[go: up one dir, main page]
More Web Proxy on the site http://driver.im/
Next Issue
Volume 8, November
Previous Issue
Volume 8, September
You seem to have javascript disabled. Please note that many of the page functionalities won't work as expected without javascript enabled.
 
 
polymers-logo

Journal Browser

Journal Browser
From the start of 2016, the journal uses article numbers instead of page numbers to identify articles. If you are required to add page numbers to a citation, you can do with using a colon in the format [article number]:1–[last page], e.g. 10:1–20.

Polymers, Volume 8, Issue 10 (October 2016) – 33 articles

Cover Story (view full-size image): Conjugated polymers (CP), including polyaniline (PANI), polypyrrole (PPy), and their derivatives, with only nonmetallic elements and some pivotal heteroatoms in their backbones, provide unique opportunities for the synthesis of metal-free heteroatom-doped carbon materials by direct carbonization of the CP. The heteroatoms homogeneously introduced into the carbon framework can not only be preserved at a relatively high content by adjusting the carbonization temperature, but also stay stable under harsh working conditions. Thus, CP-derived heteroatom-doped carbon materials are important candidates of electrode materials for electrochemical devices. By Ping Xu. View this paper.
  • Issues are regarded as officially published after their release is announced to the table of contents alert mailing list.
  • You may sign up for e-mail alerts to receive table of contents of newly released issues.
  • PDF is the official format for papers published in both, html and pdf forms. To view the papers in pdf format, click on the "PDF Full-text" link, and use the free Adobe Reader to open them.
Order results
Result details
Section
Select all
Export citation of selected articles as:
6984 KiB  
Article
Conformation Change, Tension Propagation and Drift-Diffusion Properties of Polyelectrolyte in Nanopore Translocation
by Pai-Yi Hsiao
Polymers 2016, 8(10), 378; https://doi.org/10.3390/polym8100378 - 24 Oct 2016
Cited by 10 | Viewed by 6119
Abstract
Using Langevin dynamics simulations, conformational, mechanical and dynamical properties of charged polymers threading through a nanopore are investigated. The shape descriptors display different variation behaviors for the cis- and trans-side sub-chains, which reflects a strong cis-trans dynamical asymmetry, especially when the [...] Read more.
Using Langevin dynamics simulations, conformational, mechanical and dynamical properties of charged polymers threading through a nanopore are investigated. The shape descriptors display different variation behaviors for the cis- and trans-side sub-chains, which reflects a strong cis-trans dynamical asymmetry, especially when the driving field is strong. The calculation of bond stretching shows how the bond tension propagates on the chain backbone, and the chain section straightened by the tension force is determined by the ratio of the direct to the contour distances of the monomer to the pore. With the study of the waiting time function, the threading process is divided into the tension-propagation stage and the tail-retraction stage. At the end, the drift velocity, diffusive property and probability density distribution are explored. Owing to the non-equilibrium nature, translocation is not a simple drift-diffusion process, but exhibits several intermediate behaviors, such as ballistic motion, normal diffusion and super diffusion, before ending with the last, negative-diffusion behavior. Full article
(This article belongs to the Special Issue Semiflexible Polymers)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>An illustration of the system. The negatively-charged polyelectrolyte is colored in yellow bead-spring chains. The counterions ((<math display="inline"> <semantics> <mrow> <mo>+</mo> <mn>1</mn> </mrow> </semantics> </math>)-ions) are represented in white beads, and the coions ((<math display="inline"> <semantics> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </semantics> </math>)-ions) are in green beads. A hallow wall separates the space into the cis region (Region I) and the trans region (Region III), connected by a pore channel (Region II) at the center. An electric field <math display="inline"> <semantics> <mrow> <mover accent="true"> <mi>E</mi> <mo stretchy="false">→</mo> </mover> <mo>=</mo> <mo>−</mo> <mi>E</mi> <mover accent="true"> <mi>z</mi> <mo>^</mo> </mover> </mrow> </semantics> </math> is applied inside the pore where the unit vector <math display="inline"> <semantics> <mover accent="true"> <mi>z</mi> <mo>^</mo> </mover> </semantics> </math> points to the right, along the channel axis. The chain threads through the pore and is gradually transported from the cis region to the trans region by the electric field. In order to visualize the chain section inside the pore, the wall beads (in gray color) have been plotted with a certain degree of transparency.</p>
Full article ">Figure 2
<p>Shape factor <math display="inline"> <semantics> <mrow> <mi>η</mi> <mo>=</mo> <mrow> <mo>〈</mo> <msubsup> <mi>R</mi> <mrow> <mi mathvariant="normal">e</mi> </mrow> <mn>2</mn> </msubsup> <mo>〉</mo> </mrow> <mo>/</mo> <mrow> <mo>〈</mo> <msubsup> <mi>R</mi> <mrow> <mi mathvariant="normal">g</mi> </mrow> <mn>2</mn> </msubsup> <mo>〉</mo> </mrow> </mrow> </semantics> </math> in the cis region (I) and trans region (III) for <math display="inline"> <semantics> <mrow> <mi>N</mi> <mo>=</mo> <mn>256</mn> </mrow> </semantics> </math> as a function of the scaled time <math display="inline"> <semantics> <mover accent="true"> <mi>t</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math> at five driving electric fields <span class="html-italic">E</span> whose values are indicated in the plots.</p>
Full article ">Figure 3
<p>Average variations of (<b>a</b>) the asphericity <math display="inline"> <semantics> <mrow> <mo>〈</mo> <mi>A</mi> <mo>〉</mo> </mrow> </semantics> </math> and of (<b>b</b>) the prolateness <math display="inline"> <semantics> <mrow> <mo>〈</mo> <mi>P</mi> <mo>〉</mo> </mrow> </semantics> </math> in the cis region (I) and trans-region (III) as a function of the scaled time <math display="inline"> <semantics> <mover accent="true"> <mi>t</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math>, for <math display="inline"> <semantics> <mrow> <mi>N</mi> <mo>=</mo> <mn>256</mn> </mrow> </semantics> </math> at different driving electric fields <span class="html-italic">E</span> (indicated in the plots).</p>
Full article ">Figure 4
<p>Variations of the averaged polar angle (<b>a</b>) <math display="inline"> <semantics> <mrow> <mo>〈</mo> <msub> <mi>θ</mi> <mi mathvariant="normal">I</mi> </msub> <mo>〉</mo> </mrow> </semantics> </math> and (<b>b</b>) <math display="inline"> <semantics> <mrow> <mo>〈</mo> <msub> <mi>θ</mi> <mi>III</mi> </msub> <mo>〉</mo> </mrow> </semantics> </math> in degrees <math display="inline"> <semantics> <msup> <mrow/> <mo>∘</mo> </msup> </semantics> </math>, as a function of the scaled time <math display="inline"> <semantics> <mover accent="true"> <mi>t</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math> at different driving electric fields <span class="html-italic">E</span>. The number of monomers of the chain <span class="html-italic">N</span> is 256.</p>
Full article ">Figure 5
<p>Intensity plots of the bond tension <math display="inline"> <semantics> <mrow> <mo>〈</mo> <msub> <mi>f</mi> <mi>n</mi> </msub> <mo>〉</mo> </mrow> </semantics> </math> in the scaled <math display="inline"> <semantics> <mover accent="true"> <mi>t</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math>-<math display="inline"> <semantics> <mover accent="true"> <mi>n</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math> space for <math display="inline"> <semantics> <mrow> <mi>N</mi> <mo>=</mo> <mn>256</mn> </mrow> </semantics> </math> at four field strengths <span class="html-italic">E</span> (indicated in the figures). The strength of tension is represented by color, and the color scale is given at the right of the figure. The dashed line shows the scaled translocation coordinate <math display="inline"> <semantics> <mrow> <mo>〈</mo> <mover accent="true"> <mi>s</mi> <mo stretchy="false">˜</mo> </mover> <mo>〉</mo> </mrow> </semantics> </math>, which depicts the progress of threading.</p>
Full article ">Figure 6
<p>Variation of the bond tension <math display="inline"> <semantics> <mrow> <mo>〈</mo> <msub> <mi>f</mi> <mi>n</mi> </msub> <mo>〉</mo> </mrow> </semantics> </math> (the black curves) for <math display="inline"> <semantics> <mrow> <mi>N</mi> <mo>=</mo> <mn>256</mn> </mrow> </semantics> </math> at a set of scaled time points <math display="inline"> <semantics> <mover accent="true"> <mi>t</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math> (values indicated in the figures) at the driving fields: (<b>a</b>) <math display="inline"> <semantics> <mrow> <mi>E</mi> <mo>=</mo> <mn>4</mn> <mo>.</mo> <mn>0</mn> </mrow> </semantics> </math>; (<b>b</b>) <math display="inline"> <semantics> <mrow> <mn>8</mn> <mo>.</mo> <mn>0</mn> </mrow> </semantics> </math>; and (<b>c</b>) <math display="inline"> <semantics> <mrow> <mn>32</mn> <mo>.</mo> <mn>0</mn> </mrow> </semantics> </math>. The direction of the scaled <math display="inline"> <semantics> <mover accent="true"> <mi>n</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math>-axis is reversed so that the monomers entering the trans region stay on the right-hand side of the plot while the cis monomers rest on the left-hand side. The sky-blue region indicates the monomers in the pore region. The direct distance <math display="inline"> <semantics> <mrow> <mo>〈</mo> <msub> <mi>D</mi> <mi>n</mi> </msub> <mo>〉</mo> </mrow> </semantics> </math> and the contour distance <math display="inline"> <semantics> <mrow> <mo>〈</mo> <msub> <mi mathvariant="sans-serif">Λ</mi> <mi>n</mi> </msub> <mo>〉</mo> </mrow> </semantics> </math> to the pore are plotted in red and green colors, respectively. The values of <math display="inline"> <semantics> <mrow> <mo>〈</mo> <msub> <mi>D</mi> <mi>n</mi> </msub> <mo>〉</mo> </mrow> </semantics> </math> and <math display="inline"> <semantics> <mrow> <mo>〈</mo> <msub> <mi mathvariant="sans-serif">Λ</mi> <mi>n</mi> </msub> <mo>〉</mo> </mrow> </semantics> </math> are read from the right <span class="html-italic">y</span>-axis of the figure. In each plot, a downward arrow indicates the location of the tension front, whereas a dashed line marks the boundary for the straightened chain section.</p>
Full article ">Figure 7
<p>Normalized waiting time function <math display="inline"> <semantics> <mrow> <mover accent="true"> <mi>w</mi> <mo stretchy="false">˜</mo> </mover> <mrow> <mo>(</mo> <mover accent="true"> <mi>s</mi> <mo stretchy="false">˜</mo> </mover> <mo>)</mo> </mrow> </mrow> </semantics> </math> for <math display="inline"> <semantics> <mrow> <mi>N</mi> <mo>=</mo> <mn>256</mn> </mrow> </semantics> </math> at different field strengths <span class="html-italic">E</span> indicated at the left of the curves. <math display="inline"> <semantics> <mover accent="true"> <mi>s</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math> is defined as <math display="inline"> <semantics> <mrow> <mi>s</mi> <mo>/</mo> <mi>N</mi> </mrow> </semantics> </math>. The curves have been shifted upward with a fixed value, one after the other.</p>
Full article ">Figure 8
<p>(<b>a</b>) Hump position <math display="inline"> <semantics> <msup> <mover accent="true"> <mi>s</mi> <mo stretchy="false">˜</mo> </mover> <mo>*</mo> </msup> </semantics> </math> of the normalized waiting time function <math display="inline"> <semantics> <mrow> <mover accent="true"> <mi>w</mi> <mo stretchy="false">˜</mo> </mover> <mrow> <mo>(</mo> <mover accent="true"> <mi>s</mi> <mo stretchy="false">˜</mo> </mover> <mo>)</mo> </mrow> </mrow> </semantics> </math>, as a function of <span class="html-italic">E</span>. The number of monomers <span class="html-italic">N</span> is indicated in the figure. (<b>b</b>) <math display="inline"> <semantics> <mrow> <mo>(</mo> <mi>N</mi> <mo>−</mo> <msup> <mi>s</mi> <mo>*</mo> </msup> <mo>)</mo> </mrow> </semantics> </math> vs. <span class="html-italic">N</span> at different field strengths <span class="html-italic">E</span>.</p>
Full article ">Figure 9
<p>Drift velocity <math display="inline"> <semantics> <mrow> <mi>v</mi> <mo>(</mo> <mi>s</mi> <mo>)</mo> </mrow> </semantics> </math> for: (<b>a</b>) <math display="inline"> <semantics> <mrow> <mi>N</mi> <mo>=</mo> <mn>128</mn> </mrow> </semantics> </math>; (<b>b</b>) 256; and (<b>c</b>) 384. <math display="inline"> <semantics> <mover accent="true"> <mi>s</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math> is the scaled translocation coordinate. The strength of the driving field <span class="html-italic">E</span> is indicated near the curve. In panel (c), the estimated drift velocity <math display="inline"> <semantics> <mrow> <msub> <mi>v</mi> <mi>es</mi> </msub> <mrow> <mo>(</mo> <mi>s</mi> <mo>)</mo> </mrow> </mrow> </semantics> </math> is plotted in thin dashed curves in the same color code.</p>
Full article ">Figure 10
<p>(<b>a</b>) Variance of the translocation coordinate <math display="inline"> <semantics> <mrow> <mo>〈</mo> <mo>Δ</mo> <msup> <mi>s</mi> <mn>2</mn> </msup> <mo>〉</mo> </mrow> </semantics> </math> versus the scaled time <math display="inline"> <semantics> <mover accent="true"> <mi>t</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math>; (<b>b</b>) <math display="inline"> <semantics> <mrow> <mo>〈</mo> <mo>Δ</mo> <msup> <mi>s</mi> <mn>2</mn> </msup> <mo>〉</mo> </mrow> </semantics> </math> plotted as a function of the real time <span class="html-italic">t</span> in the log-log plot. The chain has 256 monomers. The field strength <span class="html-italic">E</span> is indicated in the figures.</p>
Full article ">Figure 11
<p>Probability densities <math display="inline"> <semantics> <mrow> <mi>p</mi> <mo>(</mo> <mi>s</mi> <mo>,</mo> <mi>t</mi> <mo>)</mo> </mrow> </semantics> </math> versus the scaled time <math display="inline"> <semantics> <mover accent="true"> <mi>t</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math> for (<b>a</b>) <math display="inline"> <semantics> <mrow> <mi>E</mi> <mo>=</mo> <mn>0</mn> <mo>.</mo> <mn>2</mn> </mrow> </semantics> </math>, (<b>b</b>) <math display="inline"> <semantics> <mrow> <mn>2</mn> <mo>.</mo> <mn>0</mn> </mrow> </semantics> </math> and (<b>c</b>) <math display="inline"> <semantics> <mrow> <mn>32</mn> <mo>.</mo> <mn>0</mn> </mrow> </semantics> </math> at different translocation coordinates <span class="html-italic">s</span> indicated near the curves. For clarity, the curves have been shifted upward, one by one, by a fixed step. The dashed curves superimposed on the data are the results of fitting from Equation (<a href="#FD19-polymers-08-00378" class="html-disp-formula">19</a>). The number of monomers of the chain <span class="html-italic">N</span> is 256.</p>
