Key words
vapor deposition - polymer coating - surface modification - surface structures - material
interfaces
1. Introduction
Vapor deposition to prepare thin-film coatings renders attributes including a dry
and clean process, excellent film quality and uniformity, and the deposition coating
process is also reliable with high control and reproduction fidelity.[1] Vapor deposition processes are also widely implemented in current industrial production
and in many discipline fields, e.g. semiconductors, electronics, biomedical devices,
etc.[2] These vapor-deposited thin films are mostly inorganic materials such as metals,
oxides, metal-organics, and/or their combination and derivatives and are in some minority
cases polymer thin films; even fewer cases are industrialized into mass production
(e.g. Parylene™). That is, the vapor deposition of polymeric thin films is still in the research
development stage, and altering the interface properties of existing materials, including
metals, polymers, oxides/ceramics, glass, and silicon, is widely discussed, using
these vapor-deposited polymers as surface modification tools and achieving new properties
that the original materials do not possess. This interface technology of polymer thin
films shows promise in current materials science to provide controlled surface engineering
properties and has successfully demonstrated new possibilities and applications for
prospective materials with current existing materials.[3],[4] With the same merits of the vapor deposition process (dry process and conformal
film uniformity) described above, vapor-deposited polymers provide an additional variety
of chemical functionalities, and post- and more sophisticated conjugation chemistry
or multifunctionality[5],[6] can be further executed.[7]–[14] Furthermore, from the physical prospective point of view, these vapor-deposited
polymers are available for structuring/patterning with lithographic techniques and
render confined compartments at the micro/nanoscale of these functional polymers.[15] These combined physical and chemical properties also lead to controlled anisotropy
in which the layer-by-layer arrangement, gradient, hierarchy, and compartmentalization
of the devised properties can be addressed, as well as organizing the materials into
selected configurations from 2D to 3D.[16] Applications of using these vapor-deposited polymers from thin films to structural
devices have shown promising results and have delivered novel concepts for prospective
material design in many materials science disciplines.
In this review, we highlight the developments in vapor deposition of polymers with
the possibility of a variety of physical structures, including thin films, patterned
structures, and even 3D and porous structures. From both physical and chemical perspectives,
the production and use of these vapor-deposited polymers are discussed. The advanced
fashion of producing these polymers into controlled gradient, compartmentalized, and
hierarchical distributions is also shown with interesting fabrication processes. Finally,
some important applications of using these polymers are demonstrated with some featured
examples. Although not comprehensive, the review herein is intended to deliver insight
into vapor-deposited polymer technologies with their current advances, and we expect
that there will be more novelty and concepts to overcome current challenges and to
fulfill the increasing needs of prospective materials and interfaces.
2. Fabrication and Materials
2. Fabrication and Materials
Polymer thin films are a growing field due to their versatility and immense technological
potential in functionalizing materials and devices. They exhibit many different functions,
including tailoring the surface energy, enhancing adhesion, providing insulation,
acting as organic barriers, and providing stimuli responsiveness, UV protection and
many other additional properties.[17] These functions make polymer thin films applicable for many fields, including biomedicine,
sensors, microelectronics, and optics. Currently, the research trend in polymers has
started to shift from 2D substrates to the fabrication of free-standing nanomaterials
such as nanoparticles, nanotubes, and nanowires.[18] Polymer nanostructures possess advantages over other types of nanomaterials, as
they are easily tunable, their structures can be altered to produce structures with
various compositions, morphologies, sizes, and surface properties.[19] Vapor deposition has emerged as a promising technology for polymer synthesis because
of its unique properties over traditional solvent polymerization. Vapor deposition
enables (1) solvent-free, uniform and conformal large-area film fabrication on both
planar surfaces and 3D geometries[20] and (2) real-time control over the thickness and nanostructure of growing films.[21] Vapor deposition is a technique in which the coating ingredient evaporates into
atoms, molecules, or ions and then condenses onto the substrate surface.[22] Chemical vapor deposition (CVD) and physical vapor deposition (PVD) are two types
of vapor deposition techniques. Vapor deposition is especially suited for synthesizing
insoluble or infusible polymer thin films such as fluoropolymers, crosslinked organic
materials, and conjugated polymers.[23] Rather than utilizing atoms as film-building species like in PVD methods, e.g. sputtering
or evaporation, reactive molecules or radicals in CVD construct a polymeric film through
a chemical reaction.[24] CVD polymerization includes a wide range of deposition processes, such as initiated
CVD (iCVD), oxidative CVD (oCVD), plasma-enhanced CVD (PECVD), photoninitiated CVD
(piCVD), and atomic layer deposition. The CVD variations most commonly utilized to
fabricate polymer thin films are iCVD, piCVD, PECVD, oCVD and parylene CVD, which
will be the emphasis of this section. The comparisons of these techniques are listed
in [Table 1]. The following section will discuss the CVD techniques used to fabricate polymer
thin films and structures, as well as the material physical attributes and functionality
that each process produces.
Table 1 Comparisons of several polymer thin-film fabrication methods
|
Method
|
Polymers
|
Initiators
|
Common substrates
|
Mechanism
|
Advantages
|
Film features
|
Ref.
|
|
iCVD
|
Monovinyl
PHEMA, PHEMAx, and PGMA
Multivinyl
PMAH, PDVB, PV3D3, and PHPFO
|
tert-butyl peroxide (TBPO)
Perfluorobutanesulfonyl fluoride (PFBSF)
|
Silicon wafer
Glass
Mesoporous TiO2
|
Chain-growth polymerization
|
Wide variety of monomers
One-step copolymerization of composite film
Functional retention of the deposited polymer
|
Hydrophobic/hydrophilic properties
Stimuli-responsiveness (thermal and pH)
Mechanical robustness
Gradient properties
|
[31],[37]–[70]
|
|
piCVD
|
Photoinitiative monomers, e.g.
PHEMA,
PHEMAxE, GDA,
PHEA, and
PTFOA
|
Photoinitiator: ultraviolet (UV) light
|
Silicon wafer
Sodium-sensing optode
Polymers (as wearable sensors)
|
Chain-growth polymerization
|
High crosslinking
High deposition rate control
Operable at atmospheric pressure and room temperature
|
Biocompatible
Enhanced cell adhesion
Mechanical robustness
Hydrophobic/hydrophilic properties
|
[35],[71],[72]
|
|
PECVD
|
Graphene
Carbon nanotubes
|
Cold plasma
Gas: O2, CF4, and Ar
|
Silicon wafer
Stainless steel
SiO2, Al2O3, Ni
Cu foils
PDMS
|
Chain-growth polymerization
|
High deposition rates
Wide variety of monomers
|
Thermal-responsiveness
Hydrophobic/hydrophilic properties
|
[36],[73]
|
|
AP-PECVD
|
PNVCL
PV4D4
|
Dielectric barrier discharge (DBD) plasma
Gas: Ar and O2
|
Silicon wafer
PDMS
|
Chain-growth polymerization
|
Operable at atmospheric pressure
|
Antimicrobial properties
Insulating properties
|
[74],[75]
|
|
oCVD
|
PEDOT
Polypyrrole (PPy)
|
Gas oxidants:
metal halogen salt or halogen gas, e.g.
