[
    {
        "id": 1,
        "chunk": "# Amphiphilic Antifogging/Anti-icing Coatings Containing POSS-PDMAEMA-b-PSBMA  \n\nChuan Li, Xiaohui Li, Chao Tao, Lixia Ren, Yunhui Zhao, Shan Bai, and Xiaoyan Yuan ACS Appl. Mater. Interfaces, Just Accepted Manuscript $\\cdot$ DOI: 10.1021/acsami.7b05286 • Publication Date (Web): 20 Jun 2017 Downloaded from http://pubs.acs.org on June 24, 2017",
        "category": " References"
    },
    {
        "id": 2,
        "chunk": "# Just Accepted  \n\n“Just Accepted” manuscripts have been peer-reviewed and accepted for publication. They are posted online prior to technical editing, formatting for publication and author proofing. The American Chemical Society provides “Just Accepted” as a free service to the research community to expedite the dissemination of scientific material as soon as possible after acceptance. “Just Accepted” manuscripts appear in full in PDF format accompanied by an HTML abstract. “Just Accepted” manuscripts have been fully peer reviewed, but should not be considered the official version of record. They are accessible to all readers and citable by the Digital Object Identifier $(\\mathsf{D O}|\\oplus)$ . “Just Accepted” is an optional service offered to authors. Therefore, the “Just Accepted” Web site may not include all articles that will be published in the journal. After a manuscript is technically edited and formatted, it will be removed from the “Just Accepted” Web site and published as an ASAP article. Note that technical editing may introduce minor changes to the manuscript text and/or graphics which could affect content, and all legal disclaimers and ethical guidelines that apply to the journal pertain. ACS cannot be held responsible for errors or consequences arising from the use of information contained in these “Just Accepted” manuscripts.",
        "category": " Introduction"
    },
    {
        "id": 3,
        "chunk": "# Amphiphilic Antifogging/Anti-icing Coatings Containing POSS-PDMAEMA-b-PSBMA  \n\nChuan Li, Xiaohui Li, Chao Tao, Lixia Ren, Yunhui Zhao, Shan Bai, and Xiaoyan Yuan School of Materials Science and Engineering, and Tianjin Key Laboratory of Composite and Functional Materials, Tianjin University, Tianjin 300072, China  \n\nKEYWORDS: amphiphilic coating, semi-interpenetrating polymer network, POSS, antifogging, anti-icing  \n\nABSTRACT: Highly transparent antifogging/anti-icing coatings were developed from amphiphilic block copolymers of polyhedral oligomeric silsesquioxane-poly[2- (dimethylamino)ethyl methacrylate]-block-poly(sulfobetaine methacrylate) (POSS-PDMAEMA$b$ -PSBMA) with a small amount of ethylene glycol dimethacrylate (EGDMA) via UV-curing. The excellent antifogging properties of the prepared coatings were originated from the hygroscopicity of both PDMAEMA and PSBMA blocks in the semi-interpenetrating polymer network (SIPN) with polymerization of EGDMA, and hydrophobic POSS clusters aggregated on the surface. PDMAEMA with a lower critical solution temperature and PSBMA with an upper critical solution temperature in the block copolymers facilitated dispersion and absorption of water molecules into the SIPN coatings, fulfilling the enhanced antifogging function. Analysis of differential scanning calorimetry further confirmed that there were bond water and non-freezable bond water in the SIPN coatings. The amphiphilic SIPN coatings exhibited the anti-icing ability with a freezing delay time of more than $2~\\mathrm{min}$ , owing to the aggregation of hydrophobic POSS groups and the self-lubricating aqueous layer generated by non-freezable bond water on the surface. The prepared transparent antifogging/anti-icing coatings could have novel potential applications in practice.",
        "category": " Abstract"
    },
    {
        "id": 4,
        "chunk": "# INTRODUCTION  \n\nFormation of fog is ascribed to condensed water droplets caused by unexpected changes in temperature and humidity, bringing about optical opaque of transparent surfaces such as windshields, periscopes, display devices in the analytical instruments.1-3 To alleviate the trouble of fog, superhydrophilic polymer films have been extensively investigated because their surfaces can quickly absorb and spread condensed water droplets, forming a continuous aqueous layer that allows light to pass through without too much scattering.2-5 Superhydrophobic surfaces were also applied to mitigate fogging problems and impart these surfaces antifogging performance.6,7 Nevertheless, preparation of highly transparent antifogging coatings still remained a challenge, especially for the meticulous preparation process of the superhydrophilic and superhydrophobic surfaces with micro/nano-structures that possibly limited their applications.5-7  \n\nIn the recent years, amphiphilic coatings have been developed to achieve effective antifogging properties via the synergistic strategy of hydrophilic and hydrophobic components.3,8-10 Cohen et al. prepared zwitter-wettable antifogging coatings by layer-by-layer assembly from chitosan and Nafion with a nanoscale thin hydrophobic capping layer, enabling water vapor to diffuse rapidly into the underlying hydrophilic coatings.8 Triggered by the hydrophilic/hydrophobic balance, Ming et al. fabricated a semi-interpenetrating polymer network (SIPN) coating from an acrylate copolymer, namely, poly(2-(dimethylamino)-ethyl methacrylate-co-methyl methacrylate) via polymerization of ethylene glycol dimethacrylate (EGDMA) to achieve the antifogging purpose.9,10 In contrast to superhydrophilic or superhydrophobic antifogging coatings, amphiphilic coatings displayed high initial water contact angles which subsequently decreased to low values within a period of time.8,9 Water or vapor molecules could be rapidly absorbed from the surrounding environment and spread in the coatings by hydrogen-bond interaction in the form of non-freezable water, rather than condensed as drops of liquid water on the surface.2-4,8-10 The hydrophobicity of amphiphilic coatings also facilitated dispersion of water molecules into the coatings.3,8-10  \n\nIn addition to the antifogging capability, the amphiphilic coatings exhibited frost-resisting3,10 or anti-icing properties.11,12 For example, a small amount $(1w t\\%)$ of amphiphilic copolymer polydimethylsiloxane (PDMS)-poly(ethylene glycol) (PEG, $25\\%$ ) was introduced in the smooth PDMS coating, and then a viscous lubricating liquid-like layer could generate at the coating surface which exhibited icephobicity with lower ice adhesion strength.11 Amphiphilic crosslinked hyperbranched fluoropolymers containing water-absorbing PEG chains also demonstrated anti-icing candidates for potential engineering applications.12 Alternatively, the surfaces consisting of cross-linked hygroscopic polymers such as poly(acrylic acid) could be infused with water, bringing about a self-lubricating aqueous layer for the anti-icing purpose.13,14 Moreover, slippery liquid infused nanostructured surfaces could exhibit ice-repellency behaviors,15,16 as well as excellent optical transparency.17 The aqueous layer self-lubricating coatings with distinguished antifogging/anti-icing abilities would exhibit a great advantage in the practical applications.11-14  \n\nAs we know, dual-thermosensitive block copolymers could be prepared from a lower critical solution temperature (LCST) polymer such as poly( $N.