breathable polyurethane membranes for textile and related industries
TRANSCRIPT
Breathable polyurethane membranes for textile and related industries
George Robert Lomax
Received 6th March 2007, Accepted 8th May 2007
First published as an Advance Article on the web 22nd May 2007
DOI: 10.1039/b703447b
This Application article briefly reviews the science behind so-called ‘‘breathable’’ coatings and
films, designed originally for foul-weather garments. These materials form continuous polymer
layers over a textile substrate, which are impermeable to liquids such as rainfall and yet transmit
water vapour emitted from the body. Some bear many similarities to dense membranes used for
ultra-filtration and reverse osmosis. Hydrophilic polyurethanes containing poly(ethylene oxide),
PEO-PUs, form a distinct class that straddle the ill-defined boundaries between conventional
macromolecular chemistry, nanotechnology, biomimetics and smart materials. The unique
properties and bio-compatibility of PEO provide further opportunities for these polymers in
diverse areas such as packaging, medical devices, controlled-release systems, hydrogels,
electronics, and biosensors.
1. Introduction
Water vapour-permeable polymer membranes have been used
in sports apparel, fashion rainwear and protective workwear
for more than thirty years.1,2 Their main application is in
waterproof, breathable fabrics (WBFs) for anoraks, over-
trousers, survival suits etc., which help to alleviate problems
of heat build-up and condensation as the wearer becomes
more active.3 Increasingly therefore, WBFs play an important
role in outdoor clothing systems based on interactive layering
and total moisture-management principles.4,5 The aim here is
to provide the best possible compromise between comfort
and protection, under the widest range of activities and
climatic conditions. Non-apparel uses include shoe panels
and inserts, tents, bivouac bags, horse blankets, boat
tarpaulins and medical items such as surgeons’ gowns, drapes,
bodily fluid-proof and anti-allergy mattress covers, and wound
dressings.6
Membranes used in WBFs are typically 10–30 mm thick, and
can discriminate between water droplets (rain or other forms
of atmospheric precipitation, diameters .100 mm) and
moisture vapour or perspiration (individual water molecules,
y0.3 nm diameter), essentially on the basis of size.7 They fall
into two main categories: microporous membranes that have a
clearly visible system of holes and interconnected passage-ways
and hydrophilic membranes that do not, Fig. 1. In some types
of WBF, these two structures are combined.8
Two- and three-layer WBFs are manufactured as con-
tinuous rolls, typically 1.5–2.0 m wide and 100–5000 m long,
by well-established techniques of direct coating (with solu-
tions, dispersions and molten compounds), transfer coating
using siliconised release papers or belts, and film lamination.6,9
Tightly woven polyester and polyamide fabrics are the normal
substrates, increasingly made from textured yarns that
simulate more luxurious natural fibres. It is fair to say that
some of the earliest 2-layer garments lacked finesse. Often, the
WBF was relatively stiff and crackly, they had stitched seams
that were visible and prone to leakage, and they were unlinedBaxenden Chemicals Ltd, Applied Chemicals Division, Union Lane,Droitwich, UK WR9 9BB. E-mail: [email protected];Fax: +44-1905-794002; Tel: +44-1905-794795
George Robert Lomax
Robert Lomax holds B.Sc. andPh.D. degrees in chemistryfrom the Victoria University ofManchester. In 1979 he joinedShirley Institute, Didsbury andworked on various topics, suchas novel hydrophilic polymers,and studies on fabric wicking,absorbency and breathability.From 1990 onwards, he hasbeen employed by BaxendenChemicals in PU applications,research and technical salesroles, and is currently BusinessDevelopment Manager.
Fig. 1 SEMs of breathable membranes used in WBFs: (a) section
through an asymmetrically porous PU coating on nylon taffeta fabric
(61 800 magnification); (b) section through a non-porous, hydrophilic
PU coating on polyester/cotton fabric (6550), indicating the
successive coating layers.
APPLICATION www.rsc.org/materials | Journal of Materials Chemistry
This journal is � The Royal Society of Chemistry 2007 J. Mater. Chem., 2007, 17, 2775–2784 | 2775
Publ
ishe
d on
22
May
200
7. D
ownl
oade
d by
Uni
vers
ity o
f W
este
rn O
ntar
io o
n 31
/10/
2014
16:
20:2
3.
View Article Online / Journal Homepage / Table of Contents for this issue
so that the polymer membrane could come into direct contact
with the skin. Since the 1980s, technologies for incorporating
membranes into fabrics and garments have evolved dramati-
cally,1 see Fig. 2. Nowadays, their aesthetics (tactility, handle,
drape and visual appearance) are minimally impaired, e.g. in
configurations Fig. 2(d), (e), or can at least be offset against
cost and customer choice. Inner linings help wicking of
perspiration, and take away the ‘‘wet cling’’ sensation of
membranes against skin. Optionally, the exposed membrane
surface can be bonded to e.g. lightweight tricot or insulating
materials to give 3-ply laminates, Fig. 2(g), which were first
developed for top-end sports and fashion wear, and are now
routinely used in high-visibility workwear.
2. Water vapour diffusion through membranes
It must be noted at this point that breathability testing of
WBFs is fraught with controversy and confusion.8,10 This
applies particularly to evaluation of commercial fabrics in the
laboratory, and extends to wearer trials of garments in climatic
chambers or in the field. The basic problem stems from the
difference in water vapour transport mechanisms between
microporous and hydrophilic layers, exacerbated by swelling
effects in the latter. However, it is compounded by the desire
amongst specifiers, clothing manufacturers and end-users to
find a universal test method which simulates practice in all
respects. So far, this has proved to be a fruitless task.
2.1 Fundamentals
Diffusion of a substance through a layer is described by Fick’s
1st and 2nd Laws, which relate to the steady state and non-
steady state condition, respectively.11 Fick’s main hypothesis
states that the rate of transfer through unit area of a section,
F(x), is proportional to the concentration gradient measured
normal to the section, i.e.
F(x) = 2D(hc/hx) (1)
where c is the concentration of diffusing substance, x is the
space co-ordinate normal to the section and D is the diffusion
coefficient. The water vapour transmission (WVT) properties
of WBF membranes can be derived from eqn (1) using a
different proportionality constant (k) to relate WVT with the
pressure difference across the membrane surfaces (p1 2 p2) and
its thickness d.12
m/At = k(p1 2 p2)/d (2)
Many recognized breathability tests simply measure the
amount of water vapour (m) passing through a fixed area of
material (A) over time period (t) by gravimetry. The WVT rate
(m/At) obtained under steady state conditions has an SI
quantity of kg m22 s21, although the trivial unit g m22 day21
is most widely recognised by this industry.