Fe(III)Cl3 and CuCl2
Liquid oxidants: antimony pentachloride (SbCl5); vanadium oxytrichloride (VOCl3)
|
Silicon wafer
Fiber
Glass
Polycrystalline ZnO
|
Step-growth polymerization
|
High conformity
|
Mechanical robustness
Enhanced adhesion
Patterned film
Electrical conductivity
|
[76]–[85]
|
|
Parylene CVD
|
Parylene N
Parylene C
Parylene AF4
Parylene D
Parylene HT
Parylene F
|
–
|
Silicon wafer
Glass
PDMS
|
–
|
Wide variety of functional groups
Facilitation of chemical conjugations
|
Antifouling properties
Antimicrobial properties
Anticorrosion properties
Hydrophobicity
Thermal stability
|
[18],[86]–[105]
|
2.1 Processing Technologies
CVD systems are fundamentally composed of three elementary stages. First, the reactant
gases are delivered into the deposition chamber through the gas inlet. Second, in
the deposition chamber, the precursors undergo gas-phase reactions to activate them
and enable subsequent polymerization on the substrate surface. Heterogeneous reactions
at the gas–solid interface led to continuous thin film development. Finally, gaseous
products and unreacted species are removed through the gas exhaust.[25],[26] CVD methods are frequently named after their energy sources, such as PECVD, or reaction
mechanisms, such as iCVD or piCVD.[26]
The iCVD uses free-radical volatile initiators, such as tert-butyl peroxide (TBPO), and precursors containing vinyl bonds for the polymerization
process. Polymer synthesis and film manufacturing may be accomplished in a single
step by using this method.[2],[27] The iCVD approach mimics chain-growth synthesis in solvent polymerization to produce
electrically insulating polymers with desired organic functional groups. Some of the
merits of iCVD include conformal surface modifications, precise control of polymer
chemistry, a vast library of functional groups, minimal byproduct formation, and compatibility
with delicate substrates, making it suitable for a wide range of applications.[2],[26],[28] Welchert et al. used an oblique angle to introduce monomer vapor to the substrate
to pattern n-butyl acrylate (nBA), methacrylic acid (MAA), and 2-hydroxyethyl methacrylate (HEMA)
polymer films during iCVD.[29] A uniform coating can also be enhanced by utilizing a speaker to vibrate the substrate.[30] Chen et al. demonstrated that iCVD is a useful technique for creating well-integrated
polymer–nanostructure systems that can be used to study how polymers behave in nanoconfined
environments.[31] In another study, Mao et al. demonstrated the versatile application of iCVD by showing
the use of iCVD to stabilize an electrochemically active polymer, polyvinylferrocene,
by soft confining it with P(2-hydroxyethyl methacrylate-co-di(ethylene glycol) divinyl
ether) (P(HEMA-co-DEGDVE)) using the iCVD method.[32] Monomers that were used in the iCVD method have been tabulated and can be seen in
the review by Gleason.[33]
A variant of iCVD known as piCVD uses UV light rather than thermal light to activate
the initiators. This enables the activation of certain methacrylate monomers without
the need for thermally labile and short-lived initiators used in iCVD.[26],[34] The use of photoinitiators also eliminates the use of high-temperature sources.
However, this method has a drawback in that the reactive mixture must be photosensitive,
and as such, only a certain number of monomers can be used. This limitation, on the
other hand, aids in reaction control by allowing the molecules on the substrate to
restructure. As a result, piCVD produces more crosslinked structures.[35]
A CVD process that is similar to piCVD is PECVD; instead of using UV light, PECVD
uses cold plasma to initiate free-radical polymerization. The use of plasma enhances
the PECVD versatility due to its high energy transfer to the reactive species. For
example, PECVD enables the deposition of inorganic–organic composite films in one
chamber.[36]
PECVD has been used to functionalize nanoparticles and fabricate carbon nanotubes.[35] The issue with this technique is that it often leads to unstructured coatings. This
is because the release of a wide range of species causes nonspecific reactions to
occur.[34],[35] Pulsed-PECVD, one of the variants of this technique, uses pulsed plasma to allow
the restructuring of the coating. To eliminate the use of vacuum pressure, which is
required by the PECVD technique, PECVD has been improved to be capable of working
at atmospheric pressure, making scaling up easier; this process is known as atmospheric
pressure plasma-initiated CVD (AP-piCVD). This method uses temporally isolated discharge
to initiate the polymerization. By using this method, Loyer et al. successfully copolymerized
N-vinyl caprolactam (NVCL) with ethylene glycol dimethacrylate (EGDMA) to fabricate
water-soluble and water-stable thermoresponsive thin films.[34] Getnet et al. (2020) also used this method to deposit carvacrol extract on stainless
steel to prevent the formation of biofilms.[74] The resulting films adhere well to the substrate and remain stable for a long time
when exposed to UV light and air. Coclite et al. used initiated plasma-enhanced CVD
(iPECVD) of an organosilicon polymer (1,3,5-trivinyl-1,1,3,5,5-pentamethyltrisiloxane
[TVTSO] monomer) to planarize silicon substrates and demonstrated that when the organic
thin film is 1.8 nm thick, a 99% degree of global planarization could be achieved.[107] For graphene film growth by atmospheric pressure CVD on copper foil, the final graphene
filmʼs homogeneity and electronic transport properties were found to be strongly influenced
by the surface morphology of the Cu substrate and the concentration of carbon feedstock
gas, as reported by Luo et al.[109]
Another type of CVD used to fabricate thin films is oCVD. Unlike iCVD that employs
chain-growth polymerization, oCVD implements step-growth polymerization. Rather than
using an initiator, oCVD uses an oxidizing agent, such as an evaporated metal halogen
salt, or halogen gas, such as vapor iron(III) chloride. Together with the vaporized
monomer, for example, 3,4-ethylene dioxythiophene (EDOT), it is injected into a vacuum
chamber with a hot wall to begin polymerization.[110] The oCVD method allows for the development of grafted interfaces for firmly adherent
layers. Additionally, oCVD enables conformal coverage where layers with the same thickness
can be deposited over nonplanar structures, such as rough surfaces. Vapor printing
or patterning films could also be fabricated by using this method.[23] The oCVD is preferred for fabricating electrically conducting or semiconducting
films since it offers control over the morphology of the conjugated polymers, which
leads to optimization of their optoelectronic characteristics.[27] For example, simply by adjusting the substrateʼs temperature, it is possible to
modify the polymer electrical conductivity.[111] As shown by Wang et al. (2018), by inducing a crystallite-configuration transition
by oCVD and heating the substrate to 300 °C, poly(3,4-ethylenedioxythiophene) (PEDOT)
thin films with a record-high electrical conductivity of 6259 S/cm and a remarkably
high carrier mobility of 18.45 cm2 · V−1 · s−1 can be produced.[112] In addition to gaseous oxidants, liquid oxidants such as antimony pentachloride
(SbCl5) and vanadium oxytrichloride (VOCl3) have also been used in oCVD to fabricate PEDOT thin films with conductivities exceeding
2100 S/cm, as shown by Kaviani et al. (2019).[113] They also demonstrated that one of the most important factors that affect the properties
of the deposited material is the choice of oxidant. To date, the oCVD method has been
used to fabricate organic conducting and semiconducting polymers that are being used
in photovoltaic cells and biosensors.[23]
Parylene CVD is another type of CVD used in the fabrication of thin films. This CVD
method, as the name implies, polymerizes [2.2]paracyclophanes (PCPs) to poly(para-xylylene) (PPX) or parylene. Following the Gorham process, PCP is sublimated to form
its radical species, para-xylylene (p-xylylene), which spontaneously deposits on target surfaces that are typically kept
at or below room temperature.[114] Parylene could be deposited as thin, conformal, pinhole-free films using CVD, with
the thickness adjustable by changing the amount of precursor used for CVD polymerization.[115] Patterned coatings can also be achieved by using CVD, and patterning can occur after
the CVD process or during the CVD process.[116] By using this technique, a variety of functional groups can be added to parylene,
allowing its surface chemistry to be further modified for various applications.[26] Parylene, especially parylene C (mono-chloro-PCP), is known for its high biocompatibility,
anticorrosive properties, and antibacterial properties, making it suitable as a biomaterial.[18] Other parylenes that have been fabricated with CVD include parylene N (nonfunctionalized),
parylene D (di-chloro-PCP), and parylene-HT (tetra-fluoro-PCP). Tian et al. deposited
parylene AF4 (octafluoro-[2.2]paracyclophane) onto polydimethylsiloxan (PDMS) to create
a surface with wrinkled surface topography, low surface free energy, and negative
surface charge properties that exhibited antifouling performance against bacteria
and algae.[86] A variety of functionalized groups used in parylene CVD have been fully reviewed
by Hassan et al.[18] Sim et al. developed a single-step bifacial vertical deposition method to address
the issue of thickness variations on both sides of the sample that arise during traditional
horizontal deposition.[106] In another study, Hu et al. used a sublimating ice template as the CVD substrate
to produce an advanced functional porous material that is capable of conjugating with
thiol-Michael click chemistry.[93] Protocols to examine and characterize PPX layer stability properties, including
thermostability and adhesive strength, and biocompatibility (cell viability and immunological
responses) were proposed by Hsu et al.[117]
2.2 Physical Properties
Thin films made by vapor deposition have a wide range of properties that are dependent
on the process, monomers, and substrates used to fabricate them. The control of film
properties could be achieved by fine-tuning the system parameters such as monomer
flow rates, plasma power or filament temperatures.[38] This section will discuss the physical properties of vapor-deposited fabricated
films, such as thickness, morphology, mechanical properties, and electrical conductivity,
and factors that affect them. The physical properties discussed in this section are
shown in [Figure 1].