Full article ">Figure 12
<p>(<b>a</b>) Fitting parameter <math display="inline"> <semantics> <msub> <mi>σ</mi> <mi>s</mi> </msub> </semantics> </math> as a function of the scaled coordinate <math display="inline"> <semantics> <mover accent="true"> <mi>s</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math> at different <span class="html-italic">E</span> fields; (<b>b</b>) relative width <math display="inline"> <semantics> <msub> <mover accent="true"> <mi>W</mi> <mo stretchy="false">˜</mo> </mover> <mi>s</mi> </msub> </semantics> </math> of the log-normal distribution, calculated by <math display="inline"> <semantics> <mrow> <mn>2</mn> <mo form="prefix">sinh</mo> <mrow> <mo>(</mo> <msqrt> <mrow> <mn>2</mn> <mo form="prefix">ln</mo> <mn>2</mn> </mrow> </msqrt> <msub> <mi>σ</mi> <mi>s</mi> </msub> <mo>)</mo> </mrow> <mo form="prefix">exp</mo> <mrow> <mo>(</mo> <mo>−</mo> <msubsup> <mi>σ</mi> <mi>s</mi> <mn>2</mn> </msubsup> <mo>)</mo> </mrow> <msub> <mi>μ</mi> <mi>s</mi> </msub> <mo>/</mo> <mrow> <mo>〈</mo> <mi>τ</mi> <mo>〉</mo> </mrow> </mrow> </semantics> </math>, versus <math display="inline"> <semantics> <mover accent="true"> <mi>s</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math>. The field strengths <span class="html-italic">E</span> are indicated in the figure. The number of monomers <span class="html-italic">N</span> is equal to 256.</p>
Full article ">Figure 13
<p>(<b>a</b>) <math display="inline"> <semantics> <mrow> <mo>〈</mo> <msub> <mover accent="true"> <mi>t</mi> <mo stretchy="false">˜</mo> </mover> <mi>s</mi> </msub> <mo>〉</mo> </mrow> </semantics> </math> calculated by <math display="inline"> <semantics> <mrow> <msub> <mi>μ</mi> <mi>s</mi> </msub> <mo form="prefix">exp</mo> <mrow> <mo>(</mo> <msubsup> <mi>σ</mi> <mi>s</mi> <mn>2</mn> </msubsup> <mo>/</mo> <mn>2</mn> <mo>)</mo> </mrow> </mrow> </semantics> </math>, plotted in the scaled coordinate <math display="inline"> <semantics> <mover accent="true"> <mi>s</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math> at different <span class="html-italic">E</span>. For clarity, the curves have been shifted upward, one by one, by a fixed value. The strengths of <span class="html-italic">E</span> are indicated in the figure. The chain has 256 monomers. The dashed curves are the mean time obtained directly from the simulations, superimposed here for comparison. (<b>b</b>) Retardation <math display="inline"> <semantics> <msub> <mi>δ</mi> <mi>s</mi> </msub> </semantics> </math> as a function of the scaled coordinate <math display="inline"> <semantics> <mover accent="true"> <mi>s</mi> <mo stretchy="false">˜</mo> </mover> </semantics> </math>.</p>
Full article ">
13110 KiB  
Article
Low Band Gap Donor–Acceptor Type Polymers Containing 2,3-Bis(4-(decyloxy)phenyl)pyrido[4,3-b]pyrazine as Acceptor and Different Thiophene Derivatives as Donors
by Yan Zhang, Xuezhong Liu, Min Wang, Xiaoli Liu and Jinsheng Zhao
Polymers 2016, 8(10), 377; https://doi.org/10.3390/polym8100377 - 24 Oct 2016
Cited by 12 | Viewed by 7436
Abstract
Four donor–acceptor type conducting polymers, namely poly(2,3-bis(4-decyloxy)phenyl)-5,8-bis(4-thiophen-2-yl)pyrido[4,3-b]pyrazine) (P1), poly(2,3-bis(4-decyloxy)phenyl)-5,8-bis(4-butylthiophen-2-yl)pyrido[4,3-b]pyrazine) (P2), poly(2,3-bis(4-(decyloxy)phenyl)-5,8-bis(4-hexyloxythiophen-2-yl)pyrido[4,3-b]pyrazine) (P3) and poly(2,3-bis(4-(decyloxy)phenyl)-5,8-bis(2,3-dihydrothieno[3,4-b][1,4]dioxin-7-yl)pyrido[4,3-b]pyrazine) (P4), containing thiophene or its derivative as the donor and pyrido[4,3-b]pyrazine as the acceptor were prepared and characterized by cyclic voltammetry, scanning electron microscopy, and UV-Vis spectroscopy to detect [...] Read more.
Four donor–acceptor type conducting polymers, namely poly(2,3-bis(4-decyloxy)phenyl)-5,8-bis(4-thiophen-2-yl)pyrido[4,3-b]pyrazine) (P1), poly(2,3-bis(4-decyloxy)phenyl)-5,8-bis(4-butylthiophen-2-yl)pyrido[4,3-b]pyrazine) (P2), poly(2,3-bis(4-(decyloxy)phenyl)-5,8-bis(4-hexyloxythiophen-2-yl)pyrido[4,3-b]pyrazine) (P3) and poly(2,3-bis(4-(decyloxy)phenyl)-5,8-bis(2,3-dihydrothieno[3,4-b][1,4]dioxin-7-yl)pyrido[4,3-b]pyrazine) (P4), containing thiophene or its derivative as the donor and pyrido[4,3-b]pyrazine as the acceptor were prepared and characterized by cyclic voltammetry, scanning electron microscopy, and UV-Vis spectroscopy to detect the influence of the donor units’ strength on the electrochromic performances. The results demonstrated that all of the polymers could be reversibly reduced and oxidized by p-type doping and n-type doping, and showed near-infrared activities and different color changes in p-type doping process. Especially, P3 and P4 showed lower optical band gap than P1 and P2 due to the strong electron-donating hexyloxythiophen group of P3 and ethylenedioxythiophene group of P4. Besides, P3 and P4 displayed the saturated green color at the neutral state and the desirable transparency at the oxidized state. All the polymers displayed desirable optical contrasts, satisfactory coloration efficiency, excellent stability and short switching time, which made the polymers fascinating candidates in the electrochromic device applications. Full article
(This article belongs to the Special Issue Conjugated Polymers 2016)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Cyclic voltammetry (CV) curves of M1.</p>
Full article ">Figure 2
<p>CV curves of the polymers for p-doping and n-doping processes at various scan rates: (<b>a</b>) P1; (<b>b</b>) P2; (<b>c</b>) P3; and (<b>d</b>) P4.</p>
Full article ">Figure 3
<p>CV curves of P1 for p-type doping process at various scan rates. Insert: graphs of scan rate vs. peak current density.</p>
Full article ">Figure 4
<p>The first and the 1000th CV curve of P1.</p>
Full article ">Figure 5
<p>SEM images of the polymers with magnification of 5000: (<b>a</b>) P1; (<b>b</b>) P2; (<b>c</b>) P3; and (<b>d</b>) P4.</p>
Full article ">Figure 6
<p>UV-vis spectra of the monomers and the polymers: (<b>a</b>) M1, M2, M3 and M4 (dissolve in DCM); and (<b>b</b>) P1, P2, P3 and P4 (deposited on ITO glasses).</p>
Full article ">Figure 7
<p>Optimized geometries and molecular orbital surfaces of the HOMOs and LUMOs for M1, M2, M3 and M4, the different colors suggested the different electronic cloud densities.</p>
Full article ">Figure 8
<p>Fluorescence emission spectra of the monomers.</p>
Full article ">Figure 9
<p>Spectroelectrochemical spectra of the polymers for p-doping process: (<b>a</b>) P1; (<b>b</b>) P2; (<b>c</b>) P3; and (<b>d</b>) P4.</p>
Full article ">Figure 10
<p>Transmittance change of the polymers with a same residence time of 4 s: (<b>a</b>) P1 monitored at 375, 615 and 1500 nm; (<b>b</b>) P2 monitored at 415, 556 and 1550 nm; (<b>c</b>) P3 monitored at 408, 830 and 1630 nm; and (<b>d</b>) P4 monitored at 422, 754 and 1660 nm.</p>
Full article ">Scheme 1
<p>Monomer structures of some donor–acceptor (D-A) type polymers containing: (<b>a</b>) benzothiadiazole; (<b>b</b>) benzobis (thiadiazole); (<b>c</b>) benzimidazole; (<b>d</b>,<b>h</b>) benzotriazole, (<b>e</b>) quinoxaline; and (<b>f</b>,<b>g</b>) pyridopyrazine as acceptor units.</p>
Full article ">Scheme 2
<p>Schematic representation of syntheses of the monomers: (<b>a</b>) HBr, Br<sub>2</sub>, 135 °C, 5 h; (<b>b</b>) HAc, HBr, reflux, 12 h; (<b>c</b>) DMF, K<sub>2</sub>CO<sub>3</sub>, 1-bromine decane, TBAB, 120 °C, 90 min; (<b>d</b>) HAc, 50 °C, 12 h; (<b>e</b>–<b>h</b>) Pd(PPh<sub>3</sub>)<sub>2</sub>Cl<sub>2</sub>, tributyl(thiophen-2-yl)stannane; (<b>e</b>) tributyl(4-butylthiophen-2-yl)stannane; (<b>f</b>) tributyl(4-hexyloxythiophen-2-yl)stannane; (<b>g</b>) tributyl(2,3-dihydrothieno[3,4-b][1,4]dioxin-7-yl)stannane; (<b>h</b>) dry toluene, reflux, 24 h.</p>
Full article ">Scheme 3
<p>The n-type doping mechanism of P1. Bu<sub>4</sub>N<sup>+</sup> was electrolyte cation.</p>
Full article ">
15129 KiB  
Article
Effect of Saponification Condition on the Morphology and Diameter of the Electrospun Poly(vinyl acetate) Nanofibers for the Fabrication of Poly(vinyl alcohol) Nanofiber Mats
by Seong Baek Yang, Jong Won Kim and Jeong Hyun Yeum
Polymers 2016, 8(10), 376; https://doi.org/10.3390/polym8100376 - 21 Oct 2016
Cited by 7 | Viewed by 8003
Abstract
Novel poly(vinyl alcohol) (PVA) nanofiber mats were prepared for the first time through heterogeneous saponification of electrospun poly(vinyl acetate) (PVAc) nanofibers. The effect of varying the saponification conditions, including temperature, time, and concentration of the alkaline solution, on the morphology of the saponified [...] Read more.
Novel poly(vinyl alcohol) (PVA) nanofiber mats were prepared for the first time through heterogeneous saponification of electrospun poly(vinyl acetate) (PVAc) nanofibers. The effect of varying the saponification conditions, including temperature, time, and concentration of the alkaline solution, on the morphology of the saponified PVA fibers were evaluated by field-emission scanning electron microscopy. At 25 °C, the saponified PVA fibers exhibited a broad diameter distribution. The average fiber diameter, however, was found to decrease with increasing saponification temperature. When the saponification time was increased from 6 to 30 h, the average fiber diameter decreased gradually from 1540 to 1060 nm. In addition, the fiber diameter and morphology were also affected by the concentration of the alkaline saponification solution. The most optimal conditions for fabrication of thin, uniform, and smooth PVA nanofibers corresponded to an alkaline solution containing 10 g each of NaOH, Na2SO4, and methanol per 100 g of water, a temperature of 25 °C, and a saponification time of 24 h. Full article
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Schematic illustration of the heterogeneous saponification process employed for manufacturing of PVA nanofiber mats.</p>
Full article ">Figure 2
<p>Field emission scanning electron microscope (FE-SEM) images of saponified PVA nanofiber mats obtained at different temperatures: (<b>A</b>) 25 °C; (<b>B</b>) 35 °C; and (<b>C</b>) 45 °C. The quantities of the reagents in the saponification solution (NaOH = 10 g, Na<sub>2</sub>SO<sub>4</sub> = 10 g, MeOH = 10 g, and H<sub>2</sub>O = 100 g) and the reaction time (12 h) were kept constant.</p>
Full article ">Figure 3
<p>FE-SEM images of saponified PVA nanofiber mats obtained at different saponification times: (<b>A</b>) 6 h; (<b>B</b>) 12 h; (<b>C</b>) 18 h; (<b>D</b>) 24 h; and (<b>E</b>) 30 h. The quantities of the reagents in the saponification solution (NaOH = 10 g, Na<sub>2</sub>SO<sub>4</sub> = 10 g, MeOH = 10 g, and H<sub>2</sub>O = 10 g) and the reaction temperature were kept constant (25 °C).</p>
Full article ">Figure 4
<p>FE-SEM images of saponified PVA nanofiber mats obtained using saponification solution prepared using different respective quantities of NaOH, Na<sub>2</sub>SO<sub>4</sub>, and MeOH per 100 g of H<sub>2</sub>O: (<b>A</b>) 5, 5, and 5 g; (<b>B</b>) 7.5, 5, and 5 g; (<b>C</b>) 5, 7.5, and 5 g; (<b>D</b>) 5, 5, and 7.5 g; (<b>E</b>) 10, 5, and 5 g; (<b>F</b>) 5, 10, and 5 g; and (<b>G</b>) 5, 5, and 10 g. The saponification temperature and time were kept constant at 25 °C and 24 h, respectively.</p>
Full article ">Figure 5
<p>Fiber diameter histogram plots and FE-SEM images for saponified PVA nanofiber mats obtained at different saponification temperatures: (<b>A</b>) 25 °C; (<b>B</b>) 35 °C; and (<b>C</b>) 45 °C. The saponification solution contained NaOH (10 g), Na<sub>2</sub>SO<sub>4</sub> (10 g), and MeOH (10 g) in H<sub>2</sub>O (100 g) in each case. The time was kept constant at 12 h.</p>
Full article ">Figure 6
<p>Fiber diameter histogram plots and FE-SEM images for saponified PVA nanofiber mats obtained at different saponification times: (<b>A</b>) 6 h; (<b>B</b>) 12 h; (<b>C</b>) 18 h; (<b>D</b>) 24 h; and (<b>E</b>) 30 h. The saponification solution was prepared using the following reagents: NaOH (10 g), Na<sub>2</sub>SO<sub>4</sub> (10 g), and MeOH (10 g) per 100 g of H<sub>2</sub>O. The temperature was kept constant at 25 °C.</p>
Full article ">Figure 7
<p>Fiber diameter histogram plots and FE-SEM images for saponified PVA nanofiber mats obtained using a saponification solution prepared with different respective quantities of NaOH, Na<sub>2</sub>SO<sub>4</sub>, and MeOH per 100 g of H<sub>2</sub>O: (<b>A</b>) 5, 5, and 5 g; (<b>B</b>) 7.5, 5, and 5 g; (<b>C</b>) 10, 5, and 5 g; (<b>D</b>) 5, 7.5, and 5 g; and (<b>E</b>) 5, 10, and 5 g. The saponification time and temperature were kept constant at 24 h and 25 °C, respectively.</p>
Full article ">Figure 8
<p>(<b>A</b>) The effect of saponification temperature on the degree of saponification (DS) (%) of PVA saponified for 12 h; (<b>B</b>) The effect of saponification time on the DS of PVA saponified at 25 °C. The concentration of the saponification solution (NaOH, Na<sub>2</sub>SO<sub>4</sub>, and MeOH at 10 g each per 100 g of H<sub>2</sub>O) was kept constant.</p>
Full article ">Figure 9
<p>The effect of: (<b>A</b>) NaOH; (<b>B</b>) Na<sub>2</sub>SO<sub>4</sub>; and (<b>C</b>) MeOH concentration on the DS (%) of saponified PVA nanofibers. The saponification time and temperature were kept constant at 24 h and 25 °C, respectively.</p>
Full article ">Figure 10
<p>(<b>A</b>) A partial proton nuclear magnetic resonance spectrum of fully saponified PVA nanofibers; (<b>B</b>) Partial Fourier transform infrared spectroscopy spectra for un-saponified PVAc nanofibers (orange) and fully saponified PVA nanofibers (red). The polymer concentration was kept constant at 15 wt % and the saponification solution was comprised of NaOH (10 g), Na<sub>2</sub>SO<sub>4</sub> (10 g), MeOH (10 g), and H<sub>2</sub>O (100 g). The saponification temperature was 25 °C, the saponification time was 30 h, and DS was 99.93%.</p>
Full article ">Figure 11
<p>Stress-strain curve of: (<b>A</b>) general electrospun PVA nanofibers; and (<b>B</b>) fully saponified PVA nanofibers formed by heterogeneous saponification of electrospun PVAc nanofibers. The concentration of these nanofibers was at 15 wt % and the saponification solution was prepared using NaOH (10 g), Na<sub>2</sub>SO<sub>4</sub> (10 g), MeOH (10 g) and H<sub>2</sub>O (100 g). The saponification temperature and time were 25 °C and 30 h, respectively. The DS value of the fully saponified nanofibers was 99.93%.</p>
Full article ">
18626 KiB  
Article
FRP-Confined Recycled Coarse Aggregate Concrete: Experimental Investigation and Model Comparison
by Yingwu Zhou, Jingjing Hu, Mali Li, Lili Sui and Feng Xing
Polymers 2016, 8(10), 375; https://doi.org/10.3390/polym8100375 - 21 Oct 2016
Cited by 49 | Viewed by 7979
Abstract
The in situ application of recycled aggregate concrete (RAC) is of great significance in environmental protection and construction resources sustainability. However, it has been limited to nonstructural purposes due to its poor mechanical performance. External confinement using steel tubes and fiber-reinforced polymer (FRP) [...] Read more.