2.2 Breathability testing: understanding the dilemma
One major concern with WVT testing is that results quoted do
not take the magnitude of the driving force, (p1 2 p2), into
consideration. More often than not, values for p1, p2 at each
surface of the membrane are guesstimated rather than
accurately measured. Hydrophilic membranes can show strong
and unusual dependences on applied relative humidity and
temperature, which determine p. These two factors alone make
comparing data obtained from different sources unreliable.
For instance, it is possible to generate apparent 40-fold
increases in WVT of WBFs solely by changing the set of
‘‘standard’’ test method conditions.8 During the WBF
technology boom of the 1980s, breathability testing was used
indiscriminately and often unscrupulously to claim higher and
higher WVT rates for marketing purposes. To a certain extent,
this one-upmanship mentality still remains.
An alternative approach is to visualise the membrane as a
barrier to water vapour diffusion, rather than a transmitter.12
In this case the reciprocal quantity of water vapour resistance
(WVR) is measured. The limiting WVR is zero implying that
the membrane is infinitely breathable, but of course this can
never be achieved with a barrier layer of finite thickness. There
are two main advantages in measuring WVRs: (a) the pressure
gradient is taken into account, and (b) the data are additive,
which is useful for assessing the overall resistance of real and
hypothetical clothing assemblies if the R values of individual
layers are already known.8 On the other hand, WVR is a more
difficult concept for consumers to grasp, and the various units
(e.g. mm still air, m2 Pa W21 and s m21) are illogical compared
with transmission rates.
Fig. 2 Schematic diagram of outer-garment constructions incorporating WBFs: (a) basic 2-layer fabric with coating on inside, water repellant-
treated outer surface; (b) 2-layer, coating on outside; (c) 2-layer plus loose liner fabric; (d) loose outer fabric plus scrim-supported membrane (drop
liner); (e) drop liner insert; (f) double membrane system, e.g. Dual ProtectionTM; (g) pictogram showing breathability and weatherproofness of a
3-layer laminate.
2776 | J. Mater. Chem., 2007, 17, 2775–2784 This journal is � The Royal Society of Chemistry 2007
Publ
ishe
d on
22
May
200
7. D
ownl
oade
d by
Uni
vers
ity o
f W
este
rn O
ntar
io o
n 31
/10/
2014
16:
20:2
3.
View Article Online
WVR data are reliable for air-permeable membranes and
base fabrics, but less so for hydrophilic polymers, which are
strongly dependent on surrounding water vapour pressure or
water content, e.g. Fig. 3. True microporous components such
as (C) and (D) have low WVRs that barely change with
relative humidity (RH) at a given temperature.13 Conversely,
hydrophilic WBFs e.g. (A) are not especially breathable at low
humidities, but their WVRs decrease as the RH rises. The
shape and dip in the curve, especially in the 70–100% RH
range, depends on the hydrophilicity of the polymer, and
therefore on its own unique chemical composition. The net
outcome is that hydrophilic membranes respond to a build up
of water vapour inside a clothing assembly by swelling, thereby
becoming more breathable. This ‘‘sense and react’’ mechanism
can be classed an intelligent textile response,14 and similar to
the way human skin and biological polymers such as keratin
and cellulose behave. As might be expected, hybrid fabrics
containing both microporous and hydrophilic layers such as
type (B) show intermediate properties. Another feature in
Fig. 3 is that the ranking order observed at low–medium
humidities (A , B , C) is reversed at very high humidities,
and this exemplifies the problems with testing breathability
under different RH conditions.
Even today, the situation regarding breathability testing of
textiles has not been satisfactorily resolved. There are at least
three International Standards that may apply to WBFs, each
using different test conditions and expressing results in a
completely separate way.15 The ‘‘sweating hot-plate’’ method
or skin model (ISO 11092:1993) evolved from research into the
effects of clothing on human thermoregulation under varying
workloads, and yet the Standard test condition (35 uC;
RH 100% A 40%) is utterly meaningless for foul-weather
outer garments worn in real-life situations.
2.3 Breathability: demands versus reality
Thermoregulation involves a complex, interactive set of
physiological responses to balance metabolic heat production
(M) under workload (expended energy, Pw) with those heat
losses necessary to maintain a body core temperature (TC) of
approximately 37 uC.16 Fluctuations around the TC cannot be
tolerated for long before discomfort sets in, followed by
mental confusion, disorientation, serious illness and in extreme
cases, death.
Heat loss through the clothing occurs mainly by combined
dry processes (conduction, convection and radiation) and wet
processes (insensible perspiration and sweat), eqn (3).
M{Pwoutput
~ (HcondzHconvzHrad)dry loss
z
(HinsenszHsweatzHresp)wet loss
+ DSdebt
(3)
The relative importance of each heat loss component varies
depending on the workload and ambient atmosphere, the
individual’s metabolism and the clothing assembly worn. A
sedentary person has a typical heat output of about 100 W, a
respiratory heat loss (Hresp) of 25 W and a background water
vapour loss through the skin (Hinsens) of 250–300 g m22 day21,
equivalent to cooling of 12–15 W. Dry heat losses account for
the remainder (ca. 60 W), and the wearer usually remains
comfortable in light clothing (for example underwear, shirt
and trousers). Heat output under workloads, however, can be
as high as 1000–1250 W, i.e. similar to a one-bar electric fire,
but these levels of exertion can only be sustained for short
periods of time. Sweating is a particularly efficient cooling
mechanism in this case, because water has a very high latent
heat of evaporation (0.672 Wh g21 at 35 uC). This implies that
a sweat rate of 1 kg h21 provides 670 W cooling, but only if all
sweat evaporates away from the body. Clothing interferes by
trapping moist air, often resulting in condensation forming
somewhere within the textile layers. Some activities, e.g.
fire-fighting, produce even greater sweat rates, but coping
with 1 kg h21 is a reasonable target for moisture management
purposes.17
The heat debt, DS in eqn (3), is zero when heat output and
heat loss are in dynamic balance, i.e. the subject is in a state of
thermophysiological comfort. The case where sustained heat
output exceeds heat losses (+ve DS) or vice versa (2ve DS), has
potentially serious implications, which could lead to
hyperthermia or hypothermia, respectively. Someone under-
taking arduous exercise in foul-weather or cold climates may
encounter any one or all of these DS conditions during their
normal course of activity.