Figure 1 Schematic diagram of the fundamental physical properties of thin films. (A) Schematic
diagram of the two-sided deposition of parylene C onto a silicon wafer substrate with
vertical deposition.[106] Reprinted from Ref. [106] published under a creative commons license (CC BY). (B) Cross-sectional scanning
electron microscopy (SEM) images of iPECVD-grown PTVTSO on a trench wafer substrate.[107] Reprinted with permission from Ref. [107]. Copyright 2012 AIP Publishing. (C) SEM images of p(C6-co-IEM)-coated PET fabric
before (upper left) and after 1,000 cycles of sandpaper abrasion (upper right), as
well as close-up views of the coatings after 1,000 cycles of sandpaper abrasion (bottom).[108] Reprinted with permission from Ref. [108]. Copyright 2020 Elsevier. (D) AFM measurements of surfaces with smooth and rough
characteristics for parylene N (no. 1, 4) and parylene C (no. 2, 3) deposited with
PECVD (top) and CVD (bottom).[73] Reprinted from Ref. [73] published under a creative commons license (CC BY).
Montero et al. used piCVD to copolymerize HEMA and the functional comonomer pentafluorophenylmethacrylate
(PFM) and discovered that varying the precursor flow rates during deposition enables
the fabrication of films with thickness gradients.[118] This is consistent with the findings of Welchert et al., who used oblique angle
iCVD to polymerize n-nBA, MAA, and HEMA on silicon wafers and discovered that the
flow rate of the monomer is the major parameter that affects the thickness profile.[29] In another study, Sim et al. used vertical deposition of parylene to fabricate a
parylene C thin film on both sites of the substrate simultaneously with the same and
uniform thickness.[106] Profiling thin films is also important to achieve an understanding of the thin film
characteristics. Chen et al. developed an experimental method that combines ion milling
and high-resolution field emission scanning electron microscopy to acquire a precise
and accurate depth profile of the coating thickness and iCVD kinetics along nanopores
with a diameter of 110 nm.[119] For copolymerization of hybrid organic–inorganic polymeric films, uniform thickness
could be achieved by using modified iCVD with a dual showerhead injector, as shown
by Kim et al.[120]
Surface morphology or roughness is another parameter that depends strongly on the
CVD method and is usually characterized with atomic force microscopy (AFM). As compared
by Gerhard, parylene C fabricated by PECVD shows smoothness compared to that fabricated
by CVD. Surface roughness is one of the major causes, in addition to the existence
of hydrophilic functional groups, that could influence the hydrophobicity of thin
films.[73] Smoothening the surface can enhance its wettability. To achieve this, the deposition
rate must be kept low to direct the polymerization toward surface polymerization rather
than volume polymerization and produce a higher film quality.[121] As shown by Chen et al., treating parylene CVD with plasma CF4 could trigger volume polymerization, which will produce roughened surfaces with low
hydrophilicity.[73],[122] Therefore, the hydrophilicity of parylene films is tunable with plasma treatment
either temporarily or permanently, and superhydrophobic surfaces can be fabricated
at a minimal cost. Gołda et al. reported that by using oxygen plasma to fabricate
nanoroughness on a parylene surface after the CVD process, the contact angle could
be decreased, thereby increasing the hydrophilicity.[123] Brancato et al. also concluded that by strategically adjusting the plasma exposure
times, the degree of hydrophobicity of the prepared surface can be precisely controlled.[124] Surface roughness also plays an important role in the adhesion of parylene coating
to silicon wafers or metals, and adhesion can be increased by enlarging the surface/volume
ratio.[122] In a different study, Hsu et al. discovered that with parylene CVD, a slightly rougher
surface will be produced at a higher sublimation rate.[125] The increase in roughness is due to the higher deposition pressure. Therefore, increasing
the sublimation rate to increase film thickness or production throughput should be
done with surface roughness in mind. However, with oCVD and vapor phase polymerization
(VPP), which use oxidants, it has been reported that rapid polymerization resulting
from high redox activities increases the film roughness.[126] To counter this problem, Goktas et al. demonstrated that the addition of water vapor
while fabricating PEDOT thin films results in better molecular alignment for oCVD
PEDOT and a smoother surface for VPP PEDOT.[127] Additionally, they discovered that during the VPP process, temperature and water
vapor both affect the surface roughness. Besides the deposition rate, the surface
roughness also depends on the CVD substrate, as investigated by Amirzada et al.[128] As with oCVD, the PEDOT thin-film crystallographic texture can vary depending on
grafting, control of the growth temperature and film thickness and the choice of oxidant.[28] PEDOT produced with oCVD has an edge-on orientation, in contrast to PEDOT prepared
by liquid oxidants, which has a face-on orientation.[129] Moni et al. reported that edge-on thin films provide higher specific capacities
for a given charge/discharge rate and therefore display electrochemical activity.[130]
Mechanical properties are the physical properties a material shows when subjected
to forces and include the modulus of elasticity, tensile strength, elongation, hardness,
and others. Zhao et al. showed that the mechanical properties of poly(divinylbenzene)
(PDVB) films fabricated by iCVD on silicon wafers could be increased by incorporating
a post-CVD thermal annealing process.[131] By using iCVD to fabricate self-crosslinkable poly(perfluorohexylethyl acrylate-co-isocyanato
ethyl methacrylate), Shao et al. showed that the crosslinked network greatly improved
the mechanical strength. Additionally, by enhancing the mechanical strength, the thin
films are able to withstand a variety of durability tests, such as boiling for more
than 12 hours and 20,000 cm of sandpaper abrasion.[108] This is consistent with the results of Lee et al. using iCVD to conjugate poly(2,4,6,8-tetramethyl-2,4,6,8-tetravinylcyclotetrasiloxane)
(PV4D4) with PPFDMA, producing a PV4D4-PFDMA film with exceptional stability and durability
due to crosslinking.[132] The tests showed better tensile strength and rubbing resistance compared to those
of other films. Mechanical robustness was also shown to be enhanced by copolymerizing
2-hydroxyethylacrylate with glycidyl methacrylate (GMA) with the iCVD method in a
study performed by Jeong et al.[133] This is because GMA contains a rigid methacrylate group.
Electrical conductivity is a major focus for PEDOT films synthesized using the oCVD
method. Maintaining monomer fidelity in the film is crucial for producing high-conductivity
conjugated polymers.[28] oCVD provides control over crystallite sizes and therefore control over electrical
conductivity. Wang et al. used oCVD and demonstrated that by inducing a crystallite-configuration
transition, PEDOT thin films with a record-high electrical conductivity of 6259 S/cm
and a remarkably high carrier mobility of 18.45 cm2 · V−1 · s−1 could be achieved.[112] Smith et al. found that the electrical conductivity, which ranges from 1 to 30 S/cm,
does not clearly affect the thermal conductivity of oCVD-grown PEDOT films. It is
believed that at these electrical conductivities, phonon transport predominates, and
the electronic contribution to thermal conductivity is very small.[134] Therefore, CVD polymerization appears to be an appealing method for creating polymer
films with low thermal conductivity and relatively high electrical conductivity values.
Drewelow et al. proposed the conductivity in PEDOT films as a function of substrate
temperature and thickness due to the enhanced crystalline and chemical environmental
structures in PEDOT grown at higher substrate temperatures.[111] The conductivity increases with increasing substrate temperature initially and then
decreases with increasing film thickness.
2.3 Chemical Functionality
The functionalities of thin films greatly depend on the functional groups of the monomers.
These functional groups could enable covalent binding, surface chemistry such as alkyne–azide
“click” chemistry, reactions of active esters with amine, aldehydes/ketones with hydrazides
and alkoxyamines, and thiols with alkenes and alkynes and surface-initiated atom transfer
radical polymerization (SI-ATRP)[135] to bring specific functions such as anticorrosion and enhanced biocompatibility,
resulting in a multifunctional surface. [Figure 2] summarizes the functionalized thin-film monomers discussed in this section.
Figure 2 Schematic diagram of several functional groups of CVD monomers and their chemical
functionalities.
CVD-grown parylene has especially demonstrated surface chemistry functionalities.
For instance, Sun et al. used CVD to fabricate thiol-reactive parylene (poly(4-vinyl-p-xylylene)-co(-p-xylylene) and poly(4-N-maleimidomethyl-p-xylylene)-co-(p-xylylene). These functional groups enable thiol-ene and thiol-ene maleimide click
reactions, respectively. The resulting surfaces suppress protein fouling and enhance
surface affinity toward cell attachment.[136] Chen et al., in another study, also demonstrated the fabrication of alkyne-functionalized
parylene on which poly(sulfobetaine methacrylate-co-Az) could be conjugated via click
chemistry.[137] The conjugated polymers were remarkably stable and successfully reduced protein
adsorption and cell adhesion. The findings show that the CVD technique offers a straightforward
and reliable tool for producing antifouling surfaces on a variety of substrates. In
another study reported by Im et al., iCVD was used to fabricate click-active surfaces
via CuAAC chemistry by polymerizing poly(propargyl methacrylate) (PPMA).[138] In addition to the click reaction, CVD of parylene also shows its applicability
in surface modification via atom transfer radical polymerization (ATRP). As reported
by Jiang et al., CVD of [2.2]paracyclophane-4-methyl 2-bromoisobutyrate onto heterogeneous
groups of substrates, such as silicon and glass, enables SI-ATRP, as confirmed by
ATRP of oligo(ethylene glycol) methyl ether methacrylate.[139]
CVD also enables “covalent grafting” or covalent binding of polymers to substrates.