The in situ application of recycled aggregate concrete (RAC) is of great significance in environmental protection and construction resources sustainability. However, it has been limited to nonstructural purposes due to its poor mechanical performance. External confinement using steel tubes and fiber-reinforced polymer (FRP) can significantly improve the mechanical performance of RAC and thus the first-ever study on the axial compressive behavior of glass FRP (GFRP)-confined RAC was recently reported. To have a full understanding of FRP-confined RAC, this paper has extended the type of FRP and presents a systematic experimental study on the axial compressive performance of carbon FRP (CFRP)-confined RAC. The mechanical properties of CFRP-confined RAC from the perspective of the failure mode, ultimate strength and strain, and stress–strain relationship responses were analyzed. Integrated with existing experimental data of FRP-confined RAC, the paper compiles a database for the mechanical properties of FRP-confined RAC. Based on the database, the effects of FRP type (i.e., GFRP and CFRP) and the replacement ratio of recycled coarse aggregate were investigated. The results indicated that the stress–stain behavior of FRP-confined RAC depended heavily on the unconfined concrete strength and the FRP confining pressure instead of the replacement ratio. Therefore, this study adopted eleven high-performance ultimate strength and strain models developed for FRP-confined normal aggregate concrete (NAC) to predict the mechanical properties of FRP-confined RAC. All the predictions had good agreement with the test results, which further confirmed similar roles played by FRP confinement in improving the mechanical properties of RAC and improving those of NAC. On this basis, this paper finally recommended a stress–strain relationship model for FRP-confined RAC. Full article
(This article belongs to the Collection Fiber-Reinforced Polymer Composites in Structural Engineering)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Gradation curve of Recycled Aggregate (RA).</p>
Full article ">Figure 2
<p>Test setup and instrumentation. (<b>a</b>) Test setup; (<b>b</b>) Instrumentation.</p>
Full article ">Figure 3
<p>Failure modes. (<b>a</b>) Unconfined test specimen; (<b>b</b>) Confined test specimen.</p>
Full article ">Figure 4
<p>Stress–strain curves of CFRP-confined RAC. (<b>a</b>) <span class="html-italic">R</span> = 0% in series C1; (<b>b</b>) R = 30% in series C1; (<b>c</b>) <span class="html-italic">R</span> = 50% in series; (<b>d</b>) R = 100% in series C1; (<b>e</b>) R = 100% in series C1; (<b>f</b>) R = 100% in series C3.</p>
Full article ">Figure 5
<p>Effect of replacement ratio on stress–strain curve of CFRP-confined RAC (R = 0%, 30%, 50%, 100% in series C1).</p>
Full article ">Figure 6
<p>Effects of confinement ratio on FRP-confined RAC. (<b>a</b>) Strength gain ratio vs. confinement ratio; (<b>b</b>) Strain gain ratio vs. confinement ratio.</p>
Full article ">Figure 7
<p>Influence of the replacement ratio of RAs. (<b>a</b>) Strength gain ratio vs. replacement ratio; (<b>b</b>) strain gain ratio vs. replacement ratio.</p>
Full article ">Figure 8
<p>Models performance. (<b>a</b>) Ultimate strength models; (<b>b</b>) ultimate strain models.</p>
Full article ">Figure 9
<p>The representative stress–strain models. (<b>a</b>) Piecewise function; (<b>b</b>) Single function.</p>
Full article ">Figure 10
<p>Theo.(<span class="html-italic">f</span><sub>0</sub>) vs. Exp.(<span class="html-italic">f</span><sub>0</sub>).</p>
Full article ">Figure 11
<p>Model evaluations. (<b>a</b>) C1R0; (<b>b</b>) C2R50; (<b>c</b>) C1R100; (<b>d</b>) C2R100; (<b>e</b>) C3R100; (<b>f</b>) R0-G1~3 [<a href="#B51-polymers-08-00375" class="html-bibr">51</a>]; (<b>g</b>) R20-G1~3 [<a href="#B51-polymers-08-00375" class="html-bibr">51</a>]; (<b>h</b>) R100-G1~3 [<a href="#B51-polymers-08-00375" class="html-bibr">51</a>]; (<b>i</b>) R25 [<a href="#B52-polymers-08-00375" class="html-bibr">52</a>]; (<b>j</b>) R75 [<a href="#B52-polymers-08-00375" class="html-bibr">52</a>].</p>
Full article ">Figure 11 Cont.
<p>Model evaluations. (<b>a</b>) C1R0; (<b>b</b>) C2R50; (<b>c</b>) C1R100; (<b>d</b>) C2R100; (<b>e</b>) C3R100; (<b>f</b>) R0-G1~3 [<a href="#B51-polymers-08-00375" class="html-bibr">51</a>]; (<b>g</b>) R20-G1~3 [<a href="#B51-polymers-08-00375" class="html-bibr">51</a>]; (<b>h</b>) R100-G1~3 [<a href="#B51-polymers-08-00375" class="html-bibr">51</a>]; (<b>i</b>) R25 [<a href="#B52-polymers-08-00375" class="html-bibr">52</a>]; (<b>j</b>) R75 [<a href="#B52-polymers-08-00375" class="html-bibr">52</a>].</p>
Full article ">
2713 KiB  
Article
Synthesis of Thermo-Responsive Polymer via Radical (Co)polymerization of N,N-Dimethyl-?-(hydroxymethyl)acrylamide with N,N-Diethylacrylamide
by Yasuhiro Kohsaka and Yoshiaki Tanimoto
Polymers 2016, 8(10), 374; https://doi.org/10.3390/polym8100374 - 20 Oct 2016
Cited by 11 | Viewed by 6901
Abstract
?-Functionalized acrylamides have not been considered as an effective monomer design due to their poor polymerizability, although the analogues, ?-functionalized acrylates, are attractive monomers of which polymers exhibit characteristic properties. In this article, we report the first example of radical polymerization of ?-functionalized [...] Read more.
?-Functionalized acrylamides have not been considered as an effective monomer design due to their poor polymerizability, although the analogues, ?-functionalized acrylates, are attractive monomers of which polymers exhibit characteristic properties. In this article, we report the first example of radical polymerization of ?-functionalized N,N-disubstituted acrylamide affording thermo-responsive hydrophilic polymers. N,N-dimethyl-?-(hydroxymethyl)acrylamide (DM?HAA) was (co)polymerized with N,N-diethylacrylamide (DEAA). Although the homopolymerization did not afford a polymeric product, the copolymerizations with various feed ratios yielded a series of the copolymers containing 0%–65% of DM?HAA units. The obtained copolymers exhibited a lower critical solution temperature (LCST) in water; the cloud points (Tcs) were linearly elevated as the contents of DM?HAA units from 32 to 64 °C, indicating that DM?HAA functioned as a more hydrophilic monomer than DEAA. The linear relationship between Tc and DM?HAA content suggests that the homopolymer, poly(DM?HAA), should have Tc at ca. 80 °C, although it is not available by direct radical homopolymerization. Full article
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>LUMOs of (<b>a</b>) DMAA, (<b>b</b>) DMMA and (<b>c</b>) DMαHAA, and SOHOs of the respective radicals to (<b>d</b>) DMAA, (<b>e</b>) DMMA and (<b>f</b>) DMαHAA, by DFT calculation (B3LYP/6-31G*).</p>
Full article ">Figure 2
<p><sup>1</sup>H NMR spectra of (<b>a</b>) DMαHAA; (<b>b</b>) poly(DMαHAA-<span class="html-italic">co</span>-DEAA) obtained from Run 5; and (<b>c</b>) poly(DEAA) (400 MHz, CDCl<sub>3</sub>, 25 °C). <b>×</b>: Tetramethylsilane.</p>
Full article ">Figure 3
<p>Photographs of poly(DMαHAA-<span class="html-italic">co</span>-DEAA), obtained in Run 5, in water (1 wt %): (<b>a</b>) at 50 °C; (<b>b</b>) at 44 °C; and (<b>c</b>) at 25 °C; (<b>d</b>) Plots of content of DMαHAA unit versus <span class="html-italic">T</span><sub>c</sub>.</p>
Full article ">Scheme 1
<p>Radical (co)polymerization of DMMA and DMαHAA with DEAA.</p>
Full article ">
10156 KiB  
Review
Emerging Multifunctional NIR Photothermal Therapy Systems Based on Polypyrrole Nanoparticles
by Mozhen Wang
Polymers 2016, 8(10), 373; https://doi.org/10.3390/polym8100373 - 20 Oct 2016
Cited by 56 | Viewed by 14546
Abstract
Near-infrared (NIR)-light-triggered therapy platforms are now considered as a new and exciting possibility for clinical nanomedicine applications. As a promising photothermal agent, polypyrrole (PPy) nanoparticles have been extensively studied for the hyperthermia in cancer therapy due to their strong NIR light photothermal effect [...] Read more.