The mean WVT properties of a completely sealed survival
suit would have to be #10 000 g m22 day21 to satisfy a target
of Hsweat = 670 W, DS = 0, but this can only be achieved with
driving forces (p1 2 p2) in the order of several thousand Pa (by
eqn (2)).18 Such high pressure gradients are rarely achieved in
adverse foul/cold weather climates.
Fig. 4 shows water vapour pressure (p) as a function of
typical ambient temperatures and relative humidities, and can
be used to illustrate the difference between theoretical (skin
model, ISO 11092), standard textile test and real conditions.18
The isobars close up rapidly with decreasing temperature, but
even below 0 uC ice has a small and measurable p. This last
point is important, because in cold climates water can be
present in all three phases inside the clothing,19,20 and must be
dealt with to avoid chill effects. Most breathability tests are
carried out under isothermal conditions to avoid condensation
phenomena, and under high pressure gradients to allow short
Fig. 3 Schematic diagram showing water vapour resistance (WVR)
of WBF components with changing relative humidity (RH): (A)
hydrophilic coated fabric; (B) microporous coated fabric with
hydrophilic top coat; (C) pure microporous coated fabric; (D)
ePTFE membrane of 30 mm thickness.
This journal is � The Royal Society of Chemistry 2007 J. Mater. Chem., 2007, 17, 2775–2784 | 2777
Publ
ishe
d on
22
May
200
7. D
ownl
oade
d by
Uni
vers
ity o
f W
este
rn O
ntar
io o
n 31
/10/
2014
16:
20:2
3.
View Article Online
test periods. Neither test criterion simulates what happens in
practice for outer garments.18 For instance, the ISO test
methods15 operate respectively at 35, 23 and 20 uC, generating
nominal pressure gradients of 3093, 2168, and 818 Pa.
However, the WBF membrane is usually the next outermost
layer in a foul-weather clothing assembly, see Fig. 2, and its
operating temperature is close to ambient, not skin tempera-
ture (average 33 uC) as often mistakenly assumed. The actual
driving force for expelling perspiration (p1 2 p2) is therefore
considerably lower than for standard laboratory test condi-
tions. Temperate climates such as the UK have average
humidities in the range 70–95% and rainfall temperatures
of 2–8 uC, and the maximum pressure gradient across a
WBF membrane is only a few hundred Pa under these
conditions, Fig. 4. This means that optimistic target values
of 10 000+ g m22 day21 are unattainable, but through no
fault of the material. When (p1 2 p2) = 0, the membrane
appears to stop functioning, but it is actually in a state of
dynamic equilibrium where the vapour flows in each direction
are equal. WBFs must therefore be regarded as only one
component in moisture-management systems, where internal
clothing acting as instantaneous wicking layers (underwear) or
moisture buffer zones (mid-layers, piles, fleeces), and design
features that provide ventilation are equally, if not more,
important.5,18
WVR data afford a clearer comparison of WBFs with other
clothing layers than WVT rates, e.g. Fig. 5. The left-hand
dotted lines represent categories which relate to breathability
requirements for outer workwear garments.18,21 WBFs with
WVRs less than 20 m2 Pa W21 fall into the highest category,
Class 3 of EN 343 Specification,22 and many are equivalent to
normal clothing layers. In stark contrast, earlier types of
coated and wax-impregnated fabrics, Fig. 5(f) have much
higher resistances (200–1000 m2 Pa W21) and are notoriously
prone to condensation forming on their internal surfaces.3 The
right-hand dotted lines show further subdivisions (at 13 and
6 m2 Pa W21) used by the leading research organisation in this
field, Hohenstein Institute, to classify ordinary clothing layers.
Future revisions of the EN Standards may well adopt more
stringent pass levels for Class 3 materials, reflecting the
continual improvement in WBF performance.
3. Microporous membranes
Membranes with porous structures can be formed in numerous
ways, such as phase separation of unstable solutions, salt
extraction, mechanical frothing, and fibrillation of solid films.
The polymers employed include diverse polyurethanes (PUs),
acrylics, polyolefins and polyfluorocarbons, and these older
technologies have been extensively reviewed.23
A common feature of all microporous membranes is their
naturally dull, white appearance resulting from diffraction of
light through the surface cavities. The asymmetric structure,
Fig. 1(a), is made by the wet coagulation process developed in
the 1960s for PU synthetic leathers. As a general guideline,
the surface pores should be no larger than 1 mm to withstand
penetration by liquid water and the porosity should be as
high as possible to maximise WVT. Even so, the surface pores
can become contaminated with surfactants e.g. present in
washing powders, dry cleaning fluid, sun tan lotions, and skin
exudates which compromises their waterproof qualities. It is
now common practice to apply a thin, hydrophilic sealing
layer to a microporous membrane to overcome this potential
deficiency.8
Expanded poly(tetrafluoroethylene), ePTFE, is used in the
best-known WBFs, the Gore-TexTM laminates, with publicity
claims that there are more than 9 billion pores per square inch
of film. The ePTFE membrane, Fig. 6(a), is formed by biaxial
stretching and annealing at high temperature,24 and comprises
a 3-D network of predominantly crystalline nodes connected
by amorphous fibrils, typically with a porosity of 80% and
symmetrical pores of ca. 0.2–0.5 mm.
3.1 Still air layers and the air permeability mechanism
Normal textile structures, including tightly-woven fabrics such
as Fig. 6(b), have dead spaces between fibres and yarns
which are permeable to all constituents of air. Microporous
membranes also rely on the ability of water vapour to diffuse
through ‘‘still’’ air trapped in the vast labyrinthine structure.
Stabilised air layers act as protective heat buffers, because still
air has exceptionally low thermal conductivity (0.024 W mK21
at 20 uC) compared with water (0.6 W mK21), textile polymers
(0.1–0.5 W mK21) and other solid materials. The textile
Fig. 4 Variation of p with temperature and relative humidity.
Fig. 5 Typical WVR ratings for fabrics:21 (a) 2- and 3-layer ePTFE
laminates and uncoated microfibre; (b) microporous PU coated; (c)
hydrophilic PU coated and laminated; (d) low-swell PU system; (e)
non-breathable PU coated; (f) PVC, waxed, rubber etc. coated/
laminated; (g) underwear, light clothing layers; (h) heavy clothing
layers, fleece, pile etc.