Covalent binding promotes better adhesion of the thin film to its substrate.[140] As shown by Shao et al., copolymerization of a short-fluorinated side chain monomer,
perfluorohexylethyl acrylate (C6), and isocyanato ethyl methacrylate (IEM) with iCVD
to fiber as a substrate facilitated covalent binding with functional groups, such
as hydroxyl, amino, and carboxylic groups, in the substrate, thus exhibiting excellent
adhesion.[108] Covalent bonding also shows its functionality in patterning thin films. Patterns
can be used to resist an underlying layer being patterned or to retain specific molecules
or nanoparticles in place.[140] In another study, Vaddiraju et al. demonstrated that copolymerization of pyrrole
with thiophene-3-acetic acid with oCVD enables covalent binding of thin films with
metal nanoparticles.[145] This discovery opens the path for the development of conducting polymer–metal nanoparticle
hybrids. Organic–inorganic binding is also enabled by –OH groups in the organic monomers
that react with the inorganic precursors to form metal-oxide units in the polymer,
as shown by Kim et al., who polymerized HEMA with inorganic precursors such as trimethyl
alumina (TMA), tetrakis dimethyl amino hafnium (TDMAHf), tetrakis dimethyl zirconium
(TDMAZr), and tetrakis dimethyl amino titanium TDMATi via iCVD.[120]
Crosslinking bonds have shown their importance in fabricating polymer thin films with
high mechanical strength and hydrophobicity. Gao et al. demonstrated the feasibility
of creating a thin film that is insoluble in a number of solvents and offers stainless
steel corrosion resistance in concentrated 1 N HCl solutions by fabricating crosslinking
PDVB via cationic CVD.[17] Shao et al., as mentioned above, polymerized highly reactive isocyanate groups that
enabled self-crosslinking.[108] The fluorinated chains were fixed on the surface by crosslinking, which reduced
the contact angle hysteresis causing the thin-film superhydrophobicity property. In
another study, Soto et al. crosslinked 1H,1H-perfluorooctyl methacrylate (H1F7Ma) with DVB using iCVD and achieved an optimal combination between surface energy,
permitted carbon chain length, and polymer chain rigidity, resulting in superior nonwetting
fabrics.[146] On the other hand, in a study by Xu et al., covalent binding facilitated by the
amine functional group in poly(4-aminostyrene) opens the opportunities for detection
of various biomolecules.[147]
3. Controls of Anisotropy
3. Controls of Anisotropy
Polymeric materials have been utilized in various applications. Depending on their
applications, the chemical and physical properties of the materials are crucial. The
monomer can change the bulk material properties for polymerization, processing parameters,
or conjugating density. As we pointed out in section 2, materials with diverse chemical
properties could be obtained by polymerizing functionalized monomers or utilizing
functionalization on the surface. The materialʼs structure, surface morphology, and
anisotropic property are designed by changing the processing parameters. Recently,
the requirement for anisotropic materials has increased with the development of various
applications, such as permeation, medical devices, and tissue engineering. For example,
an asymmetric porous membrane was fabricated into hollow fibers in an extracorporeal
membrane oxygenation system.[148] In this section, fabrication techniques for preparing a membrane with a porous structure
and nanotopographic surface that has become more critical will be discussed. We will
focus on process design and combination with other techniques for the fabricated anisotropic
membrane as technology requirements increase, along with the demand for multiple properties
in materials. Thus, there has been a surge in research on compartment and composite
materials. For example, organic–inorganic composite polymers showed better performance
as electrolyte membranes.[149] At the end of this section, we will introduce some novel studies on fabricating
3D materials via vapor deposition polymerization (VDP).
3.1 Homogeneous Film and Structure
The surface tension increases the difficulty of fabricating uniform membranes on geometric
surfaces via liquid-phase polymerization. VDP removes the restrictions assessed by
solvent surface tension. Tenhaeffʼs group reported that the film thickness uniformity
on the top, sidewall, and bottom was better when the polymer was coated in the trench
via CVD vs. liquid-phase polymerization.[150],[151] On this merit, VDP could fabricate conformal membranes on topographically complex
surfaces, such as patterned surfaces,[141] microtubes,[152] microchannels,[153] particles,[154] and woven fibers.[155]–[159]
[Figure 3]A-i shows the conformal coating on the patterned substrate. The feature of diffusing
reactants in the vapor phase allows VDP to fabricate conformal membranes in small
geometries. The surface in the porous membrane of nylon was modified by poly(perfluorodecyl
acrylate) (PPFDA) and PDVB via iCVD to improve the hydrophobicity.[39] A virus-structure surface was coated with polytetrafluoroethylene (PTFE) via iCVD
to achieve continued superhydrophobicity without degradation for several months.[40]
Figure 3 Manufacturing an anisotropic structure. (A) Surface structure: (i) cross-sectional
SEM images of a conformal coating on a patterned substrate.[141] Reprinted with permission from Ref. [141]. Copyright 2018 American Chemical Society. (ii) Cross-sectional SEM images of a
columnar structure.[88] Reprinted with permission from Ref. [88]. Copyright 2007 American Chemical Society. (iii) Side-view SEM images of a worm
structure.[42] Reprinted with permission from Ref. [42]. Copyright 2022 John Wiley and Sons. (B) Schematic diagram of patterning a surface
via microcontact printing.[142] Reprinted from Ref. [142] published under a creative commons license (CC BY). (C) Schematic diagram of the
fabrication of 3D porous materials by chemical vapor sublimation and deposition.[143] Reprinted with permission from Ref. [143]. Copyright 2017 Elsevier. (D) Schematic diagram of a nanoscale gradient copolymer.[37] Reprinted with permission from Ref. [37]. Copyright 2020 Elsevier. (E) A compartmentalized membrane.[51] Reprinted with permission from Ref. [51]. Copyright 2020 American Chemical Society. (F) Schematic diagram of producing composite
nanoparticles.[144] Reprinted with permission from Ref. [144]. Copyright 2018 American Chemical Society. (G) Scheme of the fabrication of a granular
structured membrane.[105] Reprinted from Ref. [105] published under a creative commons license (CC BY).
A polymer membrane could be fabricated with nano- and microtopography by controlling
the CVD polymerization conditions.[41] The poly(perfluorodecyl acrylate-co-ethylene glycol diacrylate) (p(PFDA-co-EGDA))
film polymerized via iCVD on the plasma-etched copper showed a nanoworm-like structure.[160] In the following paragraph, we focus on fabricating polymer film with nano- and
microtopography on a flat substrate.
Guptaʼs group combined conventional and nonconventional iCVD processes to fabricate
poly(methacrylic acid) (PMAA) membranes with pillared structure surfaces. First, the
monomer was deposited in a sequential process. Then, the polymerization was subsequently
controlled by turning on the filament. This combined process was also used to coat
dense and porous membranes with PDVB and poly(methacrylic acid-co-methacrylic anhydride)
to fabricate hydrophobic and hydrophilic membranes.[161]
Demirelʼs group used oblique angle VDP to fabricate thin films of poly(chloro-p-xylylene), poly(bromo-p-xylylene), and poly(o-trifluoroacetyl-p-xylylene-co-p-xylylene) with columnar nanostructures, shown in [Figure 3]A-ii. For oblique angle deposition, a titled flux assisted the deposition process
at an oblique angle.[87],[88] By changing the monomer for polymerization and the oblique angle, the chemical properties
and film morphology of the nanostructured PPX membrane could be controlled at the
same time. A two-layer PPX membrane could be fabricated readily by changing the oblique
angle during the deposition process.[162] A columnar membrane was fabricated on a planar membrane when the oblique angle was
changed from 90° to 10°.
Wei et al. fabricated a free-standing and patterned parylene C membrane with a columnar
structure via a sequential seven-step procedure.[89] A dense thin film of arylene C was polymerized on a patterned substrate, which was
framed with thermal release tape. Then, a columnar parylene C film was polymerized
on the dense film via vapor deposition with a vapor incidence angle of 5°. After heating,
the compartment membrane was separated from the wafer.