Near-infrared (NIR)-light-triggered therapy platforms are now considered as a new and exciting possibility for clinical nanomedicine applications. As a promising photothermal agent, polypyrrole (PPy) nanoparticles have been extensively studied for the hyperthermia in cancer therapy due to their strong NIR light photothermal effect and excellent biocompatibility. However, the photothermal application of PPy based nanomaterials is still in its preliminary stage. Developing PPy based multifunctional nanomaterials for cancer treatment in vivo should be the future trend and object for cancer therapy. In this review, the synthesis of PPy nanoparticles and their NIR photothermal conversion performance were first discussed, followed by a summary of the recent progress in the design and implementation on the mulitifunctionalization of PPy or PPy based therapeutic platforms, as well as the introduction of their exciting biomedical applications based on the synergy between the photothermal conversion effect and other stimulative responsibilities. Full article
Show Figures

Figure 1

Figure 1
<p>Oxidative polymerization of pyrrole to polypyrrole.</p>
Full article ">Figure 2
<p>(<b>a</b>,<b>b</b>) Schematic illustration of the formation process and mechanism of PPy NPs in an aqueous dispersion of water-soluble polymer; (<b>c</b>) SEM images of the resulting PPy NPs (inset: photograph showing a Petri dish containing 100 g of PPy NPs obtained in a single polymerization reaction); (<b>d</b>) Tilted and cross-section SEM images of the PPy NPs stacked on a substrate (scale bar in insets: 100 nm). Reproduced with permission from [<a href="#B82-polymers-08-00373" class="html-bibr">82</a>].</p>
Full article ">Figure 3
<p>Photographs of pyrrole samples before (<b>a</b>); after polymerization (<b>b</b>,<b>c</b>); and after lyophilization (<b>d</b>,<b>e</b>). (The right of (<b>d</b>) is the SEM image of the sample in (<b>b</b>)). Reproduced with permission from [<a href="#B85-polymers-08-00373" class="html-bibr">85</a>].</p>
Full article ">Figure 4
<p>Representative (<b>a</b>) SEM and (<b>b</b>) TEM images of PPy NPs; (<b>c</b>) UV-vis-NIR spectra of PPy NPs at various concentrations; (<b>d</b>) Photothermal effect of pure water and PPy NPs with different concentrations upon the irradiation of 1 W·cm<sup>−2</sup> 808 nm laser. Reproduced with permission from [<a href="#B87-polymers-08-00373" class="html-bibr">87</a>].</p>
Full article ">Figure 5
<p>In vivo photothermal therapy study using intravenously injected PPy NPs. (<b>a</b>) Tumor growth rates of groups after different treatments; (<b>b</b>) Survival curves of mice bearing 4T1 tumor after various treatments; (<b>c</b>) Representative photos of tumors on mice after various treatments (only laser treated and PPy + laser treated). Reproduced with permission from [<a href="#B87-polymers-08-00373" class="html-bibr">87</a>].</p>
Full article ">Figure 6
<p>PPy NPs prepared from the oxidative polymerization of Py in an aqueous solution of PVA and FeCl<sub>3</sub> can act as an efficient and stable photothermal coupling agent. (<b>a</b>) UV–vis–NIR spectra of various concentrations of PPy NPs in RPMI-1640 culture medium containing 10% FBS (the inset photograph shows various concentrations of PPy NPs dispersed in RPMI-1640 culture medium, indicating good dispersity); (<b>b</b>) Temperature elevation over a period of 10 min of exposure to NIR light (808 nm, 2 W) at various PPy NPs concentrations. RPMI-1640 culture medium was used as a control; (<b>c</b>) UV–vis–NIR spectra of PPy NPs and Au nanorods before and after five LASER ON/OFF cycles of NIR light (808 nm, 2 W) illumination (LASER ON time: 10 min; LASER OFF time: 30 min); (<b>d</b>) Temperature elevation of PPy NPs and Au nanorods over five LASER ON/OFF cycles of NIR laser irradiation. Reproduced with permission from [<a href="#B92-polymers-08-00373" class="html-bibr">92</a>].</p>
Full article ">Figure 7
<p>(<b>a</b>) Cell viability of HUVECs (human umbilical vein endothelial cells) with 24 h exposure to various concentrations of PPy NPs; (<b>b</b>) Cell viability of HeLa cells after treatment with different concentrations of PPy NPs and different NIR laser irradiation time. Reproduced with permission from [<a href="#B92-polymers-08-00373" class="html-bibr">92</a>].</p>
Full article ">Figure 8
<p>(<b>A</b>) Synthetic route of PEG-POA PPy NPs; (<b>B</b>) Graphic showing the synthesis of PEG-POA PPy NPs and photothermal-induced release of pyrene dye by the retro D-A reaction under NIR irradiation. Reproduced with permission from [<a href="#B101-polymers-08-00373" class="html-bibr">101</a>].</p>
Full article ">Figure 9
<p>SEM (<b>A</b>–<b>C</b>) and TEM (<b>D</b>–<b>F</b>) images of DSNs–NH<sub>2</sub> (<b>A</b>,<b>D</b>); PPy@DSNs–NH<sub>2</sub> (<b>B</b>,<b>E</b>); and PPy@DSNs–PEG (<b>C</b>,<b>F</b>). Reproduced with permission from [<a href="#B102-polymers-08-00373" class="html-bibr">102</a>].</p>
Full article ">Figure 10
<p>Schematic illustration of the preparation of DOX/PPy@DSNs–PEG for combined chemo-photothermal therapy. Reproduced with permission from [<a href="#B102-polymers-08-00373" class="html-bibr">102</a>].</p>
Full article ">Figure 11
<p>Schematic illustration of the synthesis of H-PPy microspheres. The SEM and TEM images of PS microspheres (<b>a</b>,<b>a’</b>), PS@PPy microspheres (<b>b</b>,<b>b’</b>), and H-PPy microspheres (<b>c</b>,<b>c’</b>). Reproduced with permission from [<a href="#B103-polymers-08-00373" class="html-bibr">103</a>].</p>
Full article ">Figure 12
<p>Schematic illustration of the loading and NIR-laser-triggered release of camptothecin (CPT) in H-PPy microspheres. (<b>a</b>) The releaseprofiles of CPT from H-PPy microspheres dispersed in the aqueous solution of DMSO (5% <span class="html-italic">v</span>/<span class="html-italic">v</span>) at 25 and 45 °C; (<b>b</b>) The release profile of CPT from H-PPy microspheres dispersed in the aqueous solution of DMSO (5% <span class="html-italic">v</span>/<span class="html-italic">v</span>) (0.1 mg·mL<sup>−1</sup>) under NIR laser (808 nm, 3.3 W·cm<sup>−2</sup>) irradiation for 5 min with an ON/OFF-mode every 12 h (-●-, left ordinate), and the corresponding temperature of the dispersion at every ON and OFF point (-▲-, right ordinate). As a control, the release profile of CPT in the same dispersion without NIR laser irradiation is also listed (-■-, left ordinate). Reproduced with permission from [<a href="#B103-polymers-08-00373" class="html-bibr">103</a>].</p>
Full article ">Figure 13
<p>Schematic procedure for the synthesis of spindle-like PPy HNCs in (<b>a</b>) an aqueous solution; TEM images of (<b>b</b>) Fe<sub>2</sub>O<sub>3</sub>; (<b>c</b>) Fe<sub>2</sub>O<sub>3</sub>@PPy; and (<b>d</b>) PPy HNCs; SEM image of (<b>e</b>) PPy HNCs. Reproduced with permission from [<a href="#B104-polymers-08-00373" class="html-bibr">104</a>].</p>
Full article ">Figure 14
<p>Preparation and characterization of Fe<sub>3</sub>O<sub>4</sub>@PPy–PEG nanocomposite. (<b>a</b>) Schematic illustration to show the synthesis of Fe<sub>3</sub>O<sub>4</sub>@PPy–PEG nanoparticles, the subsequent drug loading, and the remotely controlled cancer cell killing under dual physical stimuli. (<b>b</b>) TEM image of the synthesized Fe<sub>3</sub>O<sub>4</sub>@PPy–PEG nanoparticles; (<b>c</b>) UV–vis–NIR extinction spectra of Fe<sub>3</sub>O<sub>4</sub>@PPy–PEG nanoparticles in water (100 μg·mL<sup>−1</sup>). Inset: Photo of Fe<sub>3</sub>O<sub>4</sub>@PPy-PEG nanoparticles in different solutions including water, saline, and fetal bovine serum (FBS); (<b>d</b>) Temperature elevation of water and Fe<sub>3</sub>O<sub>4</sub>@PPy–PEG solution of different concentrations over a period of ~5.5 min under exposure of NIR light (808 nm, 0.75 W·cm<sup>−2</sup>) measured every 0.15 s using a digital thermocamera; (<b>e</b>) Field-dependentmagnetization loop of the Fe<sub>3</sub>O<sub>4</sub>@PPy–PEG sample. The absence of a hystersis loop suggested the superparamagnetic property of Fe<sub>3</sub>O<sub>4</sub>@PPy-PEG. Inset: Photos of Fe<sub>3</sub>O<sub>4</sub>@PPy–PEG solutions in the absence and presence of a magnet field; (<b>f</b>,<b>g</b>) T2-weighted MR images of the nanocomposite recorded using a 3 T MR scanner revealed a concentration-dependent darkening effect, showing a high transverse relaxivity (r2) of 87 mM<sup>−1</sup>·s<sup>−1</sup>. Reproduced with permission from [<a href="#B105-polymers-08-00373" class="html-bibr">105</a>].</p>
Full article ">Figure 15
<p>Synthetic scheme for ZrO<sub>2</sub> hollow nanospheres via the template assisted method, in situ polymerization of PPy into the ZrO<sub>2</sub> hollow nanospheres, and the principle of the integration of photothermal-chemo therapy, infrared thermal imaging, and CT imaging of ZrO<sub>2</sub> hollow nanospheres loading with PPy and Dox under NIR laser irradiation. Reproduced with permission from [<a href="#B118-polymers-08-00373" class="html-bibr">118</a>].</p>
Full article ">Figure 16
<p>In vitro and in vivo evaluation of CT imaging efficiency of ZPs. (<b>a</b>) CT values and images (inset) of ZPs with different concentrations; (<b>b</b>) In vivo CT imaging of mice model before and post injection; (<b>c</b>) CT image of the whole mini swine model; (<b>d</b>) CT values of liver, spleen, kidney and heart of mini swine at different time points before and post injection. Reproduced with permission from [<a href="#B118-polymers-08-00373" class="html-bibr">118</a>].</p>
Full article ">Figure 17
<p>Schematic illustration of the synthetic route of NaYF<sub>4</sub>:Yb/Er@PPy core–shell nanoplates. Reproduced with permission from [<a href="#B119-polymers-08-00373" class="html-bibr">119</a>].</p>
Full article ">Figure 18
<p>(<b>a</b>) In vitro CT images of iopromide and the dispersions of the NaYF<sub>4</sub>:Yb/Er@PPy nanoplates with different I or La concentrations; (<b>b</b>) CT value (HU) of iopromide (black line) and the NaYF<sub>4</sub>:Yb/Er@PPy nanoplates (red line) as a function of the concentration of I or La; (<b>c</b>) CT images of mice before and after intratumoral injection of the dispersion of the NaYF<sub>4</sub>:Yb/Er@PPy nanoplates. The position of tumors is marked by dotted circles. Reproduced with permission from [<a href="#B119-polymers-08-00373" class="html-bibr">119</a>].</p>
Full article ">Figure 19
<p>Schematic illustration for the synthesis of the multifunctional PPY@PAA/fmSiO<sub>2</sub> NPs as NIR light and pH dual-stimuli responsive drug vehicles for fluorescence imaging and chemo-photothermal synergistic cancer therapy in vitro and in vivo. Reproduced with permission from [<a href="#B121-polymers-08-00373" class="html-bibr">121</a>].</p>
Full article ">Figure 20
<p>Fluorescence quenching of DOX by PPys and HA–PPys. (<b>a</b>) Illustration showing the formation of a complex between a nanoparticle and DOX, and the subsequent fluorescence quenching of DOX; (<b>b</b>) Fluorescence spectra of DOX solution (10 μg in 100 μL deionized water) mixed with HA–PPys at various concentrations (from top to bottom: 0, 10, 20, 40, 60, 80, 100, 120, 150, and 200 μg in 200 μL); (<b>c</b>) Stern–Volmer plots demonstrating the quenching of DOX fluorescence by HA–PPys. <span class="html-italic">K</span>sv of PPys (■), HA10-PPys (●), HA20-PPys (∘), and HA40-PPys (▼) was calculated to be 2.3, 9.9, 33.4, and 40.2 mL·mg<sup>−1</sup>, respectively. Reproduced with permission from [<a href="#B122-polymers-08-00373" class="html-bibr">122</a>].</p>
Full article ">Figure 21
<p>Schematic illustration of the fabrication process of Gd-PEG-PPy NPs. Reproduced with permission from [<a href="#B123-polymers-08-00373" class="html-bibr">123</a>].</p>
Full article ">
7095 KiB  
Article
New Vistas on the Anionic Polymerization of Styrene in Non-Polar Solvents by Means of Density Functional Theory
by Hideo Morita and Marcel Van Beylen
Polymers 2016, 8(10), 371; https://doi.org/10.3390/polym8100371 - 20 Oct 2016
Cited by 7 | Viewed by 7997
Abstract
The elementary processes of anionic styrene polymerization in the gas phase and in cyclohexane were studied using M062X (a recently developed density functional theory (DFT) method) combined with the 6-31+G(d) basis sets, in order to clarify the complicated phenomena caused by the association [...] Read more.