$ -isopropylacrylamide) and poly(N,Ndimethylaminoethyl methacrylate) (PDMAEMA), and an upper critical solution temperature (UCST) polymer such as zwitterionic poly(sulfobetaine methacrylate) (PSBMA) or a random copolymer of poly(acrylamide-co-acrylonitrile).18-20 The random or block copolymers could display both LCST and UCST characteristics in the aqueous solution,18-20 even though they were grafted from silica nanoparticles.18 Thus, it can be assumed that antifogging/anti-icing coatings can be developed by combining PDMAEMA with LCST and PSBMA with UCST that could possibly give rise to a self-lubricating aqueous layer when exposed to water or vapor, and synergistically enhance the antifogging and anti-icing performances. Meanwhile, PDMAEMA was chosen as the main part of the amphiphilic polymers because of its good film-forming property on substrates and fine stability. On the other hand, due to strongly electrostatic and hydrogen-bond interactions with water, zwitterionic PSBMA could regulate and control the hydrophilcity of POSS-PDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA and enhance the antifogging/anti-icing performances of the amphiphilic SIPN coatings. Additionally, the zwitterionic PSBMA component could possibly reduce the freezing point of water as stated in the references.21,22  \n\nAccording to our previous studies on polyhedral oligomeric silsesquioxane (POSS)-containing fluorosilicone block copolymers, POSS groups with low surface energy could migrate and aggregate on the coating surfaces, endowing them with hydrophobicity for anti-icing.23-26 By integrating POSS with both PDMAEMA and PSBMA via atom transfer radical polymerization (ATRP), in this work, we prepared the amphiphilic SIPN coatings from POSS-PDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ - PSBMA block copolymers with a small amount $(10w t\\%)$ of EGDMA via UV-curing. We supposed that PDMAEMA and PSBMA blocks in the cross-linked PEGDMA network coupled with hydrophobic POSS groups could facilitate absorption of water or vapor molecules into the coatings to enhance the antifogging performance. Also, the amphiphilic SIPN coating was expected to decrease the water freezing-point by forming a self-lubricating aqueous layer at the surface so as to keep high transmittance under foggy conditions and display the anti-icing properties.",
        "category": " Introduction"
    },
    {
        "id": 5,
        "chunk": "# EXPERIMENTAL SECTION  \n\nSynthesis of POSS-PDMAEMA- $\\mathbf{\\nabla}\\cdot\\mathbf{b}$ -PSBMA.  The POSS-PDMAEMA- $b$ -PSBMA block copolymers were synthesized via ATRP of DMAEMA by using POSS-Br as an initiator according to the reference,27 and followed by ATRP of SBMA by using POSS-PDMAEMA-Br as a macroinitiator (Scheme 1). Three POSS-PDMAEMA- $b$ -PSBMA block copolymers with different polymerization degrees were prepared, while block copolymer PDMAEMA- $b$ -PSBMA without POSS by using ethyl-2-bromoisobutanoate as the initiator was also synthesized as control. According to the references, stronger hydrogen-bonded water molecules can form on the zwitterionic SBMA surfaces rather than on the surface of PEG,28 and a small amount of SBMA in the PDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA block copolymers still exhibited dual-thermoresponsive performance.20 Given that PDMAEMA chains played a key role in antifogging,9,10 we further designed the block copolymers with a higher DMAEMA content. In order to obtain similar molar ratios of DMAEMA to SBMA, three block copolymers, i.e., POSS-PDMAEMA ${50}$ -bPSBMA7, POSS-PDMAEMA ${}_{70}$ - $\\boldsymbol{\\cdot}\\boldsymbol{b}$ -PSBMA10 and POSS-PDMAEMA90- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA13 were synthesized. Compositions of the prepared block copolymers, abbreviated as POSS- $\\mathrm{\\cdotD}_{50^{-}}b{-}\\mathrm{S}_{7}$ , POSS- $\\mathrm{\\cdotD}_{70^{-}}b{-}\\mathrm{S}_{10}$ , P $\\mathrm{OSS-D}_{90^{-}}b.$ and $\\mathrm{D}_{50}–b–\\mathrm{S}_{7}$ , respectively, are shown in Table 1. Detailed synthesis of the block copolymers and their characterizations by $\\mathrm{^1H}$ nuclear magnetic resonance ( $\\mathrm{^{1}H}$ NMR), Fourier transform infrared (FTIR), gel permeation chromatography (GPC) and thermogravimetric analysis (TGA) are given in the Supporting Information Figures S1-S4.  \n\nScheme 1.  Schematic illustration of synthesis of POSS-PDMAEMA- $b$ -PSBMA  \n\n![](images/bd421c33bf100bc63ce88cdb066d41a5231659d7e0bb9d632aa5ac0cac5ccd46.jpg)  \n\nTable 1. Compositions of the prepared block copolymers   \n\n\n<html><body><table><tr><td rowspan=\"2\">Sample</td><td>Feeding composition</td><td>Molar composition</td><td rowspan=\"2\">Mna) (×104)</td><td rowspan=\"2\">PDI</td></tr><tr><td>DMAEMA:SBMA (mol:mol)</td><td>DMAEMA:SBMA in the copolymer a) (mol:mol)</td></tr><tr><td>POSS-D50-b-S7</td><td>50:7</td><td>43:7 (6.14:1)</td><td>0.97</td><td>1.07</td></tr><tr><td>POSS-D7o-b-S10</td><td>70:10</td><td>65:11 (5.91:1)</td><td>1.43</td><td>1.08</td></tr><tr><td>POSS-D90-b-S13</td><td>90:13</td><td>95:15 (6.33:1)</td><td>2.02</td><td>1.11</td></tr><tr><td>D50-b-S7</td><td>50:7</td><td>40:11 (3.64:1)</td><td>0.96</td><td>1.19</td></tr></table></body></html>\n\na) The molar composition and the number-average molecular weight of the POSS-PDMAEMA-bPSBMA block copolymers (abbreviated as POSS- $\\mathrm{\\cdotD}_{50}{\\mathrm{-}}b{\\mathrm{-}}\\mathrm{S}_{7}$ , POSS- $\\mathrm{\\cdotD}_{70^{-}}b{\\cdot}\\mathrm{S}_{10}$ and POSS- $\\mathrm{\\bfD}_{90}–b–\\mathrm{S}_{13},$ , respectively) were estimated by $^1\\mathrm{H}$ NMR spectra, and the result of PDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA (abbreviated as $\\mathrm{D}_{50}–b–\\mathrm{S}_{7}$ ) was determined by GPC.  \n\nPreparation of the SIPN Coatings.  