Daniel Schwartz synthesized a PPFDA membrane with a worm structure on a silicon substrate
via iCVD to achieve superhydrophobicity and superomniphobicity.[42] The micro- and nanoworms of PPFDA were directly constructed on planar silicon because
of crystallization-directed nucleation and growth. The PPFDA membrane with worm-like
structure is shown in [Figure 3]A-iii.
A superhydrophobic membrane of P(PFDA-co-EGDA) with a cone structure was polymerized
on a polyethylene glycol diacrylate (PEGDA) membrane via iCVD.[43],[163] While the partial pressure of PFDA in the chamber was above the saturation pressure
of PFDA, the PFDA monomer was supersaturated on the PEGDA surface and nucleated to
form nuclei as nanodroplets. Then, the PFDA monomer was adsorbed and polymerized on
the cores to build a conical structure. Then, the PFDA monomer was adsorbed and polymerized
on cores to build a conical structure, shown in [Figure 3]A-iii.
Wei et al. investigated iCVD on various liquid surfaces with a range of refractive
indices.[44] A poly(perfluorooctyl methacrylate) membrane with a lens-structured protrusion formed
on the liquid with a low refractive index because of the attractive long-range van
der Waals interactions. In contrast, due to the repulsive van der Waals forces, discrete
particles formed on the liquids with higher refractive indices under slow deposition.
Robert et al. fabricated a spontaneous self-wrinkling film of poly(perfluorodecyl
acrylate) via iCVD on a liquid-filled patterned surface.[164] The surface curvature of the polymer film was affected by the patterned substrate
and the liquid filled in the patterned surface.
3.2 Patterned Structure
In recent years, researchers have devoted more effort to creating topological patterned
surfaces to satisfy applications, including biotechnology and electronics. Fabricating
patterned surfaces with masks during VDP could simultaneously obtain chemical and
topological patterns. In 2007, Lahannʼs group reported vapor-assisted micropatterning
in replica (VAMPIR) structures to fabricate chemically and topologically designable
membranes of poly(4-pentafluoropropionyl-p-xylylene-co-p-xylylene),[165] poly(4-ethynyl-p-xylylene-co-p-xylylene),[166] poly(4-formyl-p-xylylene-co-p-xylylene),[166] poly(2,5-lutidinylene-co-p-xylylene),[167] and poly(4-ethynyl-2,5-lutidinylene-co-p-xylylene)[167]. In this method, monomers are deposited and polymerized on the area not covered
by the replica structure during CVD polymerization. VAMPIR provides a straightforward
way to pattern surfaces for selectable immobilization with fluorescence-labeled proteins
or quantum dots.[165] The patterned surface via VAMPIR with functional parylenes undergoes bio-orthogonal
multiple click chemistry reactions to immobilize various biomolecules.[166]–[169] A patterned hydrogel was efficiently fabricated via a successive process of polymeric
initiator coating with a mask and SI-ATRP.[170]
3D structures can be formed using masks as well. Nathan J. Trujillo combined the principle
of colloidal lithography and iCVD to fabricate patterned films with bowl structures.[45] A 2D colloidal monolayer assembly was templated first, followed by iCVD. After sonicating
the film in a solvent, the colloidal template was moved from the patterned film. Different
functions could be achieved by using different monomers for iCVD to fabricate patterned
membranes with organic polymers (PBA and PHEMA), fluoropolymers (PPFDA and PPFM),
and organosilicones (PV4D4).
Select polymerization with an inhibitor or inducer could also produce a patterned
surface. Microcontact printing (µCP) is a common technique for patterning flat surfaces
with elastomer stamps and can assist in pattern fabrication under vapor deposition
coating processes. F. Bally immobilized various bioactive molecules via µCP on a poly(4-ethynyl-p-xylylene-co-p-xylylene) membrane fabricated via CVD polymerization.[168] The excellent selectivity of cell adhesion on the partially immobilized cell-adhesion
peptide indicates efficient patterning and the specific click chemistry reaction.[168] Through µCP of molecules with an erasable group, a second functional group could
be printed after removing the terminal group on the first patterned molecule.[142] The scheme for µCP and immobilization is shown in [Figure 3]B. An inhibitor could exclude polymer growth on the designed locations to produce
a patterned film. For example, Kahp et al. fabricated parallel channels with a selectively
polymerizing membrane on the sidewall via CVD polymerization by inhibiting polymer
growth with an iron coating.[171]
The conventional method for patterning with a mask or stamp has difficulty in applying
to non-flat surfaces. Thus, some novel techniques were designed to directly coat patterned
films. VDP-mediated inkjet-printed polyaniline (VDP-IJP) was reported to efficiently
pattern polymers on a flexible substrate (poly(ethylene terephthalate), PET) with
micrometer-scale resolution by Jyongsik Jangʼs group.[79],[80] In the VDP-IJP procedure, the oxidized ink was printed on the substrate to induce
oCVD.[78] After immobilizing RGD on VDP-IJP patterns, the pattern exhibited good selectivity
for cell growth and detecting neurotransmitters.
Some researchers have utilized photolithography to fabricate patterned surfaces with
photoactive polymers, photodefinable polymers, and polymers that can be photosynthesized.
Multilayered methyl methacrylate and styrene patterns were built via vapor-phase-assisted
surface photopolymerization (photo-VASP) with a stripe-patterned photomask on a Si
wafer and Au plate.[172] The patterned polymer film could be autodrawn under photo-VASP with a computer program.
The polymerization of N-isopropylacrylamide (NIPAAm), styrene, and acrylic acid (AA) could be conducted at
different areas separately by changing the monomer and X – Y stages.[173] The photoactivity of the polymer could also be used to produce patterns after the
polymer film was coated. Utilizing the photoactivity of PPMA, a pattern could be provided
by using e-beam irradiation.[138] The other method is fabricating the polymer with a phototrigger-clickable functional
group.[90] Colloidal particles with broad-range patterns were fabricated by a two-step procedure
of photodefinable PPX coating via CVD polymerization and photoreactive coating with
projection lithography through a digital micromirror device.
3.3 Porosity and Gradient
Resorting to the conformal coating of VDP, a porous membrane can be produced by coating
the polymer on a porous scaffold as a template. For example, porous (PPX) foam was
fabricated by CVD polymerization on spongy sugar cubes.[91] One-step VDP of acrylonitrile on colloidal silica particles was conducted to fabricate
silica-polyacrylonitrile composites.[174] Mesoporous carbon was obtained after removing the silica particles and carbonization.
In recent years, many studies have been dedicated to achieving nanostructure surfaces
by altering the polymerization processes. Guptaʼs group provided a procedure of iCVD
to fabricate a porous polymer membrane of PMAA by tuning the partial pressure of the
monomer and the tempura structure.[46] Scott Seidel reported a two-step process of fabricating porous membranes of PMMA:
(1) vapor deposition of the monomer and (2) filament cleaving of TBPO and PMMA polymerization.
The sublimation of unreacted monomer led to porous structure formation. They reported
that the membrane structure was affected by physical monomer deposition, which was
controlled by the monomer flow rate and the substrate temperature. The low temperature
of the substrate reduced the surface diffusion of MMA, causing an increase in the
shadowing effect to form a sponge-like membrane.[41],[47],[48] An asymmetric membrane of poly(1,3,5,7-tetravinyl-1,3,5,7-tetramethylcyclotetrasiloxane-co-ethylene
glycol diacrylate) (p(V4D4-co-EGDA)) was produced on silicone oil via iCVD. The bottom
surface, which was near the oil side, had greater porosity. The top surface was packed
densely and loosely in terms of topography. Increasing the V4D4 content in the copolymer
increased the porosity and microstructure regions.[49]
Matsumotoʼs group provided a technique for producing porous polyurea (PU) via vacuum
deposition polymerization with the ionic liquid (IL) of 1-ethyl-3-methylimidazolium
bis(trifluoromethylsulfonyl) amide ([Emim][TFSA]). A porous PU film was copolymerized
by depositing 4,4′-methylenebis(2-chlorophenyl isocyanate) and 2,7-diaminofluorene
monomer molecules on the IL-coated substrate.[175],[176] The reversibility of IL deposition and vacuum annealing in the PU pores provided
rewritable ion conduction.[177]
Adding porogen to change the mass transfer has been used to fabricate porous structures.
Mixing ethylene glycol as a porogen into a gas mixture of monomer and crosslinker
simultaneously combined VDP with phase separation to fabricate a porous poly(glycidyl
methacrylate) (PGMA) film when the saturation degree of the monomer and porogen surpassed
unity. The concentrations of the crosslinkers and porogens in the gas phase and the
reactivity of the monomers controlled the size, density, and morphology of the pores.