The elementary processes of anionic styrene polymerization in the gas phase and in cyclohexane were studied using M062X (a recently developed density functional theory (DFT) method) combined with the 6-31+G(d) basis sets, in order to clarify the complicated phenomena caused by the association of the active chain-ends and elucidate the details of the polymerization mechanism. Three types of HSt2Li (a model structure of polystyryllithium chain-ends) were obtained; the well-known first structure in which Li is coordinated to the side chain, the second structure in which Li is coordinated to the phenyl ring, (both without the penultimate unit coordination), and the third structure in which Li is coordinated to both the chain-end unit and the penultimate styrene unit. Although the third HSt2Li is the most stable as expected, the free energy for the transition state of its reaction with styrene is higher than those for the other two transition states due to its steric hindrance. The free energy for the transition state of the reaction of the second HSt2Li with styrene is the lowest, suggesting that the route through it is the predominant reaction path. The penultimate unit effect, slower addition of styrene to HSt2Li than to HStLi, is attributed to coordination of the penultimate styrene units of the polystyryllithium dimer (one of the starting materials) to its Li atoms. The calculated enthalpy for the reaction barrier of the second HSt2Li with styrene in cyclohexane was found to agree with the observed apparent activation energy in benzene. Full article
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Optimized geometries and relative energies of (HStLi)<sub>2</sub> in the gas phase. The small drawing on the upper part of each structure is the simplified overhead view of the lower drawing; the carbon atoms of one HStLi (the upper HStLi in the lower drawing) are colored in blue. In the lower drawings, C–Li distances less than 0.225 nm are shown. ∆<span class="html-italic">Hr</span> and ∆<span class="html-italic">Gr</span>, the relative enthalpy and relative free energy, are expressed in kJ·mol<sup>–1</sup>.</p>
Full article ">Figure 2
<p>C–C bond distances of (HStLi)<sub>2</sub>(1-a) and (1-c). Geometry of the carbon framework of one chain-end unit (HSt-) is shown for (HStLi)<sub>2</sub>(1-a) and (1-c). Distances of C–C bonds are expressed in nm.</p>
Full article ">Figure 3
<p>Optimized geometries and relative energies of HStLi in the gas phase. The small drawing on the upper part of each structure is the simplified overhead view of the lower drawing. C–Li distances less than 0.225 nm are shown in the lower drawings, and C–C bond distances are shown in the upper drawings. ∆<span class="html-italic">Hr</span> and ∆<span class="html-italic">Gr</span>, the relative enthalpy and relative free energy, are expressed in kJ·mol<sup>–1</sup>.</p>
Full article ">Figure 4
<p>Electron density distribution of HStLi(2-a) (ea<sub>0</sub><sup>−3</sup> = 0.25).</p>
Full article ">Figure 5
<p>Schematic structural formulae of HStLi.</p>
Full article ">Figure 6
<p>Transition states for the addition of styrene to HStLi(2-a) and (2-b) in the gas phase. The small drawing on the upper part of each structure is the simplified overhead view of the lower drawing; the carbon atoms of styrene are colored in blue. In the lower drawings, the shortest distances between Li and the chain-end-unit carbon and between Li and styrene carbon are shown. The blue arrows in the lower drawings indicate the displacement vectors for the imaginary frequency of the transition state. ∆<span class="html-italic">Hr</span> and ∆<span class="html-italic">Gr</span>, the relative enthalpy and relative free energy, are expressed in kJ·mol<sup>–1</sup>.</p>
Full article ">Figure 7
<p>Transition states for the addition of styrene to HStLi(2-c) in the gas phase. ∆<span class="html-italic">Hr</span> and ∆<span class="html-italic">Gr</span>, the relative enthalpy and relative free energy, are expressed in kJ·mol<sup>–1</sup>. Drawing details as in <a href="#polymers-08-00371-f006" class="html-fig">Figure 4-1</a>.</p>
Full article ">Figure 8
<p>Reaction pathway for system(s-4-d) (St/[HStLi(2-c)]) in the gas phase. ∆<span class="html-italic">Hr</span> and ∆<span class="html-italic">Gr</span>, the relative enthalpy and relative free energy, are expressed in kJ·mol<sup>–1</sup>. Numerical values in the drawings indicate the distances between the two carbon atoms participating in the reaction, in nm.</p>
Full article ">Figure 9
<p>Reaction pathway for system(s-4-a) (St/[HStLi(2-a)]) in the gas phase. ∆<span class="html-italic">Hr</span> and ∆<span class="html-italic">Gr</span>, the relative enthalpy and relative free energy, are expressed in kJ·mol<sup>–1</sup>. Numerical values in the drawings as in <a href="#polymers-08-00371-f008" class="html-fig">Figure 5</a>.</p>
Full article ">Figure 10
<p>Enthalpy changes for the addition of styrene to HStLi in the gas phase.</p>
Full article ">Figure 11
<p>Free energy changes for the addition of styrene to HStLi in the gas phase.</p>
Full article ">Figure 12
<p>Optimized geometries and relative energies of representative (HSt<sub>2</sub>Li)<sub>2</sub> structures with and without the penultimate unit coordination in the gas phase. The small drawing on the upper part of each structure is the overhead view of the lower drawing; the carbon atoms of one HSt<sub>2</sub>Li (the upper HSt<sub>2</sub>Li in the lower drawing) are colored in blue. For the lower drawings of (9-c), the carbon atoms of the upper HSt<sub>2</sub>Li are also colored in blue for clarification. Hydrogen atoms are not shown. C–Li distances less than 0.225 nm and the distances between Li and the nearest penultimate-unit carbon are shown in the lower drawings. ∆<span class="html-italic">Hr</span> and ∆<span class="html-italic">Gr</span>, the relative enthalpy and relative free energy, are expressed in kJ·mol<sup>–1</sup>.</p>
Full article ">Figure 13
<p>Optimized geometries and relative energies of representative HSt<sub>2</sub>Li structures with and without the penultimate unit coordination in the gas phase. The small drawing on the upper part of each structure is the simplified overhead view of the lower drawing; for (10-c), the carbon atoms of the penultimate styrene unit are colored in blue. C–Li distances less than 0.225 nm, and the distance between Li and the nearest penultimate-unit carbon for (10-c) are shown in the lower drawings. ∆<span class="html-italic">Hr</span> and ∆<span class="html-italic">Gr</span>, the relative enthalpy and relative free energy, are expressed in kJ·mol<sup>–1</sup>. ∆<span class="html-italic">Hrp</span> and ∆<span class="html-italic">Grp</span> in the lower parentheses for (10-f) and (10-h) are the enthalpy and free energy with respect to 1/2[(HSt<sub>2</sub>Li)<sub>2</sub>(9-f)], in kJ·mol<sup>–1</sup>.</p>
Full article ">Figure 14
<p>Representative transition states for the addition of styrene to HSt<sub>2</sub>Li with and without the penultimate unit coordination in the gas phase. In the lower drawings the shortest distances between Li and the chain-end-unit carbon, between Li and styrene carbon, and between Li and the penultimate-unit carbon for (11-a) are shown. ∆<span class="html-italic">Hr</span> and ∆<span class="html-italic">Gr</span>, the relative enthalpy and relative free energy, are expressed in kJ·mol<sup>–1</sup>. ∆<span class="html-italic">Hrp</span> and ∆<span class="html-italic">Grp</span> in the lower parentheses of (11-g) and (11-k) are the enthalpy and free energy with respect to (St + 1/2[(HSt<sub>2</sub>Li)<sub>2</sub>(9-f)]), in kJ·mol<sup>–1</sup>. Hydrogen atoms are not shown. The other drawing details as in <a href="#polymers-08-00371-f006" class="html-fig">Figure 4-1</a>.</p>
Full article ">Figure 15
<p>Reaction pathway for system(s-11-a) (St/[HSt<sub>2</sub>Li(10-c)]) in the gas phase. ∆<span class="html-italic">Hr</span> and ∆<span class="html-italic">Gr</span>, the relative enthalpy and relative free energy, are expressed in kJ·mol<sup>–1</sup>. Hydrogen atoms are not shown. Numerical values in the drawings as in <a href="#polymers-08-00371-f008" class="html-fig">Figure 5</a>.</p>
Full article ">Figure 16
<p>Reaction pathway for system(s-11-g) (St/[HSt<sub>2</sub>Li(10-f)]) in the gas phase. ∆<span class="html-italic">Hr</span> and ∆<span class="html-italic">Gr</span>, the relative enthalpy and relative free energy, are expressed in kJ·mol<sup>–1</sup>. ∆<span class="html-italic">Hrp</span> and ∆<span class="html-italic">Grp</span> in the lower parentheses are the enthalpy and free energy with respect to (St + 1/2[(HSt<sub>2</sub>Li)<sub>2</sub>(9-f)]), in kJ·mol<sup>–1</sup>. The other drawing details as in <a href="#polymers-08-00371-f015" class="html-fig">Figure 12</a>.</p>
Full article ">Figure 17
<p>Enthalpy changes for the addition of styrene to HStLi and HSt<sub>2</sub>Li in the gas phase. The sub-transition state between the initial complex and the precursor for system(s-11-a) is not shown here. <sup>a</sup> p.u.c.: penultimate unit coordination.</p>
Full article ">Figure 18
<p>Free energy changes for the addition of styrene to HStLi and HSt<sub>2</sub>Li in the gas phase. The sub-transition state between the initial complex and the precursor for system(s-11-a) is not shown here. <sup>a</sup> p.u.c: penultimate unit coordination.</p>
Full article ">Figure 19
<p>PCM models for the typical structures in solvent environment.</p>
Full article ">Figure 20
<p>Geometries of (HStLi)<sub>2</sub>(1-a) in different environment. The (α)C–Li distances and the shortest and the longest distances of the (phenyl)C–Li bonds are shown in nm.</p>
Full article ">Figure 21
<p>Geometries and relative energies of HStLi(2-c) ((18-a) through (18-c)) and HStLi(2-a) ((18-d) through (18-f)) in different environment. In (18-a) through (18-c), the shortest and the longest distances of the (phenyl)C–Li bonds are shown, and in (18-d) through (18-f), the distances of the (α)C–Li and (ipso)C–Li bonds are shown. ∆<span class="html-italic">Hr</span> and ∆<span class="html-italic">Gr</span>, the relative enthalpy and relative free energy in the gas phase, are expressed in kJ·mol<sup>–1</sup>. ∆<span class="html-italic">Hrch</span> and ∆<span class="html-italic">Grch</span> are the relative enthalpy and relative free energy in cyclohexane, and ∆<span class="html-italic">Hrth</span> and ∆<span class="html-italic">Grth</span> are those in THF, in kJ·mol<sup>−1</sup>.</p>
Full article ">Figure 22
<p>The effect of solvent environment on the enthalpies and free energies for (HStLi)<sub>2</sub> and HStLi structures shown in <a href="#polymers-08-00371-f020" class="html-fig">Figure 17</a> and <a href="#polymers-08-00371-f021" class="html-fig">Figure 18</a>. ∆<span class="html-italic">H</span> and ∆<span class="html-italic">G</span> were calculated with respect to 1/2[(HStLi)<sub>2</sub>(1-a)] in the gas phase, for which ∆<span class="html-italic">H = 0</span> (<b>a</b>) or ∆<span class="html-italic">G</span> = 0 (<b>b</b>).</p>
Full article ">Figure 23
<p>Geometries and relative free energies in the gas phase for the three types of HSt<sub>2</sub>Li and the transition states of their reaction with styrene.</p>
Full article ">
2743 KiB  
Article
CaLB Catalyzed Conversion of ?-Caprolactone in Aqueous Medium. Part 1: Immobilization of CaLB to Microgels
by Stefan Engel, Heidi Höck, Marco Bocola, Helmut Keul, Ulrich Schwaneberg and Martin Möller
Polymers 2016, 8(10), 372; https://doi.org/10.3390/polym8100372 - 19 Oct 2016
Cited by 19 | Viewed by 9263
Abstract
The enzymatic ring-opening polymerization of lactones is a method of increasing interest for the synthesis of biodegradable and biocompatible polymers. In the past it was shown that immobilization of Candida antarctica lipase B (CaLB) and the reaction medium play an important role in [...] Read more.
The enzymatic ring-opening polymerization of lactones is a method of increasing interest for the synthesis of biodegradable and biocompatible polymers. In the past it was shown that immobilization of Candida antarctica lipase B (CaLB) and the reaction medium play an important role in the polymerization ability especially of medium ring size lactones like ?-caprolactone (?-CL). We investigated a route for the preparation of compartmentalized microgels based on poly(glycidol) in which CaLB was immobilized to increase its esterification ability. To find the ideal environment for CaLB, we investigated the acceptable water concentration and the accessibility for the monomer in model polymerizations in toluene and analyzed the obtained oligomers/polymers by NMR and SEC. We observed a sufficient accessibility for ?-CL to a toluene like hydrophobic phase imitating a hydrophobic microgel. Comparing free CaLB and Novozym® 435 we found that not the monomer concentration but rather the solubility of the enzyme, as well as the water concentration, strongly influences the equilibrium of esterification and hydrolysis. On the basis of these investigations, microgels of different polarity were prepared and successfully loaded with CaLB by physical entrapment. By comparison of immobilized and free CaLB, we demonstrated an effect of the hydrophobicity of the microenvironment of CaLB on its enzymatic activity. Full article
(This article belongs to the Special Issue Enzymatic Polymer Synthesis)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Distribution of ε-CL in toluene-d<sub>8</sub> and D<sub>2</sub>O measured by <sup>1</sup>H-NMR spectroscopy at temperatures from 25 to 55 °C.</p>
Full article ">Figure 2
<p>Conversion to oligomeric products <span class="html-italic">C<sub>oligo</sub></span> determined by <sup>1</sup>H-NMR spectroscopy and <span class="html-italic">M</span><sub>n</sub> values by SEC for the CaLB catalyzed polyesterification of ε-CL in (<b>a</b>) water and (<b>b</b>) toluene with varying ε-CL concentrations (water content ε-CL: 1530 ppm, toluene: 266 ppm).</p>
Full article ">Figure 3
<p>Enzymatic polymerization of ε-CL with (<b>a</b>) free CaLB and (<b>b</b>) Novozym<sup>®</sup> 435 in toluene with varying water content from 0 to 400 ppm. Illustration of the progression of <span class="html-italic">M</span><sub>n</sub>, <span class="html-italic">M</span><sub>w</sub> and <span class="html-italic">Ð</span> with increasing water content.</p>
Full article ">Figure 4
<p>SEC trace for the polymerization of ε-CL in toluene with free CaLB.</p>
Full article ">Figure 5
<p>SEC trace for the polymerization of ε-CL with Novozym<sup>®</sup> 435 in toluene showing (<b>a</b>) the oligomeric fraction; and (<b>b</b>) the high molecular weight fraction including the deconvolution of the original chromatogram by Gaussian fits.</p>
Full article ">Figure 6
<p>Hydrolytic activity of the CaLB loaded microgels MG <b>1</b> and MG <b>2</b> before and after dialysis (MWCO 100 kDa) and the CaLB-free microgels MG <b>1.1</b> and MG <b>2.1</b> as well as the non-immobilized CaLB as reference.</p>
Full article ">Scheme 1
<p>Conversion of ε-CL to 6-hydroxy caproic acid by hydrolysis or to oligo(caprolactone) by esterification catalyzed by free or immobilized CaLB in aqueous media.</p>
Full article ">Scheme 2
<p>Synthetic route for the preparation of (<b>a</b>) hydrophilic microgels with hydrophobic domains using P(EEGE)<sub>0.8</sub>-<span class="html-italic">b</span>-P(AGE)<sub>0.2</sub> <b>1</b> as prepolymer; and (<b>b</b>) hydrophobic microgels using P(<span class="html-italic">t</span>BGE)<sub>0.8</sub>-<span class="html-italic">b</span>-P(AGE)<sub>0.2</sub> <b>2</b>. Free CaLB was entrapped in situ during the microgel synthesis.</p>
Full article ">
19702 KiB  
Article
Material Evaluation and Process Optimization of CNT-Coated Polymer Powders for Selective Laser Sintering
by Shangqin Yuan, Jiaming Bai, Chee Kai Chua, Jun Wei and Kun Zhou
Polymers 2016, 8(10), 370; https://doi.org/10.3390/polym8100370 - 19 Oct 2016
Cited by 106 | Viewed by 12530
Abstract
Multi-walled carbon nanotubes (CNTs) as nano-reinforcements were introduced to facilitate the laser sintering process and enhance the thermal and mechanical properties of polymeric composites. A dual experimental-theoretical method was proposed to evaluate the processability and predict the process parameters of newly developed CNT-coated [...] Read more.