A given amount of the block copolymer (POSS- $\\cdot\\mathrm{D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ , POSS- $\\cdot\\mathrm{D}_{70}{-}b{-}\\mathrm{S}_{10}$ , $\\mathrm{POSS-D}_{90}–b–\\mathbf{S}_{13}$ , or $\\mathrm{D}_{50}–b–\\mathrm{S}_{7},$ ) was dissolved in 2,2,2-trifluoroethanol to prepare a $25~\\mathrm{mg/mL}$ polymer solution. EGDMA ( $10\\mathrm{{wt\\%}}$ based on the copolymer) and Igracure 2959 UV photoinitiator $(2\\mathrm{wt\\%})$ were also added. The polymer coatings were prepared by casting $0.2~\\mathrm{mL}$ of the polymer solution onto a half of a clean glass slide (both sides), and then placing them under UV conditions $365~\\mathrm{nm}$ , 15 W, 1800 s) in a XL-1000 ultraviolet cross-linker apparatus (USA) for polymerization of EGDMA. The SIPN coatings containing the block copolymer POSS- $\\mathrm{\\cdotD}_{50}–b–\\ensuremath{\\mathrm{S}}_{7}$ , POSS- ${\\bf\\cdot D}_{70}$ -b-S10, POSS- $\\mathrm{\\cdotD}_{90}–b–\\mathrm{S}_{13}$ and $\\mathrm{D}_{50}–b–\\mathrm{S}_{7}$ , denoted as C-POSS- $\\cdot\\mathrm{D}_{50}{-}b{-}\\mathrm{S}_{7}$ , C-POSS- $\\cdot\\mathrm{D}_{70}{-}b{-}\\mathrm{S}_{10}$ , C-POSS- $\\mathrm{D}_{90}–b–\\mathrm{S}_{13}$ and $\\mathrm{C-D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ , respectively, were obtained by further air-drying at room temperature. The thickness of the obtained SIPN coatings was about $10\\upmu\\mathrm{m}$ .  \n\nCharacterizations.  Atomic force microscope (AFM) images were obtained by a CSPM5500A microscope AFM machine (Benyuan Nano-Instruments, China) equipped with an E-type vertically engaged piezoelectric scanner and operated in a tapping-mode at room temperature. X-ray photoelectron spectroscopy (XPS) measurements were performed on a Perkin-Elmer PHI 5000C ECSA system (USA), utilizing an excitation source of Al Kα radiation under a pressure of ${\\sim}6.7\\times10^{-6}$ Pa at $45^{\\circ}$ . Water contact angles of the SIPN coatings and their evolution were recorded by a JC2000D contact angle meter (Shanghai Zhongchen Equipment Co. Ltd., China) to examine the wettability of the samples with deionized water drops $(5\\upmu\\mathrm{L})$ .  \n\nAntifogging Tests.  The antifogging property was tested with the hot-vapor and cold-warm methods, separately. Generally, the glass slide covered by the SIPN coatings on the half was put over hot vapor (above about 5 cm high) on top of a glass beaker which contained hot water $(\\sim80$ $^{\\circ}\\mathrm{C}$ , $100\\%$ relative humidity), and the sample transparency was recorded immediately. In addition, the appearance of the samples was recorded quickly when they were exposed to a warm, humid environment ${\\mathrm{\\sim}}20~^{\\circ}\\mathrm{C},$ , $55\\%$ relative humidity) right after being stored in a ${\\displaystyle-20~^{\\circ}C}$ freezer for $45\\mathrm{\\min}$ . The transmittance of the samples was also measured in a 722s visible spectrophotometer (Shanghai Jinghua Technology Instrument Co. Ltd., China) ranging from 400 to $800\\mathrm{nm}$ for the quantitative measurement.  \n\nAnti-icing Tests.  The freezing delay time $(T_{\\mathrm{D}})$ of water droplets on the SIPN coatings was measured to test the anti-icing performance. The specimen was placed on a cold-plate (Tianjin Jing Yi Industry & Trade Co. Ltd., China) which was controlled at $-15~^{\\circ}\\mathrm{C}$ . Once a deionized water droplet $(5\\upmu\\mathrm{L})$ dropped on the coating surface, its appearance was recorded in every second, and the time when the water droplet became ice completely, i.e., when a sharp tip appeared on the droplet top, was regarded as the freezing delay time.  \n\nDifferential Scanning Calorimetry (DSC) Analysis.   The bond water amount in the SIPN coatings was analyzed by DSC (TA Q2000, USA). The samples for the DSC measurements containing a certain amount of deionized water were prepared by adding water into the SIPN coatings (about $4{\\sim}5\\ \\mathrm{mg}$ ) which were scraped from the glass slide. The sample was kept and stabilized in the aluminium pan for 10 days at room temperature. When no mass changes were confirmed in the several days, the samples were tested in the following a procedure by purging nitrogen gas. The sample was first cooled from 20 to $-70~^{\\circ}\\mathrm{C}$ at a cooling rate of $5~{^\\circ}\\mathrm{C}/\\mathrm{min}$ , and maintained for 3 min. Then, it was heated to $20~^{\\circ}\\mathrm{C}$ at a heating rate of $5~{\\mathrm{{^{\\circ}C/m i n}}}$ , and subsequently held at $20~^{\\circ}\\mathrm{C}$ for around $3~\\mathrm{min}$ . The cooling-heating cycle was also conducted in the same manner at heating/cooling rates of 10 and $15~\\mathrm{{^{\\circ}C/m i n}}$ , respectively. The total water content $(W_{\\mathrm{c}})$ , the freezable water content $(W_{\\mathrm{f}})$ , the non-freezable bond water content $(W_{\\mathrm{nfb}})$ and the bond water content $(W_{\\mathfrak{b}})$ in the samples were calculated according to the following equations.29-33  \n\n$$\n\\begin{array}{r l}&{W_{\\mathrm{c}}=m_{\\mathrm{w}}/m_{\\mathrm{c}}}\\\\ &{W_{\\mathrm{f}}=A_{\\mathrm{c}}/(334\\cdot m_{\\mathrm{c}})}\\\\ &{W_{\\mathrm{nfb}}=W_{\\mathrm{c}}\\cdot W_{\\mathrm{f}}}\\\\ &{W_{\\mathrm{b}}=W_{\\mathrm{fb}}+W_{\\mathrm{nfb}}}\\end{array}\n$$  \n\nwhere, $m_{\\mathrm{w}}$ and $m_{\\mathrm{c}}$ represent the masses of water and the coating, respectively, in the samples, and $A_{\\mathrm{c}}\\left(\\mathrm{J/g}\\right)$ refers to the integral melting peak area in the heating curves. Here, we hypothesize that the enthalpies of both free and freezable water are equal to $334\\ \\mathrm{J/g}$ , the specific heat of water fusion.29 During the analysis, the freezable bond water content $(W_{\\mathrm{fb}})$ was corresponding to the area of the symmetric peak at around $-15^{\\circ}\\mathrm{C}$ in the heating curves, and the free water content $(W_{\\mathrm{ff}})$ (that is freezable) was the difference between Wf and Wfb according to the references.29,30 Therefore, the bond water content $(W_{\\mathfrak{b}})$ was the sum of $W_{\\mathrm{fb}}$ and $W_{\\mathrm{nfb}}$ . The melting temperatures of the freezable bond water $\\left(T_{\\mathrm{fbm}}\\right)$ and the freezable free water $\\left(T_{\\mathrm{ffm}}\\right)$ were designated as the peak temperatures of the fitting symmetric peak and the melting peak, respectively in the heating curves of the samples.",
        "category": " Materials and methods"
    },
    {
        "id": 6,