A layer-by-layer membrane with a dense and porous film could be fabricated by changing
the feed-in flow under VDP.[178] The relationship between pore morphology and porogen type has been discussed in
earlier studies.[179],[180] The membrane morphologies of sphere agglomeration, unconnected sheets, and crater-like
shapes were observed when a highly immiscible liquid porogen, a highly immiscible
and crystallizable porogen, and the most miscible porogen were used, respectively.
However, in previous reports, a porous structure could only be fabricated in a polymer
membrane. Chenʼs group developed a novel method with only one step to fabricate porous
membranes and 3D particles. They developed a unique method to fabricate porous, asymmetrical,
and gradient PPX membrane structures via chemical vapor sublimation and deposition
(CVSD). The diradical deposition on the sublimating surface of the ice template formed
a porous structure.[92]
[Figure 3]C shows the scheme for CVSD and the images for the porous materials. This technique
showed remarkable controllability for making structural and functional asymmetry and
gradients at multiple scales. Functionalized porous PPX membranes of poly[(4-N-maleimidomethyl-p-xylylene)-co-(p-xylylene) and poly((methyl propiolate-p-xylylene)-co-(p-xylylene)) were produced via CVSD.[93],[94]
Physical and chemical gradients are selective in some specific applications, such
as selective cell differentiation. Here, we introduce some techniques and processes
to produce a gradient polymer membrane. A 2D morphological and compositional gradient
film of parylene C was fabricated via a two-step process of oblique angle CVD and
oxygen plasma treatment.[95] First, a parylene C film was deposited via oblique angle CVD on a columnar thin
film to fabricate a morphological gradient along the length. Then, each rowʼs surface
was treated by oxygen plasma at a different time to produce a hydrophilicity gradient.
The thickness gradient of the polymer was fabricated by sequentially evaporating a
shutter and a sliding mask under VDP.[96],[97]
Via CVSD polymerization, a porosity gradient and a multifunctional gradient were provided
by designing the composition of the ice template.[92] A PPX membrane with a porosity gradient was fabricated by CVSD polymerization on
an ice template made from a gradient solution of ethanol/water. The gradient composition
of ethanol in the template provided a volatility gradient to produce the porosity
gradient. The deposition polymerization produced the parallel gradient function of
physical magnetic and chemical electrochemical conductivity on the template with a
gradient composition of Fe3O4 and PEDOT.
Yaseen Elkasabi et al. fabricated a surface composition gradient from two functionalized
monomers of [2.2]paracyclophane (4-trifluoroacetyl[2, 2]paracyclophane and 4-aminomethyl[2, 2]paracyclophane)
via CVD copolymerization.[9] Two monomers were fed into the system from the inlet on the opposite side. When
the two sources flowed into the chamber, the monomer was gradually depleted, and the
monomer composition decreased in the gas phase. The monomers with a gradient composition
in the gas deposited and polymerized. Based on this technique, Elkasabi fabricated
composition gradients with CHO and NH2 groups to immobilize biotin hydrazide and sulfo-NHS-LC-biotin to produce cellular
transduction gradients.[181] The assistance of a PDMS channel with a metal baffle reduced the compositional slope
of the gradient and made gradient coatings for 3D objects possible.[182] By programming the gradual change of the monomer concentration of 1,3,5-trivinyl-1,3,5-trimethylcyclotrisiloxane
(V3D3) and 1H,1H,2H,2H-perfluorooctyl acrylate (C6PFA) or hexafluoropropylene oxide
(HFPO), a vertically gradient polymer membrane was fabricated with a nanoscale gradient
via CVD.[37] The scheme for producing gradient copolymer materials is shown in [Figure 3]D. The compositional gradient of PV4D4 and the polyampholyte poly(2-carboxyethyl
acrylate-co-2-(dimethylamino)ethyl acrylate) (PCD) was fabricated via iCVD by controlling
the flow rate of monomers.[50] The flow rate of V4D4 was decreased over the processing time, while the flow rate
of PCD was increased.
3.4 Polymer Compartmentalization and Composites
VDP can compartmentalize polymer films by layer-by-layer polymerization without other
treatment. The physical and chemical properties can be controlled by changing the
monomer, substrate, and processing parameters. An asymmetric bilayer membrane consisting
of a sponge layer and a dense layer with a pillared structure surface was polymerized
under different processing conditions with various monomers via iCVD.[48] A free-standing membrane (FSM) comparting with the dense film and fibrous film of
parylene-C, which was polymerized via iCVD, was fabricated by a seven-step procedure.[89] Ran et al. fabricated a compartment GMA membrane with a dense and porous structure
by layer-by-layer coating with simultaneous phase separation during CVD.[178]
By designing the processing conditions and monomer, asymmetry in both the structure
and chemical properties can be obtained simultaneously.[161] A porous membrane from MAA, ethylene glycol diacrylate (EGDA), and GMA was coated
on a dense PGMA membrane via iCVD to improve the scratch resistance and solvent resistance,
and the dense PGMA layer promoted adhesion between the porous membrane and substrates.[51] The layer-by-layer compartmentalized membrane is shown in [Figure 3]E. A bilayer coating of a highly crosslinked PEGDA bottom layer and nanostructured
P(PFDA-co-EGDA) top layer was fabricated by a two-step deposition process via iCVD
to increase the surface hydrophobicity.[43]
VDP can be used to fabricate layer-by-layer membranes on 3D substrates. For example,
coaxial nanotubes with a hydrogel core and a shape memory shell were demonstrated
by coaxial vapor deposition of poly(tert-butyl acrylate) and PHEMA, respectively, in an anodic aluminum oxide (AAO) template.[183]
A polymer membrane with compartments was fabricated via VDP. Chenʼs group provided
a multicomponent vapor-deposited porous (MVP) coating of functional poly-(p-xylylene) based on CVSD polymerization to fabricate various compartments.[98],[99] This method increases the versatility of making different multicomponent coatings
with asymmetric structures and chemical properties. It is worth mentioning that an
asymmetric hybrid coating of a porous particle-capsulated membrane could be produced
via the MVP coating. By making the ice template with different molecules or cells,
cell adhesion and differentiation were successfully controlled.[100]–[102]
For some applications, the composite material is necessary to maintain the physical
or chemical properties that the application needs. Here, we introduce some composite
membranes or particles produced via VDP. Poly(N,N-dimethylaminoethyl methacrylate-co-ethylene glycol dimethacrylate) (P(DMAEMA-co-EGDMA))
was iCVD-polymerized on candle soot (CS).[52] The CS@polymer composites were used as humidity sensors with outstanding humidity
sensing performance. Mark et al. fabricated two types of composite particles with
inorganic nanoparticles by combining iCVD and direct-current magnetron sputtering.
The scheme for procedures is shown in [Figure 3]F. First, a low-vapor liquid with embedded gold nanoparticles was capsuled with PTFE
particles, which enhanced the mechanical strength of the marble. Then, the spherical
marbles were vapor-deposited and polymerized with PPFDA or gold nanoparticles were
deposited before PPFDA deposition polymerization.[144] PPY was vapor-deposited and polymerized onto waste Si as the pre-product for the
N-doped carbon source. After carbonization, Si/N-doped carbon core-shell composites
were fabricated and provided a lower barrier of Li-ion transport energy.[184] Polyaniline was conformally coated on carbon nanotubes via oCVD at a low deposition
temperature.[81] Two-layer hybrid nano- and mesotubes were fabricated by deposition polymerization
of PPX and metal on degradable template polymer fibers (PLA, poly(L-lactide)) via
subsequent CVD.[103] A hybrid nanocomposite with graphene, dopamine, and PPY was fabricated for flexible
supercapacitor electrodes by coating PPY on dopamine-loaded graphene.[82]
3.5 From 2D to 3D
AAO templates are a standard tool for fabricating nanotubes. By VDP, nanotubes with
different polymers, such as PEDOT[83] and PPy[84], were made. Carbon nanotubes were produced after carbonizing the PPy nanotubes,
which were fabricated by VDP on an AAO template.[84] Coaxial nanotubes have been manufactured by sequence iCVD on an AAO template with
temperature-responsive poly(N-isopropylacrylamide) (PNIPAAm), pH-responsive PMAA and PHEMA.[53] Ozaydin Inceʼs group also reported various polymer nanotubes made from iCVD or oCVD
with AAO templates.[183],[185]–[187] By using the fiber template process (TUFT), PPX nanotubes and metal–PPX hybrid nanotubes
were fabricated.[103] PPX was first coated on degradable polylactic acid (PLA) template polymer fibers.
After removing the PLA fiber, a hollow tube of PPX was obtained. Combined with metal
deposition, a core-shell tube was fabricated.