Multi-walled carbon nanotubes (CNTs) as nano-reinforcements were introduced to facilitate the laser sintering process and enhance the thermal and mechanical properties of polymeric composites. A dual experimental-theoretical method was proposed to evaluate the processability and predict the process parameters of newly developed CNT-coated polyamide 12 (CNTs/PA12) powders. The thermal conductivity, melt viscosity, phase transition and temperature-dependent density and heat capacity of PA12 and CNTs/PA12 powders were characterized for material evaluation. The composite powders exhibited improved heat conduction and heat absorption compared with virgin polymer powders, and the stable sintering range of composite powders was extended and found to be favourable for the sintering process. The microstructures of sintered composites revealed that the CNTs remained at the powder boundaries and formed network architectures, which instantaneously induced the significant enhancements in tensile strength, elongation at break and toughness without sacrificing tensile modulus. Full article
(This article belongs to the Special Issue Three-Dimensional Structures: Fabrication and Application)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>(<b>a</b>) building platform of EOS P395 machine regarding as the <span class="html-italic">X</span>–<span class="html-italic">Y</span> plane; (<b>b</b>) schematic illustration of the critical parameters in laser sintering process; (<b>c</b>) micro tensile specimens (ASTM D638, type IV) produced in the <span class="html-italic">X</span>–<span class="html-italic">Y</span> and <span class="html-italic">X</span>–<span class="html-italic">Z</span> planes; (<b>d</b>) the polished specimen for microstructure characterization in the <span class="html-italic">X</span>–<span class="html-italic">Y</span> (top surface) and <span class="html-italic">Y</span>–<span class="html-italic">Z</span> (side surface) planes.</p>
Full article ">Figure 2
<p>(<b>a</b>) DSC diagrams of PA12 and CNTs/PA12 upon heating and cooling at the rate of 10 °C/min; (<b>b</b>) size distribution of PA12 and CNTs/PA12 (0.5 wt %); SEM images of (<b>c</b>) the SEM image of an entire composite powder and then zoomed in to investigate the surface coating of CNTs; (<b>d</b>) the surface layer of CNTs which are lighten network structure; (<b>e</b>) avalanche angle graph indicating the required average angle to start and maintain the flow of the PA12 and CNTs/PA12 powders.</p>
Full article ">Figure 3
<p>Specific heat of PA12 and CNTs/PA12 at (<b>a</b>) powder phase and (<b>b</b>) liquid phase.</p>
Full article ">Figure 4
<p>(<b>a</b>) melt viscosity of PA12 and CNTs/PA12 at 200 °C; (<b>b</b>) specific heat absorption of PA12 and CNTs/PA12 over the process temperature range; (<b>c</b>,<b>d</b>) TGA plots of decomposition processes of PA12 and CNTs/PA12, respectively; (<b>e</b>,<b>f</b>) the optical images of the fusion process of PA12 and PA12/CNTs powders (the scale bars are 100 µm).</p>
Full article ">Figure 5
<p>Increasing temperature from 25 to 225 °C, the modified densities of PA12 and CNTs/PA12 exhibit linear relationships with temperature in three stages via the solid, melting and liquid state.</p>
Full article ">Figure 6
<p>Optical images of microstructures of (<b>a</b>) CNTs/PA12 and (<b>b</b>) PA12 from the <span class="html-italic">X</span>–<span class="html-italic">Y</span> plane; (<b>c</b>) CNTs/PA12 and (<b>d</b>) PA12 specimen cross-section from the <span class="html-italic">X</span>–<span class="html-italic">Z</span> plane and the molten powders highlighted. SEM images of surface structures of (<b>e</b>) CNTs/PA12 and (<b>f</b>) PA12 through mechanical grinding and polishing.</p>
Full article ">Figure 7
<p>The microstructures of the CNTs/PA12 parts sintered upon varied laser input energy in the <span class="html-italic">X</span>–<span class="html-italic">Z</span> plane (power (W), scanning speed (mm/s), hatching space (mm)) (<b>a</b>–<b>f</b>).</p>
Full article ">Figure 8
<p>Energy density influences on (<b>a</b>) tensile strength and (<b>b</b>) elongation at break of specimens in the <span class="html-italic">X</span>–<span class="html-italic">Y</span> plane; (<b>c</b>) tensile strength and (<b>d</b>) elongation at break of specimens in the <span class="html-italic">X</span>–<span class="html-italic">Z</span> plane.</p>
Full article ">Figure 9
<p>(<b>a</b>) The building platform of EOS P395 with the dimension of <span class="html-italic">X</span>, <span class="html-italic">Y</span>, <span class="html-italic">Z</span> (34 cm × 34 cm × 60 cm); (<b>b</b>) Light-weight CNTs/PA12 parts with complex geometric manufactured by SLS.</p>
Full article ">
5303 KiB  
Article
Copolymers Based on 1,3-Bis(carbazol-9-yl)benzene and Three 3,4-Ethylenedioxythiophene Derivatives as Potential Anodically Coloring Copolymers in High-Contrast Electrochromic Devices
by Chung-Wen Kuo, Teng-Lu Wu, Yuan-Chung Lin, Jeng-Kuei Chang, Ho-Rei Chen and Tzi-Yi Wu
Polymers 2016, 8(10), 368; https://doi.org/10.3390/polym8100368 - 19 Oct 2016
Cited by 23 | Viewed by 6221
Abstract
In this study, copolymers based on 1,3-bis(carbazol-9-yl)benzene (BCz) and three 3,4-ethylenedioxythiophene derivatives (3,4-ethylenedioxythiophene (EDOT), 3,4-(2,2-dimethylpropylenedioxy)thiophene (ProDOT-Me2), and 3,4-ethylenedithiathiophene (EDTT)) were electrochemically synthesized and their electrochemical and electrochromic properties were characterized. The anodic copolymer P(BCz-co-ProDOT) with BCz/ProDOT-Me2 = 1/1 [...] Read more.
In this study, copolymers based on 1,3-bis(carbazol-9-yl)benzene (BCz) and three 3,4-ethylenedioxythiophene derivatives (3,4-ethylenedioxythiophene (EDOT), 3,4-(2,2-dimethylpropylenedioxy)thiophene (ProDOT-Me2), and 3,4-ethylenedithiathiophene (EDTT)) were electrochemically synthesized and their electrochemical and electrochromic properties were characterized. The anodic copolymer P(BCz-co-ProDOT) with BCz/ProDOT-Me2 = 1/1 feed molar ratio showed high optical contrast (?T%) and coloring efficiency (?), measured as 52.5% and 153.5 cm2?C?1 at 748 nm, respectively. Electrochromic devices (ECDs) based on P(BCz-co-EDOT), P(BCz-co-ProDOT), and P(BCz-co-EDTT) as anodic polymer layers, and poly(3,4-ethylenedioxythiophene)-poly(styrene sulfonic acid) (PEDOT-PSS) as cathodic polymer layer were fabricated. P(BCz-co-ProDOT)/triple-layer PEDOT-PSS ECD showed three different colors (light yellow, yellowish-blue, and dark blue) at different applied potentials. In addition, the highest optical contrast (?T%) of P(BCz-co-ProDOT)/triple-layer PEDOT-PSS ECD was found to be 41% at 642 nm and the coloration efficiency was calculated to be 416.5 cm2?C?1 at 642 nm. All ECDs showed satisfactory optical memories and electrochemical cyclic stability. Full article
(This article belongs to the Special Issue Functionally Responsive Polymeric Materials)
Show Figures

Figure 1

Figure 1
<p>Schematic diagrams of P(BCz-<span class="html-italic">co</span>-ProDOT)/triple-layer PEDOT-PSS device.</p>
Full article ">Figure 2
<p>Anodic polarization curves of: (<b>a</b>) 2 mM EDTT; (<b>b</b>) 2 mM BCz; (<b>c</b>) 2 mM ProDOT-Me<sub>2</sub>; and (<b>d</b>) 2 mM EDOT in a PC/ACN (1:1, by volume) solution containing 0.2 M LiClO<sub>4</sub> at a scan rate of 100 mV∙s<sup>−1</sup>.</p>
Full article ">Figure 3
<p>Electrochemical synthesis of: (<b>a</b>) PBCz; (<b>b</b>) P(BCz-<span class="html-italic">co</span>-EDOT); (<b>c</b>) P(BCz-<span class="html-italic">co</span>-ProDOT); and (<b>d</b>) P(BCz-<span class="html-italic">co</span>-EDTT) in a PC/ACN (1:1, by volume) solution containing 0.2 M LiClO<sub>4</sub> at 100 mV∙s<sup>−1</sup> on ITO working electrode. Arrows, red line</p>
Full article ">Figure 4
<p>The electrochemical polymerization routes of: (<b>a</b>) PBCz; (<b>b</b>) P(BCz-<span class="html-italic">co</span>-EDOT); (<b>c</b>) P(BCz-<span class="html-italic">co</span>-ProDOT); and (<b>d</b>) P(BCz-<span class="html-italic">co</span>-EDTT).</p>
Full article ">Figure 4 Cont.
<p>The electrochemical polymerization routes of: (<b>a</b>) PBCz; (<b>b</b>) P(BCz-<span class="html-italic">co</span>-EDOT); (<b>c</b>) P(BCz-<span class="html-italic">co</span>-ProDOT); and (<b>d</b>) P(BCz-<span class="html-italic">co</span>-EDTT).</p>
Full article ">Figure 5
<p>Cyclic voltammetry (CV) curves of the P(BCz-<span class="html-italic">co</span>-ProDOT) film at different scan rates between 10 and 200 mV∙s<sup>−1</sup> in a PC/ACN (1:1, by volume) solution containing 0.2 M LiClO<sub>4</sub>. The inset is scan rate dependence of the P(BCz-<span class="html-italic">co</span>-ProDOT) anodic and cathodic peak current densities, respectively.</p>
Full article ">Figure 6
<p>UV–Visible spectra of: (<b>a</b>) PBCz; (<b>b</b>) P(BCz-<span class="html-italic">co</span>-EDOT); (<b>c</b>) P(BCz-<span class="html-italic">co</span>-ProDOT); and (<b>d</b>) P(BCz-<span class="html-italic">co</span>-EDTT) on ITO in a PC/ACN (1:1, by volume) solution containing 0.2 M LiClO<sub>4</sub>.</p>
Full article ">Figure 7
<p>Optical contrast of: (<b>a</b>) PBCz; (<b>b</b>) P(BCz-<span class="html-italic">co</span>-EDOT); (<b>c</b>) P(BCz-<span class="html-italic">co</span>-ProDOT); and (<b>d</b>) P(BCz-<span class="html-italic">co</span>-EDTT) electrodes in a PC/ACN (1:1, by volume) solution containing 0.2 M LiClO<sub>4</sub> between 0.0 V and 1.2 V with a residence time of 10 s.</p>
Full article ">Figure 8
<p>UV-Visible spectra of: (<b>a</b>) PBCz/double-layer PEDOT-PSS ECD; (<b>b</b>) P(BCz-<span class="html-italic">co</span>-ProDOT)/double-layer PEDOT-PSS ECD; and (<b>c</b>) P(BCz-<span class="html-italic">c</span>o-ProDOT)/triple-layer PEDOT-PSS ECD.</p>
Full article ">Figure 8 Cont.
<p>UV-Visible spectra of: (<b>a</b>) PBCz/double-layer PEDOT-PSS ECD; (<b>b</b>) P(BCz-<span class="html-italic">co</span>-ProDOT)/double-layer PEDOT-PSS ECD; and (<b>c</b>) P(BCz-<span class="html-italic">c</span>o-ProDOT)/triple-layer PEDOT-PSS ECD.</p>
Full article ">Figure 9
<p>Optical contrast of (<b>a</b>) PBCz/double-layer PEDOT-PSS ECD; (<b>b</b>) P(BCz-<span class="html-italic">co</span>-ProDOT)/double-layer PEDOT-PSS ECD; and (<b>c</b>) P(BCz-<span class="html-italic">co</span>-ProDOT)/triple-layer PEDOT-PSS ECD between 0.0 V and 2.0 V with a residence time of 10 s.</p>
Full article ">Figure 10
<p>Open circuit stability of the P(BCz-<span class="html-italic">co</span>-ProDOT)/triple-layer PEDOT-PSS device monitored at 642 nm.</p>
Full article ">Figure 11
<p>Cyclic voltammograms of: (<b>a</b>) PBCz/double-layer PEDOT-PSS ECD; (<b>b</b>) P(BCz-<span class="html-italic">co</span>-ProDOT)/double-layer PEDOT-PSS ECD; and (<b>c</b>) P(BCz-<span class="html-italic">co</span>-ProDOT)/triple-layer PEDOT-PSS ECD as a function of repeated scan with a scan rate of 500 mV∙s<sup>−1</sup> between 1 and 1000 cycles.</p>
Full article ">
2346 KiB  
Article
Preparation and Characterization of High Surface Area Activated Carbon Fibers from Lignin
by Jian Lin and Guangjie Zhao
Polymers 2016, 8(10), 369; https://doi.org/10.3390/polym8100369 - 18 Oct 2016
Cited by 34 | Viewed by 9369
Abstract
Activated carbon fibers (ACFs) were successfully prepared from softwood lignin, which was isolated with polyethylene glycol 400 (PEG-400) as a solvolysis reagent, by water steam activation. The pore characterization and adsorption property of ACFs were investigated. The results showed that all the ACFs [...] Read more.
Activated carbon fibers (ACFs) were successfully prepared from softwood lignin, which was isolated with polyethylene glycol 400 (PEG-400) as a solvolysis reagent, by water steam activation. The pore characterization and adsorption property of ACFs were investigated. The results showed that all the ACFs with more micropores exhibited high specific surface area and total pore volume which increased with the activation time prolonging; the highest ones were around 3100 m2/g and 1.5 mL/g, respectively. The specific surface area and total pore volume were much larger than those of other types of lignin-based ACFs and activated charcoal. Besides, with increasing activation time, the amount of graphitic carbon, which was the main compound on the surface of ACFs, decreased, while the amount of functional groups containing C–O slightly increased. In addition, the adsorption capacity of ACFs for methylene blue was highly increased as the activation time increased. Accordingly, lignin isolated with PEG is a promising precursor for ACF production. Full article
(This article belongs to the Special Issue Polymeric Fibers)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>SEM morphologies of CFs (<b>A</b>) and ACFs obtained from CFs activated at 900 °C for (<b>B</b>) 30 min; (<b>C</b>) 60 min; (<b>D</b>) 90 min (white bar = 5 μm).</p>
Full article ">Figure 2
<p>N<sub>2</sub> adsorption-desorption isotherms at 77 K (<b>A</b>) and pore size distribution; (<b>B</b>) of CFs and ACFs prepared with various activation times, respectively.</p>
Full article ">Figure 3
<p>X-ray photoelectron spectroscopy spectra of CFs and ACFs (<b>A</b>); and of C1s region for ACFs-90 (<b>B</b>).</p>
Full article ">Figure 4
<p>Fourier transform infrared spectroscopy of CFs and of ACFs prepared by different activation time.</p>
Full article ">Figure 5
<p>Methylene blue adsorption capacity of various carbon materials. (<b>1</b>) Charcoal; (<b>2</b>) Activated charcoal; (<b>3</b>) CFs; (<b>4</b>), (<b>5</b>) and (<b>6</b>) ACFs treated with 30, 60 and 90 min activation, respectively.</p>
Full article ">
2107 KiB  
Article
Multiresponsive Behavior of Functional Poly(p-phenylene vinylene)s in Water
by Kanykei Ryskulova, Anupama Rao Gulur Srinivas, Thomas Kerr-Phillips, Hui Peng, David Barker, Jadranka Travas-Sejdic and Richard Hoogenboom
Polymers 2016, 8(10), 365; https://doi.org/10.3390/polym8100365 - 18 Oct 2016
Cited by 6 | Viewed by 7324
Abstract
The multiresponsive behavior of functionalized water-soluble conjugated polymers (CPs) is presented with potential applications for sensors. In this study, we investigated the aqueous solubility behavior of water-soluble CPs with high photoluminescence and with a particular focus on their pH and temperature responsiveness. For [...] Read more.