2778 | J. Mater. Chem., 2007, 17, 2775–2784 This journal is � The Royal Society of Chemistry 2007
Publ
ishe
d on
22
May
200
7. D
ownl
oade
d by
Uni
vers
ity o
f W
este
rn O
ntar
io o
n 31
/10/
2014
16:
20:2
3.
View Article Online
industry makes full use of this property for clothing and
bedding assemblies.25 ‘‘Warm’’ natural materials such as silk,
certain vegetable fibres (e.g. kapok), arctic animal furs, eider
and penguin down, have exceptionally high specific surface
areas (SSAs) that help stabilise air layers through viscoelastic
drag. Many creatures adapt to changing weather conditions by
varying the effective thickness of the surrounding air layer, for
example, by raising fur or puffing out feathers, and homo
sapiens can do the same by donning and doffing clothing
layers as required. Synthetic fibre developments that mimic
natural structures include hollow fibres, multilobal and
crenellated fibres, microfibre piles and fleeces and increasingly,
nanofibres.5 The internal structures of microporous mem-
branes also have large SSAs and possess this air-stabilising
characteristic.
It must be emphasised that still air is a poor transmitter of
water vapour as well as heat, which leads to a major comfort
paradox. Measures taken to improve the warmth of cold/foul
weather clothing by increasing still air-layer insulation will
automatically restrict breathability and increase the chance
of moisture build-up and condensation. The implications
are severe at low temperatures because sodden clothing
loses Hcond up to 25 times faster than dry material. Under
wind-free conditions, a naked human body is protected by
an air layer some 8–12 mm thick, which acts as a buffer to
heat and moisture vapour transfer with the environment.
Its effective thickness decreases exponentially with increasing
wind velocity, and this is one element of wind chill factor.
Modern breathable fabrics have equivalent still air thick-
nesses in a similar range (typically 4–10 mm),8 which puts
the high breathability of these materials into perspective
once more.
Fick’s Laws hold if there is no interaction between the
barrier layer and the diffusing substance, i.e. D is independent
of c in eqn (1).11 Diffusion of water vapour into still air is a
well-known Fickian process, where the diffusion coefficient
Dwa has an Arrhenius dependence on temperature (T, uC)
given by Dwa = (2.2 + 0.0147T) 6 1025 m2 s21. This
mechanism is easily demonstrated by measuring the WVR of n
stacked layers (n = 1–5) of hydrophobic, air-filled ePTFE
membranes under steady-state conditions (21 uC).12 The plot
of WVR versus effective film thickness is a straight line passing
through the origin, exactly as predicted by Fick’s 1st Law. The
WVR of a single ePTFE membrane (30 mm) is 0.25 Pa m2 W21
(equivalent to 6 s m21), one of the highest breathability ratings
of any commercial textile layer.
Increasing the polar or hydrophilic nature of the polymer
causes a progressive deviation from such ideal behaviour.
At the opposite end of the spectrum, hydrophilic swelling
membranes have D and d parameters which vary substantially
with c, and Fick’s Laws no longer apply.
4. Hydrophilic membranes based on PEO-PUs
Solid, hydrophilic membranes, Fig. 1(b), are impermeable to
air in textile terms. Instead, they employ a non-Fickian or
anomalous diffusion mechanism, involving transient hydrogen
bonding of water molecules to complementary functional
groups on the polymer chains. It is often described, textually
or pictorially, as a ‘‘molecular stepping-stone mechanism’’ on
swing tickets and in brochures for leisure and workwear
apparel, usually in conjunction with a pictogram such as
Fig. 2(g). Polar groups with hydrogen bond-acceptor sites such
as –OH, –NH2 and –CO2H can be utilised in hydrophilic
polymers.7,23 However, the ether linkage, –O–, with two sets of
lone pair electrons, has several advantages for commercial
breathable systems.26 The latter products are usually based on
copolymers of PEO with alternating ester (e.g. SympatexTM
membranes), amide (e.g. PebaxTM resins) or most commonly,
urethane (e.g. WitcoflexTM coating systems) segments in the
backbone. Interestingly, PEO is unique amongst the lower
polyether homologues in being water soluble, Table 1, which
indicates that hydrophilicity is not simply due to ether linkage
content (% w/w).
Other polyether segments commonly incorporated into PUs
via the corresponding glycols are poly(propylene oxide) (PPO)
and poly(tetramethylene oxide) (PTMEO). The value of n, the
average number of monomer units in the polyether segment,
typically varies from 6–40. Small proportions of PPO or
PTMEO segments are sometimes used in hydrophilic PUs to
reduce swelling,23 improve other properties such as softness
and elastic recovery or modify solubility behaviour. A route to
poly(trimethylene glycol)s from biorenewable raw material has
recently been patented,27 which opens up new possibilities for
PTMO-based PUs and other copolymers.
4.1 Basic composition
Linear PEO-PUs can be formed by the exothermic reaction of
diisocyanates with poly(ethylene glycol)s and difunctional
Fig. 6 Water-resistant structures: (a) SEM of ePTFE membrane
surface showing nodes and fibrils;7 (b) fluorochemical-treated micro-
fibre fabric made from TreviraTM polyester yarns with interstitial pores
of ca. 3 mm.
Table 1 Some properties of polyethers26
Chemical structure Acronym Water-solubleEther content(% w/w)
[CH2–O]n– PMO no 53.3[CH(CH3)–O]n– PAc no 36.4[CH2CH2–O]n– PEO yes 36.4[CH(CH3)CH2–O]n– PPO no 27.6[CH2CH2CH2–O]n– PTMO no 27.6[CH2CH2CH2CH2–O]n– PTMEO no 22.2
This journal is � The Royal Society of Chemistry 2007 J. Mater. Chem., 2007, 17, 2775–2784 | 2779
Publ
ishe
d on
22
May
200
7. D
ownl
oade
d by
Uni
vers
ity o
f W
este
rn O
ntar
io o
n 31
/10/
2014
16:
20:2
3.