        "chunk": "# RESULTS AND DISCUSSION  \n\nAntifogging Properties.  The antifogging performance of the SIPN coatings was demonstrated with the hot-vapor and cold-warm methods. For the hot-vapor method, the glass slides with both sides partially coated by the SIPN coatings were placed 5 cm high above boiling water ${\\mathrm{'}}80{}^{\\circ}\\mathrm{C},$ , $100\\%$ relative humidity). As shown in Figure 1A, it can be seen that the uncoated areas of the bare glass slides were apparently covered by small condensed water droplets of hot vapor, resulting in optical opacity. In contrast, the other halves of the glass slides with the SIPN coatings still remained highly transparent. The excellent antifogging properties of all the samples could be attributed to the hydrophilic PDMAEMA and PSBMA blocks in the copolymers and the cross-linked PEGDMA network, which allowed water molecules to be rapidly absorbed into the SIPN coating and possibly spread over the coating surface, similar with the situation stated in the references.8,34 It was supposed that surface hydration of the prepared coatings could occur owing to the hydrogen-bonded interactions of water molecules with PDMAEMA and PSBMA blocks as well as PEGDMA.28 When water molecules entered into the coatings, hydrogen bonds between water and polymer chains could be formed in the SIPN coatings at a molecular level due to the presence of oxygen atoms of ester and ether groups in PDMAEMA, PSBMA and PEGDMA chains as well as nitrogen atoms in the structure of PDMAEMA, ensuring the excellent optical transparency. Moreover, because of the electrostatic attraction of zwitterionic groups, the hydrogen-bonded interaction between hydrophilic PSBMA and water molecules is stronger than that between water and PDMAEMA or PEGDMA chains in the coatings.28,35  \n\n![](images/b0f89a3e31d15a43327375501360b06d6298ec7fddcb1f7304426c99aa17d942.jpg)  \n\nFigure 1. Photographs of the glass slides partially covered with the SIPN coatings containing POSS- $\\mathrm{\\cdotD}_{50^{-}}b{-}\\mathrm{S}_{7}$ (a), POSS- $\\mathrm{\\cdotD}_{70}$ -b-S10 (b), POSS- $\\mathrm{.D}_{90}$ -b-S13 (c) and $\\mathrm{D}_{50}–b–\\mathrm{S}_{7}$ (d), respectively over boiling water ${\\sim}80~^{\\circ}\\mathrm{C},$ , $100\\%$ relative humidity) (A), and exposed quickly at ambient conditions 1 ${\\sim}20^{\\circ}\\mathrm{C}$ , $55\\%$ relative humidity) right after being stored at ${\\displaystyle-20~^{\\circ}C}$ for 45 min (B).  \n\nIn addition, when the temperature exceeded LCST (about $48~^{\\circ}\\mathrm{C})$ ) of PDMAEMA,20 the random coil conformation of the PDMAEMA chains tended to collapse due to the break of hydrogen-bonded interactions between the polymer and water molecules, resulting in the gathering tendency of PDMAEMA chains.20 The PDMAEMA chains, however, were restricted by the cross-linked network and could not aggregate to some extent. Therefore, the contractive force caused by PDMAEMA chains gathering could give rise to free voids for water molecules dispersion in the SIPN coatings.  \n\nThe antifogging performance of the SIPN coatings was also evaluated with the cold-warm method. The SIPN coatings were first stored in a $-20\\ ^{\\circ}\\mathrm{C}$ freezer for $45\\ \\mathrm{min}$ and then rapidly exposed to a warm, humid environment ( ${\\sim}20~^{\\circ}\\mathrm{C}$ , $55\\%$ relative humidity). As shown in Figure 1B, the uncoated parts of the glass slides were fogged severely and the words and patterns under the container became heavily blurred due to light scattering. In contrast, the coated parts displayed high transparency, indicating the excellent antifogging performance of the SIPN coatings. When water molecules were absorbed in the coatings, hydrogen bonds between water and the polymer molecules were subsequently generated at a molecular level.28 Additionally, when the temperature was inferior to UCST $({\\sim}5^{\\ \\circ}\\mathrm{C})$ of PSBMA,20 the random coil of the PSBMA chains tended to collapse due to the strong inter-chain ionic interactions between PSBMA chains, resulting in gathering tendency of PSBMA chains.18-20 Therefore, water molecules were conducive to well dispersion in the SIPN coatings, which was attributed to the contractive force generated by the trend of gathering of PSBMA blocks under the limitation of the cross-linked PEGDMA structure.  \n\nThe antifogging properties were quantitatively characterized by measuring the transmittance of the bare glass and the coated parts of the glass slides in range of visible light wavelength from 400 to $800\\ \\mathrm{nm}$ (Figure 2). The optical transmittances of C-POSS- $\\mathrm{\\cdotD}_{50^{-}}b{-}\\mathrm{S}_{7}$ , C-POSS- ${\\bf\\cdot D}_{70}$ -b-S10, C-POSS- $\\mathrm{D}_{90}–b–\\ensuremath{\\mathrm{S}}_{13}$ and $\\mathrm{C}{\\cdot}\\mathrm{D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ were $87.2{\\sim}89.2\\%$ , $88.0{\\sim}90.2\\%$ , $89.0{\\sim}91.2\\%$ and $85.9\\sim88.6\\%$ , respectively, which were quite similar to that of the bare glass $(85.1{\\sim}91.0\\%)$ ). The transmittance of the SIPN coatings containing POSS-PDMAEMA-b-PSBMA slightly increased with the rise of the molecular weight of the block copolymers, and all the SIPN coatings with or without POSS exhibited minor differences in the transmittance (Figure 2A). As shown in Figure 2B, during the cold-warm antifogging test, the transmittance of the bare glass decreased sharply to about $61.5{\\sim}63.2\\%$ due to the formation of fog on the surface. The transmittance of the SIPN coatings containing POSS- $\\mathrm{\\cdotD}_{50}–b–\\mathrm{S}_{7}$ , POSS- $\\mathrm{\\cdotD}_{70^{-}}b{-}\\mathrm{S}_{10}$ and POSS- $\\mathrm{\\cdotD}_{90}–b–\\mathrm{S}_{13}$ still remained $87.1{\\sim}89.8\\%$ , $87.1{\\sim}90.0\\%$ and $88.0{\\sim}90.4\\%$ , respectively, with trivial variations compared to the values before tests, showing excellent antifogging performance. The SIPN coating containing $\\mathrm{D}_{50}–b–\\mathrm{S}_{7}$ without POSS became $86.4{\\sim}88.7\\%$ , also exhibiting good antifogging property but inferior to the coatings containing POSS related copolymers. It was suggested that there was an important effect of hydrophobic POSS groups on the antifogging performance of the SIPN coatings.  \n\n![](images/cfcea5cde85f49571ab5b43698c72a74ec489cce27747c040f098fd01e9f81aa.jpg)  \nFigure 2. Transmittance of the SIPN coatings before (A) and after stored at $-20~^{\\circ}\\mathrm{C}$ for $45\\mathrm{min}$ , and exposed quickly to a warm, humid surrounding ${\\sim}20^{\\circ}\\mathrm{C},$ , $55\\%$ relative humidity) (B).  \n\nFor different structures of the polymeric coatings with or without POSS, the $\\mathrm{C}{\\cdot}\\mathrm{D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ coating exhibited low transmittance before and after fogging in comparison with C-POSS- ${\\bf\\cdot D}_{50}$ -b$\\mathbf{S}_{7}$ , indicating that the incorporation of POSS led to an active effect on the transmittance of the coating. It was assumed that the aggregated POSS groups on the SIPN coating surfaces could facilitate water dispersion into the amphiphilic SIPN coatings. However, for the amphiphilic SIPN coatings with similar structures, the transmittance of the coatings slightly increased before and after fogging with the rise of the molecular weight of the POSS block copolymers. It was indicated that the introduction of POSS resulted in a little negative effect on the transmittance which did not decease too much. It was assumed that the POSS-PDMAEMA- $b$ -PSBMA copolymers could regulate and control the wettability of the amphiphilic SIPN coatings.  \n\nAdditionally, the SIPN coatings may possess the ability of “thermal remediation” because the score scratched by a clean blade could be healed by vapor. The score on the C-POSS- ${\\bf\\cdot D}_{70}$ -b-S10 coating disappeared completely when the sample was exposed over the hot vapor for 3 min as shown in the Supporting Information Figure S5. The phenomenon may be explained by the fact that the molecular chains of collapse could be reorganized under the drive of water vapor due to the partially cross-linked network of the SIPN coating as well as the hydrogen-bond interactions between water and the polymeric molecules.3,36 Moreover, the SIPN coatings demonstrated great stability when immersed in water, suggesting their long-lasting utilities as shown in the Supporting Information Figure S6. With the healable antifogging performance and stability, the SIPN coatings of the POSS-PDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA block copolymers could have versatile potential applications.  \n\nSurface Characteristics of the SIPN Coatings.  AFM was employed to observe the surface morphology of the SIPN coatings. As shown in Figure 3, all C-POSS- $\\mathrm{\\cdotD}_{50^{-}}b{-}\\mathrm{S}_{7}$ , C-POSS- ${\\bf\\cdot D}_{70}$ -b$\\mathrm{S}_{10}$ , C-POSS- $\\mathrm{\\cdotD}_{90}\\mathrm{-}b\\mathrm{-}\\mathrm{S}_{13}$ and $\\mathrm{C}{\\cdot}\\mathrm{D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ samples exhibited smooth coating surfaces. Their root mean square roughness $(R_{\\mathrm{q}})$ values were estimated at ca. 0.6, 0.8, 0.5 and $1.0\\mathrm{nm}$ , respectively. It was proved that an integrated film structure was successfully cross-linked by polymerization of EGDMA, endowing the SIPN coatings with preferable surface morphology.  \n\n![](images/c79a2515a1b5beec3d272085d88a553e15317a8d2e4a204d42f2e40a0dca1a3d.jpg)  \nFigure 3. AFM images over a scope of $10\\upmu\\mathrm{m}\\times10\\upmu\\mathrm{m}$ of the SIPN coatings containing POSS$\\mathrm{D}_{50}–b–\\mathrm{S}_{7}$ (a), POSS- ${\\bf\\cdot D}_{70}$ -b-S10 (b), POSS- $\\mathrm{D}_{90}–b–\\mathrm{S}_{13}$ (c) and $\\mathrm{D}_{50}–b–\\mathrm{S}_{7}$ (d).  \n\nSurface compositions of the SIPN coatings were measured by XPS. All the element percentages on the coating surfaces, i.e., C, N, O, S and Si are shown in Table 2. The theoretical bulk contents of Si element, calculated from the molecular weight of the copolymers and the SIPN coating compositions, are also introduced in Table 2. It can be seen that the surface Si amounts of the amphiphilic SIPN coatings containing POSS-PDMAEMA- $b$ -PSBMA copolymers detected by XPS were all higher than those of their bulk Si contents, respectively. It was suggested that POSS groups could possibly aggregate on the coating surfaces due to their low surface energy and endowed the SIPN surfaces with the hydrophobic property.24-26 ATR-FTIR spectra were also applied in order to analyze and confirm the chemical structure of the SIPN coatings containing $\\mathrm{POSS-D}_{50}–b–\\mathrm{S}_{7}$ , POSS- $\\mathrm{\\cdotD}_{70^{-}}b{-}\\mathrm{S}_{10}$ , $\\mathrm{POSS-D}_{90}–b.\\backslash$ and $\\mathrm{D}_{50}–b–\\mathrm{S}_{7}$ block copolymers, as shown in the Supporting Information Figure S7.  \n\nTable 2. Surface elemental atomic percentages of the SIPN coatings detected by XPS   \n\n\n<html><body><table><tr><td rowspan=\"2\">Sample</td><td>C1s</td><td>O1s</td><td>N1s</td><td>S 2p</td><td>Si 2p</td><td>Bulk Si</td></tr><tr><td>(atomic%)</td><td>(atomic%)</td><td>(atomic%)</td><td>(atomic%)</td><td>(atomic%)</td><td>(atomic%)</td></tr><tr><td>C-POSS-D50-b-S7</td><td>72.3</td><td>20.3</td><td>3.7</td><td>0.7</td><td>3.1</td><td>1.21</td></tr><tr><td>C-POSS-D7o-b-S10</td><td>72.9</td><td>19.9</td><td>3.6</td><td>1.2</td><td>2.5</td><td>0.82</td></tr><tr><td>C-POSS-D90-b-S13</td><td>70.2</td><td>21.2</td><td>3.5</td><td>0.9</td><td>4.2</td><td>0.58</td></tr><tr><td>C-D50-b-S7</td><td>79.1</td><td>17.9</td><td>2.3</td><td>0.5</td><td></td><td></td></tr></table></body></html>  \n\nIn order to further examine the morphology of aggregated POSS clusters in the SIPN coatings, the samples prepared by dropping a droplet of dilute copolymer solutions (1 wt% in trifluoroethanol) on copper grids and UV-curing were observed under a transmission electron microscope (TEM). As shown in the Supporting Information Figure S8, it can be found that the aggregated POSS clusters were well dispersed within the polymer matrix in the size of $10{\\sim}80~\\mathrm{nm}$ , coincided with the reference.37 The size of POSS aggregates tended to decrease with the increase of the relative molecular weight of POSS-PDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA due to the relative reduction of the POSS proportion in the copolymers. In fact, the size (less than $100\\ \\mathrm{nm},$ ) of the POSS clusters was far smaller than the wavelength of visible light, and hence, the optical properties exhibited trivial discrepancy between samples with and without POSS. Besides, the discrete POSS clusters on the coating surfaces would not affect the absorption of water molecules into the hygroscopic polymers, and play an important role in regulating and controlling the dispersion of water molecules in the coatings. The POSS clusters could be analogous to the outmost layer of hollow silica nanoparticles for antifogging and antireflective thin films as Zhang reported.38 Therefore, the surface structure of $\\mathrm{C}{\\cdot}\\mathrm{D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ coating lack of the POSS function was different from that of the coatings containing POSS-PDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA copolymers, exhibiting a little lower transmittance (Figure 2B) than the latter.  \n\nWettability of the SIPN Coatings.  