The multiresponsive behavior of functionalized water-soluble conjugated polymers (CPs) is presented with potential applications for sensors. In this study, we investigated the aqueous solubility behavior of water-soluble CPs with high photoluminescence and with a particular focus on their pH and temperature responsiveness. For this purpose, two poly(phenylene vinylene)s (PPVs)—namely 2,5-substituted PPVs bearing both carboxylic acid and methoxyoligoethylene glycol units—were investigated, with different amount of carboxylic acid units. Changes in the pH and temperature of polymer solutions led to a response in the fluorescence intensity in a pH range from 3 to 10 and for temperatures ranging from 10 to 85 °C. Additionally, it is demonstrated that the polymer with the largest number of carboxylic acid groups displays upper critical solution temperature (UCST)-like thermoresponsive behavior in the presence of a divalent ion like Ca2+. The sensing capability of these water-soluble PPVs could be utilized to design smart materials with multiresponsive behavior in biomedicine and soft materials. Full article
(This article belongs to the Special Issue Young Talents in Polymer Science)
Show Figures

Figure 1

Figure 1
<p>Synthetic scheme of PMEE-PDTriG.</p>
Full article ">Figure 2
<p>Structures of the polymers: PDTriG and PMEE-PDTriG.</p>
Full article ">Figure 3
<p>Emission and excitation spectra of (<b>a</b>) PDTriG; (<b>b</b>) PMEE-PDTriG, measured at pH = 13, 0.01 M. Fluorescence spectra of (<b>c</b>) PDTriG; (<b>d</b>) PMEE-PDTriG at different pH values at 20 °C, 0.01 mg/mL. Linear fit of fluorescence intensity of (<b>e</b>) PDTriG (<b>f</b>) PMEE-PDTriG as a function of pH at emission λ<sub>max</sub>.</p>
Full article ">Figure 4
<p>Fluorescence emission as a function of temperature at different pH values (<b>a</b>) PMEE-PDTriG. Thermal stability with heating and cooling cycles of PMEE-PDTriG at (<b>b</b>) pH = 13; (<b>c</b>) pH = 10; (<b>d</b>) pH = 7.</p>
Full article ">Figure 5
<p>(<b>a</b>) Fluorescence emission spectra of PMEE-PDTriG at low temperatures, from 4 to 20 °C; (<b>b</b>) emission intensity at emission maxima, λ<sub>max</sub> versus temperature plot.</p>
Full article ">Figure 6
<p>(<b>a</b>) UV–vis spectra of PDTriG (pH = 10, 0.5 mg/mL) on addition of CaCl<sub>2</sub> (1:1 equivalents) in basic media at 25 °C after 5 min (red), after 30 min (green), after 2 h (blue), after 3 h (light blue), and at 60 °C (purple); (<b>b</b>) visual observation of complexation within time demonstrating the phase separation of PDTriG in presence of calcium(II) ions.</p>
Full article ">Figure 7
<p>Transmittance as a function of temperature for PDTriG (black) and PDTriG with CaCl<sub>2</sub> (red) at pH = 10 (0.5 mg/mL) measured at a wavelength of 600 nm.</p>
Full article ">Scheme 1
<p>General polymer structure with stimuli-responsive functional units, its response to pH, temperature, and upper critical solution temperature (UCST)-like behavior when complexed with Ca<sup>2+</sup>.</p>
Full article ">Scheme 2
<p>Schematic representation of the reversible binding of PDTriG with CaCl<sub>2</sub> in basic media leading to UCST behavior.</p>
Full article ">
2707 KiB  
Review
A Review of Thermo- and Ultrasound-Responsive Polymeric Systems for Delivery of Chemotherapeutic Agents
by Az-Zamakhshariy Zardad, Yahya Essop Choonara, Lisa Claire Du Toit, Pradeep Kumar, Mostafa Mabrouk, Pierre Pavan Demarco Kondiah and Viness Pillay
Polymers 2016, 8(10), 359; https://doi.org/10.3390/polym8100359 - 18 Oct 2016
Cited by 80 | Viewed by 10531
Abstract
There has been an exponential increase in research into the development of thermal- and ultrasound-activated delivery systems for cancer therapy. The majority of researchers employ polymer technology that responds to environmental stimuli some of which are physiologically induced such as temperature, pH, as [...] Read more.
There has been an exponential increase in research into the development of thermal- and ultrasound-activated delivery systems for cancer therapy. The majority of researchers employ polymer technology that responds to environmental stimuli some of which are physiologically induced such as temperature, pH, as well as electrical impulses, which are considered as internal stimuli. External stimuli include ultrasound, light, laser, and magnetic induction. Biodegradable polymers may possess thermoresponsive and/or ultrasound-responsive properties that can complement cancer therapy through sonoporation and hyperthermia by means of High Intensity Focused Ultrasound (HIFU). Thermoresponsive and other stimuli-responsive polymers employed in drug delivery systems can be activated via ultrasound stimulation. Polyethylene oxide/polypropylene oxide co-block or triblock polymers and polymethacrylates are thermal- and pH-responsive polymer groups, respectively but both have proven to have successful activity and contribution in chemotherapy when exposed to ultrasound stimulation. This review focused on collating thermal- and ultrasound-responsive delivery systems, and combined thermo-ultrasonic responsive systems; and elaborating on the advantages, as well as shortcomings, of these systems in cancer chemotherapy. The mechanisms of these systems are explicated through their physical alteration when exposed to the corresponding stimuli. The properties they possess and the modifications that enhance the mechanism of chemotherapeutic drug delivery from systems are discussed, and the concept of pseudo-ultrasound responsive systems is introduced. Full article
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Conceptual illustration representing the drug release mechanism of a thermoresponsive micellar system with a lower critical solution temperature (LCST) (outer shell: thermoresponsive segments, inner core: hydrophobic segments). (Source: de Oliveira et al. [<a href="#B29-polymers-08-00359" class="html-bibr">29</a>]. Licenced under a Creative Commons Attribution License).</p>
Full article ">Figure 2
<p>Schematic illustrating low and high power ultrasound assisting in drug delivery though microbubbles and cavitation (Source: Zhao et al. [<a href="#B36-polymers-08-00359" class="html-bibr">36</a>]. Licenced under a Creative Commons Attribution License).</p>
Full article ">Figure 3
<p>Image illustrating a Near InfraRed Laser being applied to the site of delivery and the mechanism of action that occurs with heat stimulus. Adapted with permission from Zhang et al. [<a href="#B52-polymers-08-00359" class="html-bibr">52</a>]. Copyright <sup>©</sup> 2014. American Chemical Society.</p>
Full article ">Figure 4
<p>The molecular structure of the Chitosan-graft-PEI-candesartan polymer used in targeting pancreatic cancer cells [<a href="#B66-polymers-08-00359" class="html-bibr">66</a>]. (Source: Bao et al., 2014).</p>
Full article ">Figure 5
<p>The Molecular structure of the γ-cyclodextran nanocarrier system used against breast cancer cell lines [<a href="#B93-polymers-08-00359" class="html-bibr">93</a>]. (Source: Gourevich et al., 2013).</p>
Full article ">Figure 6
<p>Schematic illustrating various ultrasound-responsive mechanisms: (<b>a</b>) Application of focused ultrasound guides nanosystems to the site of action and disrupts vascular endothelial barrier allowing the nanosystem direct access to tumour cells; (<b>b</b>) Sonoporation of the tumour cell membrane increases its permeability with possible sonochemical shape change of nanosystem promoting entry into the cell; (<b>c</b>) Should the nanosystem incorporate an ultrasound-responsive component, extracellular/intracellular nanosystem disruption with subsequent drug release is also promoted.</p>
Full article ">Figure 7
<p>Structural configuration of sphingolipid ceramide loaded linear-dendritic nanoparticles grafted using P(NIPAM), PLLA and PLA [<a href="#B115-polymers-08-00359" class="html-bibr">115</a>]. (Source: Stover et al., 2008).</p>
Full article ">
4066 KiB  
Review
Heteroatom-Doped Carbon Nanostructures Derived from Conjugated Polymers for Energy Applications
by Yanzhen He, Xijiang Han, Yunchen Du, Bin Zhang and Ping Xu
Polymers 2016, 8(10), 366; https://doi.org/10.3390/polym8100366 - 17 Oct 2016
Cited by 47 | Viewed by 10144
Abstract
Heteroatom-doped carbon materials have been one of the most remarkable families of materials with promising applications in fuel cells, supercapacitors, and batteries. Among them, conjugated polymer (CP)-derived heteroatom-doped carbon materials exhibit remarkable electrochemical performances because the heteroatoms can be preserved at a relatively [...] Read more.
Heteroatom-doped carbon materials have been one of the most remarkable families of materials with promising applications in fuel cells, supercapacitors, and batteries. Among them, conjugated polymer (CP)-derived heteroatom-doped carbon materials exhibit remarkable electrochemical performances because the heteroatoms can be preserved at a relatively high content and keep stable under harsh working conditions. In this review, we summarized recent advances in the rational design and various applications of CP-derived heteroatom-doped carbon materials, including polyaniline (PANI), polypyrrole (PPy), and their ramification-derived carbons, as well as transition metal-carbon nanocomposites. The key point of considering CP-derived heteroatom-doped carbon materials as important candidates of electrode materials is that CPs contain only nonmetallic elements and some key heteroatoms in their backbones which provide great chances for the synthesis of metal-free heteroatom-doped carbon nanostructures. The presented examples in this review will provide new insights in designing and optimizing heteroatom-doped carbon materials for the development of anode and cathode materials for electrochemical device applications. Full article
(This article belongs to the Special Issue Conjugated Polymers 2016)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>(<b>a</b>) Fabrication of N- and O-doped mesoporous carbons by calcination of PANI/SBA-15 and then etching SBA-15. Linear sweep voltammetry (LSV) curves at 900 rpm (<b>b</b>) and the number of electrons transferred as a function of potential for PDMCs prepared at different temperatures (<b>c</b>). Reprinted with permission from [<a href="#B35-polymers-08-00366" class="html-bibr">35</a>].</p>
Full article ">Figure 2
<p>(<b>a</b>,<b>b</b>) TEM and (<b>c</b>) SEM images of fabricated C–N–Co catalysts: (<b>a</b>) VB12/silica colloid; (<b>b</b>) VB12/SBA-15; and (<b>c</b>) VB12/montmorillonite (MMT). Insets of (<b>a</b>–<b>c</b>) are the model illustration of the materials with multiple mesoporous structures. LVS polarization plots at 1600 rpm, 10 mV/s (<b>d</b>) and electron-transfer numbers (<b>e</b>) of different C–N–Co materials and Pt/C as functions of the electrode potential; (<b>f</b>) LSV polarization curves of VB12/silica colloid before and after 10,000 potential cycles in O<sub>2</sub>-saturated electrolyte. Reprinted with permission from [<a href="#B45-polymers-08-00366" class="html-bibr">45</a>].</p>
Full article ">Figure 3
<p>Schematic illustration for the fabrication of the electrode material application in an asymmetric supercapacitor device using bacterial cellulose (BC) as a template and precursor. Reprinted with permission from [<a href="#B54-polymers-08-00366" class="html-bibr">54</a>], copyright 2014, Wiley-VCH.</p>
Full article ">Figure 4
<p>(<b>a</b>) Fabrication of N-, O-, and S-tridoped mesoporous carbon (NOSCs) with the ability of catalyzing ORR and AOR; (<b>b</b>) ORR polarization plots of NOSC<sub>x</sub>-900 materials on RDE rotating at 1600 rpm; (<b>c</b>) CV curves of NOSC<sub>8</sub>-900 in 0.1 M KOH conditions with O<sub>2</sub> and N<sub>2</sub>-saturated; and (<b>d</b>) kinetic current density (<span class="html-italic">J</span><sub>k</sub>) of NOSC<sub>8</sub>-T catalysts for ORR at different potentials. Reprinted with permission from [<a href="#B58-polymers-08-00366" class="html-bibr">58</a>].</p>
Full article ">Figure 5
<p>(<b>a</b>) Illustration of the synthesis for N-GNRs-A; (<b>b</b>) photographs of fabricated 3D graphene nanoribbon aerogels derived without (left) or with (middle) 5 vol % Py GONRs suspension (10 mg<math display="inline"> <semantics> <mo>∙</mo> </semantics> </math>mL<sup>−1</sup>) under hydrothermal treatment. Photograph of ultralight N-GNRs-A standing on a dandelion (<b>c</b>) and in a hot flame of an alcohol burner (<b>d</b>); and (<b>e</b>) XRD patterns of (1) pristine MWCNTs, (2) GONRs, (3) GNRs-A, and (4) N-GNRs-A. Reprinted with permission from [<a href="#B62-polymers-08-00366" class="html-bibr">62</a>], copyright 2015, Wiley-VCH.</p>
Full article ">Figure 6
<p>Schematic illustration for the fabrication processes of nitrogen-doped CNFs. Reprinted with permission from [<a href="#B75-polymers-08-00366" class="html-bibr">75</a>].</p>
Full article ">Figure 7
<p>A schematic illustration depicting the synthesis route for N- and O-doped HCSs. Reprinted with permission from [<a href="#B85-polymers-08-00366" class="html-bibr">85</a>], copyright 2015, RSC Publishing.</p>
Full article ">Figure 8
<p>Schematic illustration of the fabrication of meso/micro-PoPD electrocatalyst. (<b>a</b>) Polymerization of oPD using the silica colloid as templates, and with the assistance of ammonium peroxydisulphate (APS); (<b>b</b>) carbonization of PoPD/SiO<sub>2</sub> materials in N<sub>2</sub> atmosphere, followed by etching the SiO<sub>2</sub> templates with 2.0 M NaOH solution to yield meso-PoPD; (<b>c</b>) the formation of the final meso/micro-PoPD materials by the further activation of the meso-PoPD with NH<sub>3</sub>. Reprinted with permission from [<a href="#B87-polymers-08-00366" class="html-bibr">87</a>].</p>
Full article ">Figure 9
<p>Schematic illustration of the preparation of poly(<span class="html-italic">o</span>-methylaniline) (POT) by a hydrothermal technique and N-doped carbon microspheres (NCMSs) from pyrolysis of POT. Reprinted with permission from [<a href="#B89-polymers-08-00366" class="html-bibr">89</a>].</p>
Full article ">
2390 KiB  
Article
Aromatic Copolyamides with Anthrazoline Units in the Backbone: Synthesis, Characterization, Pervaporation Application
by Galina A. Polotskaya, Alexandra Yu. Pulyalinа, Mikhail Ya. Goikhman, Irina V. Podeshvo, Irina A. Valieva and Alexander M. Toikka
Polymers 2016, 8(10), 362; https://doi.org/10.3390/polym8100362 - 17 Oct 2016
Cited by 15 | Viewed by 5759
Abstract
Copolyamides with anthrazoline units in the backbone (coPA) were synthesized and dense nonporous films were prepared by solvent evaporation. Glass transition temperature, density, and fractional free volume were determined for the dense nonporous films composed of polyamide and two of its copolymers containing [...] Read more.
