 70 298
EXAMPLE 5
Varying Level of Tackifier
[0115] Formulations are made by compounding the components in the
weight percentages shown in the below table. A small 250 g Haake
Bowl is employed for the compounding.
TABLE-US-00005 TABLE 5 Formulations 11-15 Density (g/cc) 11 12 13
14 15 Eastotac 1.04 11.00 8.00 6.00 22.00 15.05 H100 R OBC1 0.877
19.32 21.84 23.52 10.08 16.45 OBC2 0.877 0.00 0.00 0.00 0.00 0.00
LDPE 662i 0.919 3.68 4.16 4.48 1.92 2.5 Magnesium 2.36 60.00 60.00
60.00 60 60 Hydroxide FR20S10 Zinc stearate 1.09 0.40 0.40 0.40 0.4
0.4 Fusabond 0.87 5.00 5.00 5.00 5 5 MN 493 Irganox 1010 1.15 0.60
0.60 0.60 0.6 0.6 Tackifier: wt/wt 0.5 0.3 0.2 1.8 0.8 Total
Polymer Density of 1.46 1.45 1.44 1.50 1.47 formulation
[0116] The load vs. strain and normalized stress vs. time and
recovery on retraction are measured for formulations 11-15 above.
The results are shown in FIGS. 10-12. The results indicate
surprising and unexpected properties for a ratio of polymer to
tackifier of from about 50 to about 70%.
[0117] For formulations 11 to 15, the ratio of LDPE to OBC 2 is
kept nearly constant as is the filler content, but the amount of
tackifier is varied to determine the influence of the amount of
tackifier on the physical properties. The weight fraction of
(OBC+LDPE)/(OBC+LDPE+tackifier) is reported as percentage of
polymer in the legend of FIG. 13. FIG. 13 shows tan 6 as a function
of temperature for formulations 11 through 14 as compared to the
control formulation 1. The sample with the least % of polymer
(formulation 14) tends to shift the glass transition temperature
closest to room temperature or more f-PVC like behavior.
EXAMPLE 6
[0118] Using raw materials (Table 6), compositions (Table 7) were
made. Corresponding mechanical properties are shown (Table 8). Of
note was the choice of a surface treated filler (Filmlink 400
available from Imerys Performance Minerals), a calcium carbonate.
As can be seen, the inventive formulations were able to achieve
high stress relaxation performance equal to or higher than
comparative sample L* (a f-PVC film from a commercially available
f-PVC based bandage marketed under the Band-Aid tradename by
Johnson & Johnson Corporation). Though not limited by theory,
it is thought that the selection of a surface treated filler
enables debonding which produced a breathable structure upon
stretching due to formation of microvoids. Such a structure is
thought to be advantageous for wound care applications to manage
moisture for the benefit of improved skin health.
TABLE-US-00006 TABLE 6 Components MFR Crystal- or MI Designa-
Density Ethylene linity (g/10 Tg Components: tion (g/cm.sup.3) (wt.
%) (wt. %) min) (.degree. C.) Regalite T1 0.99 n/a -- n/a 50* R1100
Regalite T2 0.98 n/a -- n/a 73* R1125 PBEP P/E-1 0.866 15 7.3
2.sup.a -18 INFUSE OBC3 0.887 -- 24.9 5.sup.b -50 9530 OBC INFUSE
OBC4 0.866 -- 8.8 5.sup.b -60 9507 OBC .sup.adenotes melt flow rate
measured at 230.degree. C. and 2.16 kg for polypropylene (ASTM D
1238-00) .sup.bdenotes melt index measured at 190.degree. C. and
2.16 kg for polyethylene (ASTM D 1238-00) `n/a` denotes not
available
TABLE-US-00007 TABLE 7 Formulations T1 T2 P/E-1 OBC3 OBC4
CaCO.sub.3* Formulation (wt. %) (wt. %) (wt. %) (wt. %) (wt. %)
(wt. %) 27 25 75 28 25 75 29 25 75 30 25 75 31 25 75 32 25 75 33
12.5 37.5 50 34 12.5 37.5 50 35 12.5 37.5 50 36 12.5 37.5 50 37
12.5 37.5 50 38 12.5 37.5 50 *denotes calcium carbonate Filmlink
400 available from Imerys Corporation (Roswell, GA, USA)
TABLE-US-00008 TABLE 8 Mechanical Properties Example: *L 27 28 29
30 31 32 33 34 35 36 37 38 Tensile 2% Sec 51 4.3 22 6 4.4 28 7.2 60
98 38 82 144 47 Mod (MPa): Stdev -- 0.5 2 0.9 0.6 1 0.8 4 9 0.5 4 4
9 Elongation 246 1210 1222 2500 1280 1055 2020 1400 609 2200 25 274
1000 at Break (%): Stdev -- 40 40 100 20 9 20 40 70 200 1 4 100
Tensile 18.6 6.6 13 5.2 9 14 6 2.5 5.6 2.4 2.1 6.4 3.8 Strength MPa
Stdev 0.5 1 0.3 0.3 0.5 0.1 0 0.4 0.3 0.1 0.1 0.1 25% Hyst Set (%):
4 3.1 3.9 3.3 3.03 4.15 3.5 6.1 6.5 4.7 6.7 5.8 5.3 Stdev 0.01 0.1
0.1 0.3 0.02 0.02 0.1 0.3 -- 0.3 0.3 0.3 0.3 Stress- Stress @ 11.39
0.94 2.5 0.77 1.04 3 0.87 1.2 4.5 1.4 1.6 6.29 3.1 Relaxation 100%,
0 (Condition min (MPa): B, Ambient) Stdev 0.02 0.02 0.8 0.01 0.03
0.1 0.01 0.1 0.1 0.1 0.1 0.04 0.2 Stress @ 3.53 0.59 1.68 0.548
0.66 1.9 0.61 0.37 1.8 0.51 0.46 2.66 0.9 100%, 5 min (MPa): Stdev
0.031 0.01 0.02 0.007 0.01 0.1 0.01 0.04 0.1 0.03 0.01 0.01 0.1
Stress- 69 37 32 28.6 36 37 31 69 61 63 72 57.8 69 Relaxation (%):
Stdev 0.6 1 10 0.5 1 2 1 8 4 4 4 0.5 6
* * * * *