Changes of the water contact angle (CA) values of the SIPN coatings with time were recorded carefully under ambient conditions for $150~\\mathrm{s}.$ . As shown in Figure 4A, all C-POSS $\\mathrm{\\cdotD}_{50}–b–\\mathrm{S}_{7}$ , C-POSS- $\\cdot\\mathrm{D}_{70}{-}b{-}\\mathrm{S}_{10}$ and C-POSS- $\\cdot\\mathrm{D}_{90}–b\\ –\\mathrm{S}_{13}$ coatings exhibited high initial CA values of around $105^{\\circ}$ , while the initial CA value of the $\\mathrm{C}{\\cdot}\\mathrm{D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ coating was about $60^{\\circ}$ . The results were coincided with the recent findings in the references that an effective antifogging coating could not be superhydrophilic.3,8-10 Particularly, the C-POSS$\\mathrm{D}_{90}–b–\\ensuremath{\\mathrm{S}}_{13}$ coating had a higher initial CA value $(105.8{\\pm}0.4^{\\circ})$ , followed by a rapid decrease to $43.3{\\pm}1.3^{\\circ}$ in 60 s and $31.4{\\pm}0.7^{\\circ}$ in $150\\mathrm{~s~}$ , which was mainly attributed to the discrete POSS clusters on the coating surface and water-absorbing polymer chains inside. During the measurement, the water CA values on all SIPN surfaces decreased rapidly in 30 s, similar to the situation of the coatings containing strongly hydrophilic polymers such as poly(vinyl alcohol)/poly(acrylic acid) and chitosan/carboxymethyl cellulose as Cohen et al. reported.4,8 The water CA value on all SIPN coatings decreased much more quickly at the early time due to water dispersion than water evaporation. It was suggested that water molecules could diffuse well into the SIPN coatings in a short time, similar to the results in the reference.8  \n\nIn order to further analyze the wettability of the SIPN coatings, the diameter development of the water droplets on the coating surfaces was also calculated as shown in Figure 4B. It can be seen that the diameter of the droplet on the bare glass was almost constant during the measurement period, while the diameter of the water droplet on the $\\mathrm{C}{\\cdot}\\mathrm{D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ coating increased by about $35\\%$ . However, the variation of the droplet diameters on the C-POSS- ${\\bf\\cdot D}_{50}$ -b-S7, C$\\mathrm{POSS-D}_{70}–b–\\mathrm{S}_{10}$ and $\\mathrm{C-POSS-D_{90}-}b{\\mathrm{-}}\\mathrm{S}_{13}$ coatings increased by $70\\%$ , $73\\%$ and $84\\%$ , respectively, demonstrating that the water droplets were fast spread on the coating surfaces containing the POSS related copolymers and well dispersed into the coatings. Moreover, the larger the polymer molecular weight was, the faster the water droplet spread. The C-POSS- $\\mathrm{\\DeltaD}_{90}–b–\\mathrm{S}_{13}$ with the highest molecular weight $(2.02\\times10^{4})$ of the block copolymer exhibited the fastest absorbed water process, whereas the SIPN coatings containing POSS- $\\mathrm{\\cdotD}_{50^{-}}b{-}\\mathrm{S}_{7}$ (with a molecular weight of ${0.97\\times10}^{4}$ ) and $\\mathrm{POSS-D}_{70}–b–\\mathrm{S}_{10}$ (with a molecular weight of $1.43\\times10^{4}$ ) demonstrated similar water-dispersion speeds. Thus, the enhanced antifogging property could be caused by the strong hydrophilic blocks embedded in cross-linked PEGDMA network and the hydrophobic POSS groups on the coating surfaces.  \n\n![](images/e65e6a7dfd16a4e4c6a16e31e1b739670499cd9151ea7c52c9ec3810a6499979.jpg)  \nFigure 4. Variation of the water contact angle (CA) values on the different SIPN coatings with  \n\ntime in 150 s (A), and the diameter evolution $(\\triangle D/D_{0})$ of the droplets on the coating surfaces during the recording period (B), where $\\triangle D{=}D{-}D_{0},{\\cal I}$ $D_{0}$ is the original diameter $\\scriptstyle(t=0\\ s)$ and $D$ is the diameter of the water droplet on the coating surface at a given time.  \n\nAnti-icing Properties.  The freezing delay time of water droplets on the SIPN coatings was recorded at $-15~^{\\circ}\\mathrm{C}$ to evaluate the anti-icing properties. As shown in Figure 5, it can be observed that the SIPN coating containing $\\mathrm{D}_{50}–b–\\mathrm{S}_{7}$ showed a short freezing delay time of $10\\mathrm{~s~}$ , i.e. the water droplet became ice as quickly as it was on the bare glass. In contrast, all the three coatings containing the POSS-PDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA block copolymers presented a freezing delay time of more than $124{\\mathrm{~s~}}$ , much longer than that of the $\\mathrm{C}{\\cdot}\\mathrm{D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ coating without POSS. Particularly, the C-POSS- $\\mathrm{\\cdotD}_{50^{-}}b{-}\\mathrm{S}_{7}$ coating exhibited a longer freezing delay time of 334 s than C-POSS- ${\\bf D}_{70}$ - ${b\\mathrm{-}}\\mathrm{S}_{10}$ and C-POSS- $\\mathrm{.D}_{90}$ -b-S13 with similar freezing delay times of about 124 s. This phenomenon could be attributed to the following reasons. Firstly, POSS groups with low surface free energy have the ability of improving the surface icephobicity as shown in POSS-containing methacrylate coatings.24,25,39 Secondly, a certain amount of water molecules could be interacted with the hydrophilic PDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA copolymers inside the cross-linked coatings as nonfreezable bond water through hydrogen bonds,8-10,28 and the freezing point of water could be decreased by the zwitterionic groups of PSBMA in the coatings.21 Finally, the POSSPDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA coating surfaces, that were comprised of hydrophobic POSS groups on the coating surfaces and hydrophilic components in the SIPN coatings, could motivate the formation of a self-lubricating aqueous layer,11,13,14 and subsequently endow the coatings with the anti-icing properties. In other words, the POSS clusters on the C-POSS- $\\mathrm{\\cdotD}_{50^{-}}b{-}\\mathrm{S}_{7}$ coating surface could give rise to a hydrophobic surface, whereas the hygroscopic PDMAEMA and PSBMA chains were well distributed beneath them. And then, a self-lubricating aqueous layer could form when the coating absorbed water molecules.13,16 The surface structure of the coating is similar with the self-lubricating water layer fabricated by cross-linked hygroscopic polymers inside the micropores of silicon wafer surfaces as Chen et. al. put forward.13 However, the hydrophilic $\\mathrm{C}{\\cdot}\\mathrm{D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ coating surface without hydrophobic components could be a reservoir of water molecules rather than generation of a self-lubricating aqueous layer.13,16  \n\n![](images/e642027f9b8e418f468c0f2f69c24488ab8b9e09830de8da08d9c1a6a4afbc86.jpg)  \n\nFigure 5. Optical images of the water droplets on the bare glass slide and the SIPN coatings containing $\\mathrm{POSS-D}_{50^{-}}b.