View Article Online
chain extenders,28,29 as a melt, in various solvents or with
greater difficulty in water. The fundamental reaction is:
This is an idealized sequence where the PEO soft segments
are incorporated first, step (i), followed by chain extension of
the prepolymer with an equimolar proportion of diol (X = O)
or diamine (X = NH), step (ii). It predicts a perfect array of
alternating hard and soft segments along a molecular chain
where the number of repeat units, m, tends to infinity. In
practice, (a) the reaction stoichiometry is generally more
complicated than 2m : m : m, (b) more than three reactants are
often selected, (c) chain terminators are used to control Mw
and viscosity, and (d) the kinetics of steps (i) and (ii) affect
segment build-up. Consequently, the structure, length and
regularity of the segments, average chain length and therefore
the polyurethane molecular network as a whole are consider-
ably less than perfect.26 With certain diisocyanate–chain
extender (R1 : R2) combinations it is possible to elaborate
the hard segments first, i.e. carry out step (ii) before (i), which
can lead to improved physical properties,28 or use a one-shot
process where steps (i) and (ii) occur simultaneously. The terms
hard and soft correctly suggest that each segment type
contributes different properties in the final membrane.
Structure–property correlations for PEO-PUs have been
reported in the open literature, e.g. reference 30, but the
composition of commercial polymers is normally hidden
within complex patent specifications, or else remains a trade
secret. In order to achieve an acceptable balance between
breathability, waterproofness, swelling and adequate durabi-
lity, the overall PEO content and segment length are best kept
within certain limits, typically 40–60% w/w and n = 12–45.
PEO-PUs with parameters outside this range can be gainfully
used in other, non-WBF applications.
4.2 Some practical aspects of the textile technology
Eqn (2) implies that hydrophilic membranes should be as
thin as possible to maximize WVT, but this is inevitably
limited by manufacturing tolerances, handling considerations
and the conflicting durability and cleaning requirements.
Uniform films for transfer coating and lamination are typically
1.5–2.0 m wide and 15–25 mm thick, although 5–10 mm
PEO-ester films produced by biaxial stretching have appeared
on the market.
By comparison, PEO-PU coatings applied directly onto the
substrate are non-uniform in thickness, because they follow the
surface contours of the base fabric and fill into the interstices
between yarns. Direct coatings have a stratified composition,
Fig. 2(a), and surprisingly complex chemistry. They may also
contain additives such as pigments, flame retardants, slip aids
and matting agents in one or more layers. Base and middle
coat PUs are normally very soft and extensible, and require
crosslinkers to afford adequate ‘‘wet’’ properties, durability
and adhesion promotion to the fabric substrate.26 They are
often based on TDI (commercial blends of 2,4- and 2,6-
diisocyanatotoluene) with PEO contents higher than 50% w/w
and supplied as 45–55% solids in MEK (methyl ethyl ketone)
or blends. Top coats are harder, more abrasion resistant and
less hydrophilic; they are usually manufactured from MDI
(4,49-diisocyanatodiphenylmethane) with lower PEO contents
than base coats and require more powerful solvents (usually
supplied at 30% solids in DMF blends). Crosslinkers are
normally avoided in top coat formulations, because the outer
surface must remain thermoplastic for taping of seams in
finished garments. As each layer is progressively built up, the
solvent is removed and the dried layer becomes the substrate
for the next. This is best carried out in a one-pass operation
and lines with 2, 3 or even 4 coating heads and associated
ovens in tandem are now commonplace. The final consolida-
tion process is usually carried out at higher temperatures to
ensure complete removal of solvents, and crosslinking of the
base-coat polymer before the coated fabric is rolled up.
In contrast to the porous types, hydrophilic coatings are
transparent and glossy, and top coats are usually matted to
give an acceptable surface lustre. Ironically, some coaters
incorporate white pigments into a hydrophilic coating so that
it resembles a microporous system, or perhaps can be passed
off as one in the WBF marketplace. By doing so, high loadings
of pigment can detract from the excellent physical integrity of
the hydrophilic PU, which was one of the main reasons for
their development in the first instance.
4.3 Phase separation and swelling effects in membranes
As the coating or film consolidates, the segmented molecules
undergo phase separation to a lesser or greater extent. It is
initiated by hard segments agglomerating together via intra-
and inter-molecular hydrogen bonding involving urethane
and/or urea groups, Fig. 7.
The excellent physical properties (tensile strength, elonga-
tion, elastic recovery, tear strength etc.) of many PUs rely on
optimal phase separation. This is best achieved using R1, R2
Fig. 7 Phase separation in hydrophilic PEO-PUs:18,26 (a) SEM of
non-porous membrane surface etched with DMF vapour showing hard
and soft contours; (b) highly schematic 2-D diagram of nanophase
structure; (c) ‘‘stick and string model’’ of segmented molecular chain.
2780 | J. Mater. Chem., 2007, 17, 2775–2784 This journal is � The Royal Society of Chemistry 2007
Publ
ishe
d on
22
May
200
7. D
ownl
oade
d by
Uni
vers
ity o
f W
este
rn O
ntar
io o
n 31
/10/
2014
16:
20:2
3.
View Article Online
residues that form linear, compact or symmetrical hard blocks,
which are capable of packing closer together than those
obtained with asymmetrical species. For this reason, MDI-
based polymers tend to have improved physical properties
compared with TDI analogues. In hydrophilic PUs, the hard
segments can be visualised as forming a constraining mesh
around the PEO soft segments, which prevents excessive
swelling or even complete dissolution of the polymer in water.
Crosslinking with e.g. multifunctional isocyanates leads to
covalent bonds forming between adjacent hard segments.26
At higher water vapour pressures, PEO-PU membranes
absorb increasing numbers of water molecules and start to
swell. Condensing water can also be slowly absorbed by the
PEO-rich surface of the polymer membrane, which is an
important and often overlooked advantage over hydrophobic,
microporous types. Bringing liquid water into contact with
the membrane can increase the WVT rate substantially, by a
factor of 3 or more, over the dry state.12 Swelling is therefore
an intrinsic property of these materials,26 and vital for their
modus operandi. It has to be encouraged and yet controlled,
through correct choice of the hard segment constraint (R1, R2),
hard : soft segment ratio and optional crosslinking system.