Poly(4-vinylpyridine) and PHEMA polymer particles were polymerized in silicone oil
via sequential CVD.[54] The monomer was first condensed on the oil surface and then polymerized via a free
radical reaction. Chenʼs group reported a novel method to fabricate porous particles
with various structures and sizes via CVD.[93],[104] The particle size can be controlled by tuning the sublimation/deposition process.[104] More importantly, particles with growth factors, platelet-rich plasma, or live cells
were directly encapsulated in the membrane by VDP. This compartmentalized membrane
has been utilized to control cell growth.[100]–[102]
Franklinʼs group fabricated nonspherical polymer nanoparticles (PNPs) by condensed
droplet polymerization, which is similar to iCVD.[188] The nanoscale droplets were condensed on the PPFDA from the vapor-phase monomer
of HEMA firstly, then the free radical initial polymerization occurred after the vapor-phase
initiator (TBPO) was fed into the heated chamber (300 °C). The authors point out that
the shape, size, and intensity of PNPs could also be alternated by using various monomers,
tuning the surface energy of the base layer.
By depositing monomers on a drop of liquid, a curved polymer membrane could be fabricated.
This year, Yung-Chiang Liu et al. fabricated hybrid granular structures of parylene
C, a polystyrene layer, GlyCVD particles, SiO2, and carboxylated polystyrene particles by combining colloidal self-assembly and
CVD.[105] The processing illustration is shown in [Figure 3]G. By depositing the polymer on a glycerin drop, a granular structure membrane of
parylene C was obtained. After 5 days of incubation, human bone marrow mesenchymal
stem cells aggregated without a reduction in the cell activity.
Transformable compartmentalized microstrips, which can reversibly change the structure
between 2D and 3D, have been produced via VDP. Myung Seok Oh et al. demonstrated Janus
microstrips by coating PDVB on active microstrips.[55] The active microstrips were photopolymerized from PHEMA, poly((ethylene glycol)
diacrylate), AA, and the photoinitiator 2-hydroxy-2-methylpropiophenone. Then, the
Janus property was provided by the iCVD coating PDVB layer, which was not responsive
to pH changes. While increasing pH condition, the pH-responsive AA-containing microstrip
swelled, resulting in directional self-bending. The self-bending degree was affected
by the thickness changes of the active layer and passive layer, and a 3D microstructure
was formed under high pH conditions.
4. Applications
Synthesized polymers have been widely applied to surface modification and membrane
fabrication. Here, we discuss surface modification and membrane formation.
4.1 Surface Modification Coatings
Surface modification for various applications can be satisfied by proper coating polymers
to utilize the surface physicochemical properties. Controlling surface hydrophilicity
and hydrophobicity has drawn much interest in antibacterial,[189]–[191] corrosion resistance,[192]–[194] drug delivery,[195] gate dielectric,[69] and electrolyte[177] applications. The surface of a porous ceramic tube was modified into a hydrophobic
surface with PPFDA via iCVD to enhance the performance of membrane distillation by
limiting membrane wetting.[196] The polymer film also impacted droplet shedding and decreased the contact angle.
PEDOT was coated on layered oxide cathode materials via oCVD to improve the capacity
and thermal stability under high-voltage operation.[85] P(DMAEMA-co-EGDMA) was coated on a CS film via iCVD.[52] The polymer@CS composite was highly hydrophilic and had good sensitivity when used
as a humidity sensor. The PNIPAAm, which is sensitive to humidity, was coated on an
optical cavity via iCVD to demonstrate a humidity sensor.[56] An iCVD-polymerized gradient membrane of PV4D4 and PCD provided good antifouling
properties with the outer layer of pCD and strong substrate-independent adhesion of
PV4D4.[50] Poly(dimethyl amino methyl styrene-co-1H,1H,2H,2H-perfluorodecyl acrylate) (P(DMAMS-co-PFDA))
was modified on the negatively charged and hydrophilic surface of polyester textile
via iCVD to provide antifouling properties.[57] The schematic diagram of the coating process and antifouling is shown in [Figure 4]A. The hydrophobic PDP membrane exhibited excellent killing efficiency against gram-negative
Escherichia coli and gram-positive methicillin-resistant Staphylococcus aureus.
Figure 4 Surface modification. (A) Schematic diagram of the iCVD process for antifouling application.[57] Reprinted with permission from Ref. [57]. Copyright 2021 Elsevier. (B) P(HEMA-co-EGDMA)-coated SVP-PLA composite patch: (i)
composite patch and (ii) fluorescence imaging of human osteoblasts on the composite
patch and copolymer-coated patch[61] (scale bar = 20 µm). Reprinted from Ref. [61] published under a creative commons license (CC BY). (C) pH-responsive Janus membrane:
(i) illustration of the Janus membrane and (ii) the cumulated BSA concentration in
the feed and permeated cells.[68] Reprinted with permission from Ref. [68]. Copyright 2019 Elsevier. (D) The scheme of a hybrid dielectric and the device performance.[69] Reprinted with permission from Ref. [69]. Copyright 2018 American Chemical Society.
Zwitterionic polymers are commonly used in antifouling applications. The iCVD polymerized
2-hydroxyethyl methacrylate-co-perfluorodecyl acrylate (HEMA-co-PFDA), a zwitterionic
copolymer, also exhibited good resistance to organic fouling for assisting a reverse
osmosis (RO) membrane.[58] Poly[2-(dimethylamino)ethyl methacrylate-co-ethylene glycol dimethacrylate) (PDE)
was coated on a RO membrane via iCVD, and the zwitterionic structure was obtained
by reacting with 1,3-propane sultone. Then, the zwitterionic membrane was crosslinked
with EGDMA to prevent dissolution in water.[59]
Providing a specific interface with nanomembranes has played an important role in
biotechnology. Various surface properties can be obtained using different polymer
coatings to achieve applications. Poly(methylacrylic acid-ethylene glycol diacrylate)
(P(MAA-EGDA)) was coated on a PLA membrane to improve the hemocompatibility.[60] The negative carboxyl groups on P(MAA-EGDA) were hydrophilically interacting with
protein and platelets and electrostatically interacting with the amide groups of thrombin
to inhibit clotting.[60] A composite patch was modified with poly(2-hydroxyethyl methacrylate-co-ethylene
glycol dimethacrylate) (P(HEMA-co-EGDMA)) via iCVD to improve wettability and biocompatibility
and exhibited good cell interaction with human osteoblasts.[61] The composite patch and fluorescence imaging of human osteoblasts at 48 h culturing
are shown in [Figure 4]B. By coating the biocompatible poly(ethylene glycol dimethacrylate) (PEGDMA) via
iCVD, the morphology durability of gelatin nanofibers was improved without losing
cytocompatibility.[158] A hybrid polyionic nanocoating was fabricated by two-stage iCVD to graft polyionics
onto a polyionic poly(2-dimethylamino ethyl methacrylate-co-methacrylic acid-co-ethylene
glycol diacrylate) (PDME) membrane on neural microelectrodes to reduce microglial
adhesion and adsorption of laminin and bovine serum albumin (BSA).[62]
A hydrogel copolymerized from HEMA and EGDMA can change the indomethacin release behavior
by changing the composition of EGDMA.[63] When the EGDMA content increased, the crosslinker fraction increased, and the release
rate decreased. The hydrogels PHEMA and PMMA were coated on clotrimazole (CLOT)-loaded
cotton, PET fabrics, or polycaprolactone nanofibers via iCVD, which prevented sudden
drug release.[64]
Stimuli-responsive polymers can change properties by altering the environmental conditions,
such as pH, temperature, and water exposure. These properties can be used in providing
drug delivery, controlling permeation, and fabricating cell sheets. A thermoresponsive
poly(N-vinylcaprolactam) (PNVCL) surface was fabricated via iCVD on glass to provide the
surface with alterable hydrophilicity to thermally separate the cell sheet by lowering
the temperature.[65] Degradation and swelling could also be utilized for drug release. The pH-dependent
degradable poly(methacrylic anhydride) (PMAH) was coated via iCVD to capsulate a drug
within the microporous membrane.[66] The drug release rate was controlled by the degradation of PMAH resulting from the
pH increase. PMAA also showed good pH responsiveness to control drug release by polymer
swelling.[51] By polymerizing MAA, an epoxide-containing monomer (GMA), and a crosslinker (EGDA)
via iCVD, a robust porous polymer membrane for drug delivery and wound dressing was
fabricated. The pH-sensitive poly(methylacrylic acid-co-ethylene glycol dimethacrylate)
(p(MAA-co-EGDMA)) was conformally coated in the pore walls of AAO templates via iCVD.