$ , POSS- $\\mathrm{\\cdotD}_{70^{-}}b{-}\\mathrm{S}_{10}$ , POSS- $\\mathrm{\\cdotD}_{90}\\mathrm{-}b\\mathrm{-}\\mathrm{S}_{13}$ , and $\\mathrm{D}_{50^{-}}b{-}\\mathrm{S}_{7}$ during freezing process. The freezing delay time $(T_{\\mathrm{D}})$ of each sample was observed. The temperature of the coolplate was controlled at $-15^{\\circ}\\mathrm{C}$ .  \n\nIn fact, there were water molecules in the amphiphilic coatings surfaces to maintain the presence of the self-lubricating aqueous layer.11,13 The results of the freezing delay time for each sample exhibited a trend of decrease with the increase of the molecular weight of the copolymers. When the molecular weight of the copolymers was lower than a certain value, the total content of POSS aggregated on the coating surface would be higher, whereas the relative proportion of hydrophilic components dropped. The freezing process of a water droplet on the bare glass and the hydrophilic $\\mathrm{C}{\\cdot}\\mathrm{D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ coating without POSS presented much shorter delay times in about 10 s, very similar to the case of the general polyacrylate coating.40 With the contribution of POSS, the C-POSS- ${\\bf\\delta D}_{50}$ -b-S7, C-POSS- $\\cdot\\mathrm{D}_{70}{-}b{-}\\mathrm{S}_{10}$ and C-POSS- $\\mathrm{\\cdotD}_{90}\\mathrm{-}b\\mathrm{-}\\mathrm{S}_{13}$ coatings exhibited the freezing delay times of more than $2~\\mathrm{min}$ . It could be suggested that POSS groups played an important role in regulating and controlling superior hydrophobic/hydrophilic balance of the coating surface to form a self-lubricating aqueous layer with anti-icing performance.  \n\nTherefore, C-POSS- $\\cdot\\mathrm{D}_{50}{-}b{-}\\mathrm{S}_{7}$ coating, which has the lowest content of hydrophilic units, exhibited the longest freezing delay time, whereas $\\mathrm{C}{\\cdot}\\mathrm{D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ could only prevent water from freezing in a short time.  \n\nNon-freezable Bond Water Amount in the SIPN Coatings.  In order to further understand the antifogging/anti-icing properties of the SIPN coatings, the amounts of bond water, nonfreezable bond water and freezable water in the coatings were analyzed by DSC. Figure 6 shows the DSC thermograms of the samples with the similar water content ( $\\cdot W_{\\mathrm{c}}{\\approx}1.22)$ in the heating process at a rate of $10~\\mathrm{{^{\\circ}C/m i n}}$ , whereas the results of sample C-POSS- $\\mathrm{\\cdotD}_{90}\\mathrm{-}b\\mathrm{-}\\mathrm{S}_{13}$ with different water contents and the pure deionized water were also included. It can be seen that most of the melting peaks in the heating scans of the samples could be fitted into two peaks, a smaller one at around ${\\bf-}20{\\bf-}17\\ ^{\\circ}{\\bf C}$ and a sharp one at ${\\boldsymbol{-8}}{\\boldsymbol{\\sim}}0^{\\circ}\\mathrm{C}$ close to the melting point of pure deionized water. The smaller and the sharp peaks could correspond to the melting enthalpies of freezable bond water $(W_{\\mathrm{fb}})$ and freezable free water $(W_{\\mathrm{ff}})$ , respectively, depending on the different endothermic states in the melting process.29,30 By quantitatively comparing the water contents in different states, we could verify the existence of the non-freezable bond water in the SIPN coatings.29-33  \n\nTable 3 summarizes the water contents in different states determined by DSC. In the C-POSS$\\mathrm{D}_{50}–b–\\mathrm{S}_{7}$ , C-POSS- ${\\bf\\cdot D}_{70}$ -b-S10, C-POSS- $\\mathrm{\\cdotD}_{90}\\mathrm{-}b\\mathrm{-}\\mathrm{S}_{13}$ and $\\mathrm{C-D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ coating/water binary systems, when the total water content $W_{\\mathrm{c}}{\\approx}1.22$ , the measured non-freezable bond water contents $(W_{\\mathrm{nfb}})$ were 0.45, 0.43, 0.45 and $0.52~\\mathrm{mg/mg}$ , respectively, showing similar non-freezable bond water contents in all the SIPN coatings. In addition, the total bond water contents exhibited the similar results about $0.59{\\mathrm{-}}0.61~\\mathrm{mg/mg}$ , indicating that all the SIPN coatings with or without POSS may have the similar situation of polymer-water interactions at a molecular level via hydrogen bonds.28-33  \n\n![](images/a24771f91220144748cbf3e0146808c9bdd346a6743a2314daf7dcbbb43fd509.jpg)  \nFigure 6. DSC heating curves of the SIPN coatings with a total water content $(W_{\\mathrm{c}})$ of approximate 1.22, and the sample C-POSS- ${\\bf\\cdot D}_{90}$ - $b{\\mathrm{-}}\\mathrm{S}_{13}$ with different water contents at a heating rate of $10~{^\\circ}\\mathrm{C}/\\mathrm{min}$ . The DSC heating scan of pure deionized water was also added as control.  \n\nAdditionally, DSC heating curves of C-POSS- $\\mathrm{\\cdotD}_{90}\\mathrm{-}b\\mathrm{-}\\mathrm{S}_{13}$ with different water contents were specially shown in Figure 6. We selected four $W_{\\mathrm{c}}$ values, which are 1.22, 0.83, 0.53 and 0.26 $\\mathrm{{mg/mg}}$ , for comparison. It can be seen that as the water content decreased, the melting points of the free water as well as all the contents of water in different states tended to reduce (Table 3). It was noticed that when $W_{\\mathrm{c}}{=}0.26$ , only one melting peak was detectable in the DSC heating curve, and it was difficult to distinguish the different states of water in this case. It was assumed that the smaller amount of water in the sample could possibly appear only in the state of freezable water because the melting peak was close to the melting peak $T_{\\mathrm{ffm}}$ values $\\mathrm{-}7{\\sim}\\mathrm{-}3^{\\circ}\\mathrm{C}$ of other samples, and higher than the $T_{\\mathrm{fbm}}$ values about ${\\bf-17}\\mathrm{\\sim}{\\bf-14}^{\\circ}\\mathrm{C}$ (Table 3).  \n\nTable 3. Different water contents in the SIPN coatings analyzed by DSC   \n\n\n<html><body><table><tr><td rowspan=\"4\">Sample</td><td rowspan=\"4\">W. (mg/mg)</td><td colspan=\"6\">Freezable water</td><td>Bond</td></tr><tr><td>Wf</td><td colspan=\"2\">Freezable bond water</td><td colspan=\"2\">Freezable Free water</td><td>Non-freezable bond water</td><td>water</td></tr><tr><td>(mg/mg)</td><td>Wfb</td><td>Tfbm</td><td>Wff</td><td>Tffim</td><td>Wnfb (mg/mg)</td><td>Wb</td></tr><tr><td></td><td>(mg/mg)</td><td>(C)</td><td>(mg/mg)</td><td>(℃)</td><td></td><td>(mg/mg)</td></tr><tr><td>C-POSS-D50-b-S7</td><td>1.21</td><td>0.76</td><td>0.14</td><td>-14.01</td><td>0.62</td><td>-1.30</td><td>0.45</td><td>0.59</td></tr><tr><td>C-POSS-D70-b-S10</td><td>1.20</td><td>0.77</td><td>0.16</td><td>-17.42</td><td>0.61</td><td>-1.91</td><td>0.43</td><td>0.59</td></tr><tr><td>C-POSS-D90-b-S13</td><td>1.22</td><td>0.77</td><td>0.14</td><td>-15.01</td><td>0.63</td><td>-1.50</td><td>0.45</td><td>0.59</td></tr><tr><td rowspan=\"4\">C-D5o-b-S7</td><td>0.83</td><td>0.61</td><td>0.15</td><td>-16.14</td><td>0.46</td><td>-3.35</td><td>0.22</td><td>0.37</td></tr><tr><td>0.53</td><td>0.39</td><td>0.10</td><td>-16.79</td><td>0.29</td><td>-7.38</td><td>0.14</td><td>0.24</td></tr><tr><td>0.26</td><td>0.26</td><td></td><td></td><td>0.26</td><td>-8.76</td><td></td><td></td></tr><tr><td>1.24</td><td>0.72</td><td>0.09</td><td>-16.34</td><td>0.63</td><td>-2.13</td><td>0.52</td><td>0.61</td></tr></table></body></html>  \n\nA sufficient amount of the non-freezable bond water in the SIPN coatings played an important role for the excellent antifogging/anti-icing properties. In fact, the non-freezable bond water formed by the polymer-water interactions via hydrogen bonds may vary with hydrophilic polar groups and hydrophobic nonpolar groups.41 Therefore, the similar non-freezable bond water contents in all the SIPN coatings was dominated by the polymeric structure, especially the hydrophilic components. In fact, the C-POSS- $\\mathrm{\\cdotD}_{50}{\\mathrm{-}}b{\\mathrm{-}}\\mathrm{S}_{7}$ , C-POSS- $\\mathrm{\\cdotD}_{70}$ -b-S10, C-POSS- ${\\bf\\cdot D}_{90}$ -b-S13 and $\\mathrm{C}{\\cdot}\\mathrm{D}_{50}{\\cdot}b{\\cdot}\\mathrm{S}_{7}$ coatings exhibited quite close non-freezable bond water contents even when detected at different heating rates of 5, 10 or $15~\\mathrm{{^{\\circ}C/m i n}}$ as shown in the Supporting Information Table S1. The different heating rates exerted no significant influence on non-freezable bond water contents, suggesting well absorption of water in all the SIPN coatings with or without POSS. Containing similar non-freezable water contents, the SIPN coating with or without POSS demonstrated different antifogging/anti-icing properties, further confirming the important role of POSS on the coating surface.  \n\n![](images/dd81f57c65c0efae99bf125b811bd9cff024ebafc4931184b217744ee92be52f.jpg)  \nFigure 7. Illustration of amphiphilic SIPN coatings containing POSS-PDMAEMA- $b$ -PSBMA  \n\n(A) and PDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA (B) with cross-linked PEGDMA network. Hydrophobic POSS aggregated on the surface and strongly hydrophilic chains distributed beneath them endowed the amphiphilic SIPN coatings with excellent antifogging/anti-icing performances in comparison with the hydrophilic SIPN coating.  \n\nThe SIPN coatings, which contained POSS-PDMAEMA- $b$ -PSBMA and were comprised of both low surface energy and hydrophilic blocks, endowed the surfaces with the optimum antifogging/anti-icing performances. As illustrated in Figure 7, hydrophobic POSS clusters aggregated on the coating surfaces featured the amphiphilic surface of the SIPN coatings containing POSS-PDMAEMA- $b$ -PSBMA block copolymers. The hygroscopic polymeric components of the coatings manipulated water molecules to well disperse into the hydrophilic matrix via hydrogen bonded interactions. Based on the POSS clusters and the self-lubricating aqueous layer formed by the non-freezable bond water on the surface, the amphiphilic SIPN coating containing POSS-PDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA block copolymers exhibited excellent antifogging/anti-icing performances over the hydrophilic SIPN coating without POSS.",
        "category": " Results and discussion"
    },
    {
        "id": 7,
        "chunk": "# CONCLUSIONS  \n\nIn this work, we developed an amphiphilic SIPN coating containing block copolymers of POSS-PDMAEMA- $b$ -PSBMA with cross-linked PEGDMA network. The obtained SIPN coatings that were comprised of both low surface energy and hydrophilic components endowed the coatings with optimal antifogging/anti-icing performances. The excellent antifogging properties were originated primarily from the hygroscopicity of PDMAEMA and PSBMA blocks embedded in cross-linked PEGDMA network, as well as the hydrophobic POSS aggregated on the surface. The amphiphilic SIPN coatings with POSS groups had excellent transparency due to rapid water-absorption in the coatings. PDMAEMA with LCST and PSBMA with UCST facilitated the dispersion of water molecules to enhance the antifogging behaviors. Also, a selflubricating aqueous layer formed by non-freezable bond water at the surface endowed the amphiphilic SIPN coatings with great anti-icing performance which had a freezing delay time of more than $2~\\mathrm{min}$ . The amphiphilic antifogging/anti-icing coatings combining POSS and PDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA would contribute to novel potential applications in the future, such as transparent substrates in airplanes and lenses in medical instruments.",
        "category": " Conclusions"
    },
    {
        "id": 8,
        "chunk": "# ASSOCIATED CONTENT",
        "category": " References"
    },
    {
        "id": 9,
        "chunk": "# Supporting Information  \n\nThe Supporting Information is available including characterizations of the POSSPDMAEMA- $\\mathbf{\\nabla}\\cdot\\boldsymbol{b}$ -PSBMA block copolymers by $\\mathrm{^{1}H N M R}$ , FTIR spectra, GPC and TGA techniques, and the characterizations of the SIPN coatings by TEM and DSC. The “thermal remediation” pictures of the SIPN coating by a digital camera were also presented.",
        "category": " Results and discussion"
    },
    {
        "id": 10,
        "chunk": "# AUTHOR INFORMATION",
        "category": " References"
    },
    {
        "id": 11,
        "chunk": "# Corresponding Author  \n\n\\*E-mail: yuanxy $@$ tju.edu.cn; xyuan28@yahoo.com.",
        "category": " References"
    },
    {
        "id": 12,
        "chunk": "# Notes  \n\nThe authors declare no competing financial interest.",
        "category": " References"
    },
    {
        "id": 13,
        "chunk": "# ACKNOWLEDGMENTS  \n\nThis work is financially supported by National Natural Science Foundation of China (Nos. 51603143 and 51273146).",
        "category": " References"
    },
    {
        "id": 14,
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S.; King, H. E. Thermal Analysis of Polymer  \nWater Interactions and Their Relation to Gas Hydrate Inhibition. J. Appl. Polym. Sci. 2007, 103,   \n2642-2653.  \n\n![](images/03ab1750fc3af80ba2b525d4ce0b8f06566f635c81f87b745ad003ec353f58a3.jpg)  \nTable of Contents Graphic",
        "category": " References"
    }
]