Base-coat and top-coat polymers typically absorb 70–100%
and 40–70% w/w, respectively when immersed in water at
room temperatures.21
4.4 Effect of temperature on hydrophilicity
PEO homopolymer, PEGs, PEG ethers and other PEO-
containing species show inverse water solubility features with
temperature. This anomaly is also observed when measuring
the WVR or, more conveniently, the swelling properties of
PEO-PU membranes over a range of temperatures.18
For example, Fig. 8 shows the effect of varying PEO content
and chain length on equilibrium water uptake of a series of
PUs (A–D) with constant hard : soft segment ratio (1.66), as
detailed in Table 2. All films clearly become less hydrophilic
with increasing temperature, but the effect is more pronounced
as the size of the PEO nanophase increases (i.e. film A & D)
and becomes more difficult to constrain. Because water is
absorbed exclusively by the soft segment nanophase, the
results can also be expressed as the hypothetical number of
water molecules associating with each ether oxygen atom
(H2O : EO ratio) at a given temperature.31 This provides a
comparative measure of hydrophilicity. Other researchers have
shown that PEO-PUs and PEO itself form stable complexes
with water at H2O : EO ratios of 1 and 3.32–34 Above the
trihydrate level, water molecules in PEO-PUs start to combine
and form clusters within the molecular network,31 which is
detrimental for vapour transport through WBFs.18 Empirical
studies in Baxenden laboratories have also shown that PEO-
PUs with H2O : EO ratios of 2–4 at 20 ¡ 2 uC prove most
suitable for textile membranes.35 Commercial products are
often selected so that an optimum transport condition of
H2O : EO # 3 occurs at typical foul-weather temperatures.18
Film C could fall into this category. Alternative polymers with
ratios below 2 are insufficiently breathable, e.g. D, whilst those
with higher ratios swell too much for practical purposes, B. At
even higher ratios of 7+, such as A, there is an onset of
hydrogel properties where water is retained rather than
transmitted. In the extreme case where H2O : EO tends to
infinity, the polymer becomes water soluble.
4.5 Elucidating the water vapour transport mechanism
During the past decade, fundamental studies have been carried
out on the biologically important PEO molecule that provide
an insight into how hydrophilic PU membranes actually work
at the nano-level. Vapour diffusion through hydrophilic PU
membranes occurs predominantly through the interconnected
PEO soft segments.
Water molecules have a greater hydrogen-bond affinity for
the EO ether oxygen (34–38 kJ mol21) than they have for other
water molecules in clusters (19–23 kJ mol21),36 which may
assist initial absorption into the surface monolayers and
transfer through the membrane under a concentration
gradient. It is now widely accepted that the thermodynamically
preferred conformation of PEO chains (n . 10) is a 72 helix,
formed by a repeating trans–gauche–trans (tgt) arrangement of
C–C–O–C bonds in the backbone,36–38 Fig. 9(a).
There is a striking similarity between the adjacent and next
nearest O–O distances in the 72 PEO helix and those in water
clusters,39 Fig. 9(c). This exceptional stereo-compatibility is
held responsible for the water solubility characteristics of PEO
and many derivatives, and it almost certainly accounts for the
high permeability of PEO-PU textile membranes.18,21 There is
strong supporting evidence for this conjecture. First, the
closest polyether homologues, PMO and PTMO, have
incompatible O–O arrangements (being 0.22 nm and 0.48 nm
apart, respectively) and are not water soluble or hydrophilic.
Secondly, replacing PEO with equivalent PTMEO orFig. 8 Equilibrium water uptake of homologous PEO-PU films.
Table 2 Hydrophilic properties of PEO-PU films A–D (see Fig. 8)a
Film
PEO nanophase H2O : EO ratio at
(% w/w) av. n value 2 uC 35 uC 70 uC
A 72 44 7.29 5.73 3.11B 66 33 4.97 3.81 2.14C 54 22 2.90 2.09 1.07D 44 13 1.18 0.83 0.55a Polymers A–D were prepared from MDI, PEG (of Mw 2000, 1500,1000 and 600 respectively) and butan-1,4-diol (molar ratio 2 : 0.8 :1.2) in a one-shot, 100% solids process, then dissolved in DMF andcast into films.
This journal is � The Royal Society of Chemistry 2007 J. Mater. Chem., 2007, 17, 2775–2784 | 2781
Publ
ishe
d on
22
May
200
7. D
ownl
oade
d by
Uni
vers
ity o
f W
este
rn O
ntar
io o
n 31
/10/
2014
16:
20:2
3.
View Article Online
especially, isomeric PPO segments drastically reduces the
breathability properties of poly(ether-urethane)s.29 Thirdly,
water molecules are thought to form bridges between
adjacent ether oxygens, which help stabilise the helix.40
Empirical and theoretical studies have shown that stretching
a PEO strand in the presence of water alters the spatial
O–O distances, destroys the bridging capability and progres-
sively converts the hydrophilic tgt helix into a relatively
hydrophobic, planar ttt conformation.40–42 The general feature
that PEO species, including the polyurethanes in Fig. 8,
become less hydrophilic with increasing temperature can then
be explained in terms of growing imperfections (random
gauche defects) in the 72 helix, brought about by increased
thermal motion.
The 72 unit can be visualised as a grooved cylinder,36 with its
inside electronegative relative to the outside, due to the
location of the ether lone pair electrons, Fig. 9(d). The
attractive theory that PEO helices might behave as bundles of
nano-capillaries, with water molecules temporarily bonding to
the internal walls, can be discounted because the central
channel is too narrow. A more likely scenario is that water
molecules bond to the outside of the PEO chains, possibly
using the helical groove to form a hydration sheath.36 Taking
the favoured case where H2O : EO # 3, there are only two
hydrogen-bond acceptor sites per ether oxygen, so a third
water molecule must somehow bridge across two already
bound molecules. It is possible to draw several structures for
inter- or intra-chain bridging involving three water molecules
per EO unit, any of which could easily be integrated into a
‘‘stepping-stone’’ mechanism.35
4.6 Low-swell developments
In most garment constructions, the breathable membrane is
located on the inside, partly to protect it from snagging and
abrasion damage whilst the outer fabric surface is treated with
durable water repellants to help shed rainfall, Fig. 2(a),(g).
However, there are other potential applications, for instance in
some types of mattress covers, medical dressings, shoes and
easy-wipe workwear, where the membrane normally forms
the outside layer, Fig. 2(b). Conventional swelling polymers
cannot be used in this case, because they often develop
unsightly wrinkling or water-spotting effects in wet or rainy
conditions, or else are too fragile in the swollen state.
Several approaches have been taken to solve this problem,
but all lead to the inevitable trade-off between dimensional
swelling and breathability.23 Most attention has focused on
modifying the PEO soft segment, for example, by using ABA
or (AB)n copolymers which combine shorter PEO units with
PPO or PTMEO units.