The pore size change due to pH-responsive swelling controlled the permeation rate
of molecules.[67] Different pH-responsive polymers were coated in the pore walls at opposite sides
of the AAO templates via iCVD. The polymer-coated pores acted as controllable gates
at the opposite sides to block the molecular permeation individually.[68] The schematic of the Janus membrane and the protein concentration change in the
feed and permeated cells are shown in [Figure 4]C.
Coating with a specific polymer can also promote the performance of applications.
Coating the poly(hydroxyethyl methacrylate-co-ethylene glycol diacrylate) (poly(HEMA-co-EGDA))
hydrogel electrolyte via iCVD on a patterned nanostructure can be applied for 3D microbatteries.[141] The hydroxyl groups in the HEMA component promoted strong interactions with anions,
resulting in lithium salt dissociation enhancement. A homogenous organic–inorganic
hybrid membrane was vapor-deposited and polymerized from TMA, the vinyl monomer HEMA,
and the initiator TBPO via iCVD polymerization.[69]
The performance of the device with hybrid dielectric and the illustration of hybrid
dielectric are shown in [Figure 4]D. The organic thin-film transistors with the designed hybrid dielectrics exhibited
excellent flexibility and good dielectric performance. The heat transfer coefficient
of a vapor-side condenser was successfully enhanced by coating poly-(1H,1H,2H,2H-perfluorodecyl
acrylate)-co-divinyl benzene (p(PFDA-co-DVB)) on the metal tube.[202] VPP can be utilized to connect fibers. For instance, macroscopic graphene composite
webs were fabricated by CVD of polymerized polyacrylonitrile (PAN) on PAN fibers.[156] After carbonizing fibers at a high temperature (1000 °C), the PAN polymer was carbonized
with sp2-hybridized carbon atoms in the macroscopic graphene composite webs. The graphene
composite webs reveal outstanding electrical conductivity. PHEMA was modified in mesoporous
TiO2 via iCVD as a polymer electrolyte.[203] The efficiency of electrolyte dye-sensitized solar cells was enhanced compared to
that of liquid-filled devices, while PHEMA formed a stable gel electrolyte.
4.2 Membranes
Free-standing polymer films have been applied as filters, tissue scaffolds, and drug
delivery systems. A heat or solvent-removable layer is coated on the holder before
VDP. Below are some examples of CVD-polymerized free-standing films.
Five millimeter thick polymeric FSMs of nBA were fabricated by iCVD and crosslinked
with diethylene glycol divinyl ether (DEGDVE).[204] After dissolving the poly(acrylic acid) (PAA) layer, FSMs were obtained and combined
in a microfluidic device and showed 1.3 times the CO2 permeance compared to the control membrane.
A PHEMA FSM was fabricated via iCVD and is shown in [Figure 5]A.[197] The hydrophilic molecules showed a higher permeability coefficient because of the
polarities. The crosslinking ratio of the membrane affected the diffusion coefficient.
Jyun-Ting Wu et al. produced a prototype of a PPX intraocular lens (PPX-IOL) device
with functionalized PPXs via CVD encapsulation.[198]
[Figure 5]B shows the scheme of fabrication process and the image of prototype PPX-IOL. During
CVD encapsulation, the polymer was deposited on the placed liquid droplet and polymerized.
After photoimmobilization with thiol-PEGs and cysteine-containing peptides, the PPX-IOL
devices showed cell resistance and cell attachment.
Figure 5 Free-standing membrane fabrication. (A) PHEMA membrane and the diffusion cell for
the permeation test[197] Reprinted with permission from Ref. [197]. Copyright 2014 John Wiley and Sons. (B) Schematic diagram of fabricating poly-para-xylylene (PPX) intraocular lens and the image of PPX intraocular lens[198] Reprinted with permission from Ref. [198]. Copyright 2015 American Chemical Society.
4.3 Device Fabrication
VDP has the advantage of preparing pure and conformal membranes on various substrates.
By combining with other techniques, such as functionalization, VDP has been employed
as a modification process for producing devices, such as electric devices, biomedical
devices, and sensors. For example, iCVD was used to fabricate a conformal copolymer
in a microfluidic sensor. Jung et al. produced DNA hydrogels by the isothermal amplification
of complementary target (DhITACT) system in a microfluidic channel with an iCVD-coated
copolymer ([Figure 6]A).[199] PV4D4 was conformally modified in the channel. It needs to be emphasized that the
iCVD process can directly modify the inside wall of microfluidic channels without
pretreatment and coat a large number of devices at once. Then, the copolymer-coated
channel was immobilized with DNA primer via a thiol-end click reaction. The DhITACT
system showed rapid diagnosis with high sensitivity for MERS (Middle East respiratory
syndrome) coronavirus.
Figure 6 Vapor deposition polymerization for device fabrication. (A) Microfluidic device for
target virus detection.[199] Reprinted with permission from Ref. [199]. Copyright 2016 John Wiley and Sons. (B) Schematic diagram of hybrid dielectric
synthesis.[200] Reprinted with permission from Ref. [200]. Copyright 2021 John Wiley and Sons. (C) Copolymer-based ReRAM device and its stability
test results.[201] Reprinted with permission from Ref. [201]. Copyright 2021 John Wiley and Sons.
Recently, the iCVD has been used to coat ultra-thin polymers for producing organic/inorganic
hybrid dielectrics with good performance.[200] A scheme of hybrid dielectric fabrication is shown in [Figure 6]B. Poly-2-hydroxyethyl methacrylate-co-1,3,5-trivinyl-trimethyl-cyclotrisiloxane
(PHEMA-co-V3D3) was coated on a Ni bottom electrode in a resistive random access memory
(ReRAM) device via iCVD, and the copolymer-based ReRAM device showed high endurance
properties.[201] The PV3D3 dielectric was found to have a more stable and robust insulating property
than the pHEMA dielectric, preventing soft breakdown behavior. The ReRAM device with
the copolymer dielectric achieved both low switching power and high endurance characteristics.
The copolymer ReRAM on flexible PEN and the performance under different bending radii
are shown in [Figure 6]C.
5. Conclusions and Outlook
5. Conclusions and Outlook
In vapor deposition, the coating component evaporates into atoms, molecules, or ions,
which then condense on the surface of the substrate. Vapor deposition is an excellent
technique for fabricating insoluble or infusible polymer thin films such as fluoropolymers,
crosslinked organic materials, and conjugated polymers. Unlike PVD methods such as
sputtering or evaporation, which use atoms as the film-building species, CVD uses
reactive molecules or radicals to fabricate polymeric films through a chemical reaction.
The most common CVD variations used to fabricate polymer thin films are iCVD, piCVD,
PECVD, oCVD, and parylene CVD. The thin film properties, such as thickness, surface
morphology, and mechanical properties, vary depending on the vapor deposition process,
monomers, and substrates used to construct it. However, the thin film functionalities
are highly dependent on the functional groups of monomers. Covalent bonding, surface
chemistry such as alkyne–azide “click” chemistry, and other chemical reactions are
made possible by these functional groups. The control over these properties and functions
is provided by the CVD technique, demonstrating that CVD is a versatile way to fabricate
thin films that can be tailored to fit the needs. Nanotopography and a porous structure
can be achieved by modifying the processing settings during deposition or combining
other processing techniques. In addition, the patterning process has the capability
of designing surfaces with anisotropic chemistry and topography for subsequent functionalization
as modifications for specific purposes. Producing a gradient in terms of the chemical
characteristics, thickness, and porosity of the material is possible with the assistance
of other methods. In addition, 3D particles, tubes, and curved FSMs have also been
constructed. Surface modification by VDP demonstrates its versatility for a wide range
of applications after being compartmentalized with different types of materials. With
the increasing demand and sophistication of the interface requirements for prospective
materials, the capabilities of an interface modification tool (surface modification
and/or a coating) are expected with (i) multiple functions from both physical and
chemical aspects and/or their combined properties, (ii) controlled configuration and
compositions of these physical and chemical properties from 2D to 3D and in selected
locations (anisotropic control), (iii) increased compatibility with a wide spectrum
of substrate materials and devices without compromising the fabrication process or
the intended functionality, (iv) easy accessibility of the fabrication process, cost,
and the possibility of mass production for industrialization applications, (v) sustainable
presentation of the properties for prolonged cycles and usages, and (vi) combination
of different coating techniques in a complimentary and combinatorial fashion. We expect
the advancement of the vapor deposition and coating technologies of polymers to expand
beyond the discussions, and new researchers in this field will benefit from this review
and bring new insights into vapor deposition coatings in the future.
Funding Information
The authors gratefully acknowledge funding support from the National Science and Technology
Council of Taiwan (111-2221-E-002-030-MY3; MOST 108-2221-E-002-169-MY3; 109-2314-B-002-041-MY3).