More recently, poly(urethane-urea)s with exceptionally low
water uptakes (typically , % w/w), no perceptible swelling
and acceptable WVRs at lower coating weights have been
introduced for some niche markets. These low-swell polymers
have substantial ether atom contents (15–20% w/w) and are
therefore water vapour permeable,43 yet they are PEO-free and
not hydrophilic in the accepted sense.7 Fig. 10 suitably
illustrates where they fit into the breathability spectrum of
solid polyurethanes used by the textile industries.21 The wedges
were constructed by measuring the WVRs of stacked layers of
appropriate films,35,43 using the modified ISO 15496 test
method previously described.12 By combining low-swell and
hydrophilic chemistries, e.g. using physical blends of the
separate polymers or preparing copolymers with two phase-
separable soft segments, it is possible to develop membranes
with an intermediate balance of properties, Fig. 10(c).
Composite membranes, e.g. tri-layers of polymers with low,
medium and high swell propensity, show interesting aniso-
tropic behaviour,43 with WVT/R properties depending on
the direction of water vapour flow and stacking order. This
promises to be an exciting area for further expansion of
breathable polyurethane technology.
4.7 Crossovers with other technologies
PEO-PUs are already used in, or may be considered for, many
other applications, see Fig. 11, which is by no means an
exhaustive list. These products benefit from one or more of the
following properties, imparted by the PEO segment.
1. Low water content: the moisture regain of PEO-PUs is low
(ca. 1–2%), but still significantly higher than that of non-
breathable PUs. This provides anti-static properties,44 which
Fig. 9 (a) Helical structure of PEO molecule with n = 20;36 (b) 72
helix dimensions (7 EO monomer units per 2 complete turns); (c)
distances between oxygen atoms; (d) cross section through helix.
Fig. 10 Breathability wedges for textile-grade PU membranes:21 (a)
typical non-breathable (water uptake ca. 1–3% w/w); (b) low swell
(1–3%); (c) hybrids of low swell and hydrophilic (10–25%); (d)
hydrophilic top coat (40–70%); (e) hydrophilic base coat (70–100%).
The vertical line represents a nominal 25 mm thickness.
2782 | J. Mater. Chem., 2007, 17, 2775–2784 This journal is � The Royal Society of Chemistry 2007
Publ
ishe
d on
22
May
200
7. D
ownl
oade
d by
Uni
vers
ity o
f W
este
rn O
ntar
io o
n 31
/10/
2014
16:
20:2
3.
View Article Online
can be further improved by incorporating carbon black, metal
powders and organic conductors.
2. Water transport: vapour diffusion has been discussed in
detail, but PEO-PUs also have surface energies that encourage
wetting out and wicking of liquid water.5,18
3. Swelling capacity: these materials behave as hydrogels at
high PEO contents, n values and H2O : EO ratios.33 The 3-D
molecular network can be designed so that the degree of
swelling can be precisely and reproducibly controlled, which is
essential for e.g. drug delivery systems.46
4. Crystallinity: this increases with the size of the PEO phase,
i.e. with chain length or n value.47 Highly crystalline, radial
spherulites may be observed in the soft segments with PEO n
values .60.46 The degree of soft phase crystallinity influences
gas and vapour diffusion, physical properties such as modulus
and tear strength, and the effective glass transition tempera-
ture, Tg, of the polymer. PEO-PUs with relatively high Tgs
(above 10 uC), e.g. DiaplexTM breathable membranes, are
claimed to have WVT properties that change significantly and
advantageously with ambient temperature.48,49 However, their
effectiveness has also been refuted.50
5. Bio- and haemo-compatibility: PEO-rich surfaces are
resistant to protein absorption and blood platelet attachment.
Pendant PEO groups are particularly effective.51
6. Lewis basicity: to a certain extent, PEO segments can be
regarded as open-chain versions of crown ethers, such as
18-crown-6, with chelating and catalytic activity. They can use
the electron donor properties of the oxygen atoms to bind
small metal ions, e.g. Li+ for polymer electrolytes,52 and other
electropositive species.
5. Conclusions
Breathable polyurethanes are an important class of
polymers widely used, for example, in sportswear, weather-
resistant workwear and medical textiles. There are two basic
types—microporous and hydrophilic membranes—which
transfer water vapour by markedly different mechanisms.
Like ordinary fabrics, microporous membranes rely on
having a degree of air permeability. Water vapour and other
constituents of air can freely diffuse through the intercon-
nected holes and passageways under a suitable concentration
gradient. This transport mechanism closely obeys Fick’s Laws
of Diffusion, and increases with increasing temperature and/or
relative humidity gradient. The ultimate waterproof properties
of microporous membranes such as Fig. 1(a) and 6(a) depend
on the maximum size of the surface pores and their ability to
withstand applied water pressure (commonly known as
hydrostatic head resistance, HHR). Agencies which lower the
surface tension of the liquid water, and therefore reduce
the contact angle that it makes with the pore walls, will lower
the HHR. This has been observed in practice with washing
detergents, dry cleaning fluids, sun-creams and other products
containing surfactants.
Conversely, hydrophilic polymers with solid (non-porous)
structures, e.g. Fig. 1(b) and 7(a), give much higher HHRs and
are intrinsically more waterproof than microporous types.
They also have zero air permeability by textile standards.
Instead, they breathe via an absorption–diffusion–desorption
mechanism which is accelerated by specific water-binding
components, usually PEO segments, incorporated into the
molecular chains. Another common feature of hydrophilic
membranes is that they undergo controlled swelling at high
vapour pressures or when in contact with liquid water. In the
swollen state, the water vapour transfer properties are
enhanced, typically by a factor of three. This process shows
abnormal dependences on temperature and relative humidity,
and is often described as anomalous or non-Fickian diffusion.
Many tens of millions of garments are manufactured each
year incorporating PEO-PU films and coatings as a barrier
layer. These products have evolved so that a good balance
of breathability, waterproofness, durability, laundering and
aesthetic qualities can be achieved at relatively modest cost.
However, because polyurethane chemistry is so infinitely
variable, the polymers outlined in section 4.1 form only a
small fragment of the technology available—plenty of scope
remains for future developments and transfer into new
application areas.
References
1 D. A. Holmes, in Handbook of Technical Textiles, ed. A. R.Horrocks and S. C. Anand, Woodhead Publishing, Cambridge,2000, ch. 12, pp. 282–315.
2 L. Kramar, J. Coated Fabr., 1998, 28, 106–115.3 G. R. Lomax, Textiles, 1985, 14, 2–8.4 J. E. Ruckman, J. Fashion Marketing Management, 2005, 9,
122–129.5 G. R. Lomax, Proceedings of the 11th International Techtextil-
Symposium for Technical Textiles, Nonwovens and Textile-Reinforced Materials, Frankfurt, June, 2005, published on CD.
6 L. Johnson and D. Schultze, Med. Dev. Diagn. Ind., 2000, 30.7 G. R. Lomax, J. Coated Fabr., 1985, 15, 40–66.8 G. R. Lomax, J. Coated Fabr., 1990, 20, 88–107.9 G. R. Lomax, Textiles, 1992, 21, 18–23.
10 E. A. McCullough, M. Kwon and H. Shim, Meas. Sci. Technol.,2003, 14, 1402–1408.
11 J. Comyn, in Polymer Permeability, ed. J. Comyn, Elsevier,London, 1985, ch. 1, pp. 1–10.
Fig. 11 Some non-WBF applications for PEO-PUs.
This journal is � The Royal Society of Chemistry 2007 J. Mater. Chem., 2007, 17, 2775–2784 | 2783
Publ
ishe
d on
22
May
200
7. D
ownl
oade
d by
Uni
vers
ity o
f W
este
rn O
ntar
io o
n 31
/10/
2014
16:
20:2
3.
View Article Online
12 G. R. Lomax, Proceedings of the 9th International Techtextil-Symposium for Technical Textiles, Nonwovens and Textile-Reinforced Materials, Frankfurt, April, 2001, published on CD.
13 P. W. Gibson, Polym. Testing, 2000, 19, 673–691.14 P. Leitch and T. H. Tassinari, J. Ind. Text., 2000, 29, 173–190.15 ISO 11092:1993; ISO 15496:2004 and ISO 8096:2005.16 G. Havenith, Exog. Dermatol., 2002, 1, 221–230.17 I. Holmer, Ind. Health, 2006, 44, 404–413.18 G. R. Lomax, presented in part at the Limits of Protection and
Comfort Conference, Leeds, April, 2006.19 R. J. Osczevski, Text. Res. J., 1996, 66, 24–29.20 V. T. Bartels and K. H. Umbach, Text. Res. J., 2002, 72, 899–905.21 G. R. Lomax, Proceedings of the Nanotechnologies and Smart
Textiles for Industry and Fashion Conference, London, October,2006, published on CD.
22 EN 343:2003.23 H. Traubel, in New Materials Permeable to Water Vapor, Springer-
Verlag, Berlin, 1999, part 4, pp. 107–213.24 W. L. Gore and Associates, Inc., US Pat., 3 953 566, 1976.25 E. E. Clulow, Textiles, 1978, 7, 47–52.26 G. R. Lomax, Proceedings of the 40th International Man-Made
Fibres Congress, Dornbirn, September, 2001, published on CD.27 E. I. du Pont de Nemours and Company, US Pat., 7 164 046, 2007.28 Shirley Institute, Br. Pat., 2 087 909, 1981.29 Shirley Institute, Br. Pat., 2 157 703, 1985.30 V. M. Desai and V. D. Athawale, J. Coated Fabr., 1995, 25, 39–46.31 N. S. Schneider, J. L. Illinger and F. E. Karasz, J. Appl. Polym.
Sci., 1993, 47, 1419–1425.32 K. J. Liu and J. L. Parsons, Macromolecules, 1969, 2, 529.33 N. B. Graham, N. E. Nwachuku and D. J. Walsh, Polymer, 1982,
23, 1345–1349.34 N. B. Graham, M. Zulfiqar, N. E. Nwachuku and A. Rashid,
Polymer, 1989, 30, 528–533.
35 G. R. Lomax, unpublished work.36 Y. Aray, M. Marquez, J. Rodrıguez, D. Vega, Y. Simon-Manso,
S. Coll, C. Gonzalez and D. A. Weitz, J. Phys. Chem. B, 2004, 108,2418–2424.
37 F. Gu, H. Bu and Z. Zhang, Macromol. Chem. Phys., 1998, 199,2597–2600.
38 J. A. Johnson, M.-L. Saboungi, D. L. Price, S. Ansell, T. P. Russell,J. W. Halley and B. Nielsen, J. Chem. Phys., 1998, 109, 7005–7010.
39 R. Kjellander and E. Florin, J. Chem. Soc., Faraday Trans. 1, 1981,77, 2053–2077.
40 F. Oesterhelt, M. Reif and H. E. Gaub, New J. Phys., 1999, 1, 6.41 H. J. Kreuzer, R. L. C. Wang and M. Grunze, New J. Phys., 1999,
1, 21.42 B. Heymann and H. Grubmuller, Chem. Phys. Lett., 1999, 307,
425–432.43 Baxenden Chemicals, Ltd, World Pat., 2006 075 144, 2006.44 J.-J. Lin and Y.-C. Chen, Polym. Int., 1999, 48, 57–62.45 U. Makal and K. J. Wynne, Langmuir, 2005, 21, 3742–3745.46 N. B. Graham and M. E. McNeill, Biomaterials, 1984, 5, 27–35.47 A. S. Vatalis, A. C. Stergiou, A. H. Kehayoglou and C. G. Delides,
Polym. Int., 2004, 53, 1957–1962.48 S. Hayashi, N. Ishikawa and C. iordano, J. Coated Fabr., 1993, 23,
75–83.49 H. M. Jeong, B. K. Ahn and B. K. Kim, Polym. Int., 2000, 49,
1714–1721.50 P. W. Gibson, Proceedings of the 21st Membrane/Separations
Technology Conference, Boston, December, 2003, published onCD.
51 J. H. Park, K. D. Park and Y. H. Bae, Biomaterials, 1999, 20,943–953.
52 P. Basak, S. V. Manorama, R. K. Singh and O. Parkash, J. Phys.Chem. B, 2005, 109, 1174–1182.
2784 | J. Mater. Chem., 2007, 17, 2775–2784 This journal is � The Royal Society of Chemistry 2007
Publ
ishe
d on
22
May
200
7. D
ownl
oade
d by
Uni
vers
ity o
f W
este
rn O
ntar
io o
n 31
/10/
2014
16:
20:2
3.
View Article Online