Copolyamides with anthrazoline units in the backbone (coPA) were synthesized and dense nonporous films were prepared by solvent evaporation. Glass transition temperature, density, and fractional free volume were determined for the dense nonporous films composed of polyamide and two of its copolymers containing 20 and 30 mol % anthrazoline units in the backbone. Transport properties of the polymer films were estimated by sorption and pervaporation tests toward methanol, toluene, and their mixtures. An increase in anthrazoline fragments content leads to an increasing degree of methanol sorption but to a decreasing degree of toluene sorption. Pervaporation of a methanol–toluene mixture was studied over a wide range of feed concentration (10–90 wt % methanol). Maximal separation factor was observed for coPA-20 containing 20 mol % fragments with anthrazoline units; maximal total flux was observed for coPA-30 with the highest fractional free volume. Full article
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>The scheme of copolyamide (coPA) synthesis.</p>
Full article ">Figure 2
<p>(<b>a</b>) Thermogravimetric (TG) and (<b>b</b>) differential scanning calorimetry (DSC) curves of PA, coPA-20, and coPA-30.</p>
Full article ">Figure 3
<p>Scanning electron microscopy (SEM) micrographs of cross-section of PA, coPA-20, and coPA-30 films.</p>
Full article ">Figure 4
<p>Dependence of equilibrium sorption degree and interaction parameter <math display="inline"> <semantics> <mrow> <msub> <mi>χ</mi> <mn>1</mn> </msub> </mrow> </semantics> </math> on methanol concentration in methanol–toluene mixtures, 20 °C.</p>
Full article ">Figure 5
<p>Dependence of methanol concentration in the permeate on methanol concentration in the feed for the pervaporation of a methanol–toluene mixture. Vapor–liquid equilibrium curve of methanol and toluene mixture, 760 mm Hg.</p>
Full article ">Figure 6
<p>Dependence of (<b>a</b>) separation factor <span class="html-italic">α</span><sub>Methanol/Toluene</sub> and (<b>b</b>) total flux on methanol concentration in the feed for the pervaporation of a methanol–toluene mixture, 20 °C.</p>
Full article ">Figure 7
<p>Dependence of total flux and separation factor α<sub>Methanol/Toluene</sub> on temperature for the pervaporation of azeotropic methanol–toluene (70:30 wt %) mixture through coPA films, 20 °С.</p>
Full article ">Figure 8
<p>Dependence of methanol and toluene permeance on methanol concentration in the feed, 20 °С.</p>
Full article ">Figure 9
<p>Dependence of selectivity β<sub>Methanol-Toluene</sub> on methanol concentration in the feed for the pervaporation of a methanol–toluene mixture, 20 °С.</p>
Full article ">
2539 KiB  
Article
Synthesis of Novel Cobalt-Containing Polysilazane Nanofibers with Fluorescence by Electrospinning
by Qian Zhang, Dechang Jia, Zhihua Yang, Xiaoming Duan, Qingqing Chen and Yu Zhou
Polymers 2016, 8(10), 350; https://doi.org/10.3390/polym8100350 - 17 Oct 2016
Cited by 9 | Viewed by 8362
Abstract
Emission in the nanostructured materials is important in micro/nanoelectronic devices. We report here a strategy for the processing of micron and submicron fibers from a cobalt-containing hyperbranched polysilazane by electrospinning. The electrospun nanofibers have uniform average diameters of ~600 nm and lengths of [...] Read more.
Emission in the nanostructured materials is important in micro/nanoelectronic devices. We report here a strategy for the processing of micron and submicron fibers from a cobalt-containing hyperbranched polysilazane by electrospinning. The electrospun nanofibers have uniform average diameters of ~600 nm and lengths of ~10 ?m. The photophysical properties of polycobaltsilazane (PCSN) are studied using UV-VIS and photoluminescence spectroscopies. PCSN fibers display a series of emission peaks between 490 and 615 nm. The Co(II) doping into polysilazane leads to the emission from 465 to 415 nm. The emission wavelength shift of Co(III)-containing polysilazane is specific under 340 and 470 nm excitation wavelengths, respectively, while it is not observed with metal-free polysilazane. Thermogravimetric analysis-Differentical thermal analysis (TGA-DTA) profiles also show good thermostability of the PCSN fibers at 800 °C under Ar atmosphere. The use of PCSN offers both enhanced ceramic yields against ~5 wt % starting material and the fluorescence intensity of polymeric fibers. Full article
(This article belongs to the Special Issue Conjugated Polymers 2016)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>(<b>a</b>) Schematic representing of the electrospinning setup (1: power source, 2: the syringe with polymer solution and the needle, 3: collection target, and 4: wires attached to the power source); (<b>b</b>–<b>e</b>) SEM images of electrospun fibers of 20 wt % PCSN solution.</p>
Full article ">Figure 2
<p>(<b>a</b>) TEM image of the polymer fibers; (<b>b</b>,<b>c</b>) FIB images of polycobaltsilazane nanofibers; (<b>c</b>) the porous nature and cross-sectional view of the nanofiber; (<b>d</b>) SEM image of the nanofibers at PCSN/DMF ratios of 12 wt %; (<b>e</b>) SEM image of the nanofibers at PCSN/DMF ratios of 20 wt %; and (<b>f</b>) SEM image of the nanofibers at PCSN/DMF ratios of 25 wt %.</p>
Full article ">Figure 3
<p>FT-IR spectra of polysilazane (PSN) and with 20 wt % Co(en)<sub>3</sub>-containing polysilazane (PCSN). FTIR spectra of [Co(en)<sub>3</sub>]·Cl<sub>3-</sub>modified polysilazane (blue line), polysilazane (red line), and Co(en)<sub>3</sub> (cyan line). The strong absorptions from 1178 to 1080 cm<sup>−1</sup> correspond to Si–CH<sub>2</sub>.</p>
Full article ">Figure 4
<p>The fitting curves of XPS analysis of polycobaltsilazane. (<b>a</b>) The spectra of Si 2p reveals the Si–C bonding (yellow line), Si–H bonding (blue line) and Si–N bonding (pink line); (<b>b</b>) the spectra of C 1s reveals the C–C bonding (blue line) and C–Si bonding (Cyan line); (<b>c</b>) the spectra of N 1s reveals the Si–N bonding (Dark Cyan and blue line) and the N–H bonding (pink line); (<b>d</b>) the spectra of Co 2p reveals the characteristic of Co(II) ions (blue and Cyan line) and Co 2p3/2 (yellow line) and 2p1/2 (pink line) satellite structures. The spectrum curves (open circles) are deconvoluted by Gaussian fitting (red solid curves).</p>
Full article ">Figure 5
<p>Polymeric fiber thermograms obtained from simultaneous thermal analysis of TGA-DSC under Ar at a scanning rate of 10 K·min<sup>−1</sup>. (<b>a</b>) Thermogravimetric analysis; and (<b>b</b>,<b>c</b>) mass spectrometry quadrupole mass spectrometer (QMS) ion current curves of cross-linked polysilazane modified with 20 wt % Co(en)<sub>3</sub> showing the release of (<b>b</b>) hydrogen and methane; (<b>c</b>) ethane, and ethylamino fragments during the thermal degradation process.</p>
Full article ">Figure 6
<p>UV-Visible absorption spectra (<b>a</b>) and fluorescence (<b>b</b>) spectra of PCSN powder at room temperature; and (<b>b</b>) normalized photoluminescence excitation and emission spectra of polycobaltsilazane powder. The fluorescence studies were conducted at excitation wavelengths of 340 nm; the maximum emission wavelengths were observed at 390, 415, 485, 580, and 630 nm.</p>
Full article ">Figure 7
<p>The fluorescence micrographs of some polymer powder on commercially available filter paper under UV light (<b>a</b>) and (<b>b</b>), as well as daylight (<b>c</b>).</p>
Full article ">Scheme 1
<p>The approach involved in the synthesis of polycobaltsilazane: polysilazane reacted with the Co(III)-complex in DMF to form a conjugated polymer, polycobaltsilazane.</p>
Full article ">
5982 KiB  
Article
Relaxation Oscillation with Picosecond Spikes in a Conjugated Polymer Laser
by Wafa Musa Mujamammi, Saradh Prasad, Mohamad S. AlSalhi and Vadivel Masilamani
Polymers 2016, 8(10), 364; https://doi.org/10.3390/polym8100364 - 14 Oct 2016
Cited by 8 | Viewed by 5959
Abstract
Optically pumped conjugated polymer lasers are good competitors for dye lasers, often complementing and occasionally replacing them. This new type of laser material has broad bandwidths and high optical gains comparable to conventional laser dyes. Since the Stokes’ shift is unusually large, the [...] Read more.
Optically pumped conjugated polymer lasers are good competitors for dye lasers, often complementing and occasionally replacing them. This new type of laser material has broad bandwidths and high optical gains comparable to conventional laser dyes. Since the Stokes’ shift is unusually large, the conjugated polymer has a potential for high power laser action, facilitated by high concentration. This paper reports the results of a new conjugated polymer, the poly[(9,9-dioctyl-2,7-divinylenefluorenylene)-alt-co-{2-methoxy-5-(2-ethylhexyloxy)-1,4-phenylene}](PFO-co-MEH-PPV) material, working in the green region. Also discussed are the spectral and temporal features of the amplified spontaneous emissions (ASE) from the conjugated polymer PFO-co-MEH-PPV in a few solvents. When pumped by the third harmonic of the Nd:YAG laser of 10 ns pulse width, the time-resolved spectra of the ASE show relaxation oscillations and spikes of 600 ps pulses. To the best of our knowledge, this is the first report on relaxation oscillations in conjugated-polymer lasers. Full article
(This article belongs to the Special Issue Conjugated Polymers 2016)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>The molecular structure of the conjugated-polymer PFO-<span class="html-italic">co</span>-MEH-PPV (green polymer, GP).</p>
Full article ">Figure 2
<p>Absorption spectra of GP in toluene for concentration ranging from 1 nanomolar to 50 nanomolar.</p>
Full article ">Figure 3
<p>Fluorescence spectra of GP in toluene for concentration ranging from 10 nanomolar to 200 nanomolar.</p>
Full article ">Figure 4
<p>(<b>a</b>) Laser induced fluorescence (LIF) for high concentration (1 µM) at low pump power (1 mJ) and (<b>b</b>) amplified spontaneous emission (ASE) for the same concentration at 2.3 mJ pump power.</p>
Full article ">Figure 5
<p>Shows the temporal profile of (<b>a</b>) pump pulse; (<b>b</b>) LIF and (<b>c</b>) ASE, with a full width half maximum (FWHM) of 10, 5 and 1 ns respectively.</p>
Full article ">Figure 6
<p>Shows the temporal profile of ASE for pump pulse energy (4 mJ) well above threshold, one could see the emission become jittery with spikes of 600 ps attributed the relaxation oscillation.</p>
Full article ">Figure 7
<p>Shows the temporal oscillation trace of another relaxation oscillation pulse, indication of non-reproducible spikes.</p>
Full article ">Figure 8
<p>(<b>a</b>) Show the three dimensional (3D) ASE profile of GP under transverse excitation. It is displayed with wavelength (nm) in <span class="html-italic">x</span>-axis, Intensity (a.u) in <span class="html-italic">y</span>-axis and Time in <span class="html-italic">z</span>-axis, each fame represents a time duration of 0.5 ns. Note: ASE starts at <span class="html-italic">z</span> = 6 ns and reaches a maximum at 8 ns; but rapidly falls in next 500 ps. (<b>b</b>) Show the 3D representation of non-reproducible spikes of relaxation oscillation.</p>
Full article ">Figure 9
<p>Show the 3D ASE profile of GP under longitudinal excitation. One could see that the spectral width is broader than transverse excitation, due to exponential attenuation of pump pulse, still the power is sufficient to produce relaxation oscillation (Note that different color lines are used to differentiate one time frame from the other).</p>
Full article ">
978 KiB  
Article
Highly Branched Bio-Based Unsaturated Polyesters by Enzymatic Polymerization
by Hiep Dinh Nguyen, David Löf, Søren Hvilsted and Anders Egede Daugaard
Polymers 2016, 8(10), 363; https://doi.org/10.3390/polym8100363 - 14 Oct 2016
Cited by 17 | Viewed by 9009
Abstract
A one-pot, enzyme-catalyzed bulk polymerization method for direct production of highly branched polyesters has been developed as an alternative to currently used industrial procedures. Bio-based feed components in the form of glycerol, pentaerythritol, azelaic acid, and tall oil fatty acid (TOFA) were polymerized [...] Read more.
A one-pot, enzyme-catalyzed bulk polymerization method for direct production of highly branched polyesters has been developed as an alternative to currently used industrial procedures. Bio-based feed components in the form of glycerol, pentaerythritol, azelaic acid, and tall oil fatty acid (TOFA) were polymerized using an immobilized Candida antarctica lipase B (CALB) and the potential for an enzymatic synthesis of alkyds was investigated. The developed method enables the use of both glycerol and also pentaerythritol (for the first time) as the alcohol source and was found to be very robust. This allows simple variations in the molar mass and structure of the polyester without premature gelation, thus enabling easy tailoring of the branched polyester structure. The postpolymerization crosslinking of the polyesters illustrates their potential as binders in alkyds. The formed films had good UV stability, very high water contact angles of up to 141° and a glass transition temperature that could be controlled through the feed composition. Full article
(This article belongs to the Special Issue Enzymatic Polymer Synthesis)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Spectroscopic analysis of the UBP obtained from a feed composition of glycerol, azelaic acid, and TOFA with a molar ratio of 1:1:0.57 (UBP3). (<b>a</b>) FT-IR spectrum; (<b>b</b>) Expanded DEPT135 NMR spectrum.</p>
Full article ">Scheme 1
<p>CALB-catalyzed preparation of UBPs by one-pot bulk polymerization between azelaic acid, glycerol, and TOFA.</p>
Full article ">Scheme 2
<p>Two-stage synthesis of UBPs containing pentaerythritol. In the first step PTA was prepared from pentaerythritol using an excess of azelaic acid. Subsequently glycerol and TOFA as well as CALB were added and polymerization took place in the second stage.</p>
Full article ">
2347 KiB  
Article
Atomistic Modelling of Confined Polypropylene Chains between Ferric Oxide Substrates at Melt Temperature
by Ali Gooneie, Joamin Gonzalez-Gutierrez and Clemens Holzer
Polymers 2016, 8(10), 361; https://doi.org/10.3390/polym8100361 - 14 Oct 2016
Cited by 19 | Viewed by 8502
Abstract
The interactions and conformational characteristics of confined molten polypropylene (PP) chains between ferric oxide (Fe2O3) substrates were investigated by molecular dynamics (MD) simulations. A comparative analysis of the adsorbed amount shows strong adsorption of the chains on the high-energy [...] Read more.
The interactions and conformational characteristics of confined molten polypropylene (PP) chains between ferric oxide (Fe2O3) substrates were investigated by molecular dynamics (MD) simulations. A comparative analysis of the adsorbed amount shows strong adsorption of the chains on the high-energy surface of Fe2O3. Local structures formed in the polymer film were studied utilizing density profiles, orientation of bonds, and end-to-end distance of chains. At interfacial regions, the backbone carbon-carbon bonds of the chains preferably orient in the direction parallel to the surface while the carbon-carbon bonds with the side groups show a slight tendency to orient normal to the surface. Based on the conformation tensor data, the chains are compressed in the normal direction to the substrates in the interfacial regions while they tend to flatten in parallel planes with respect to the surfaces. The orientation of the bonds as well as the overall flattening of the chains in planes parallel to the solid surfaces are almost identical to that of the unconfined PP chains. Also, the local pressure tensor is anisotropic closer to the solid surfaces of Fe2O3 indicating the influence of the confinement on the buildup imbalance of normal and tangential pressures. Full article
(This article belongs to the Special Issue Computational Modeling and Simulation in Polymer)
Show Figures

Figure 1

Figure 1
<p>The temperature (<b>circles</b>) and volume (<b>squares</b>) of the system during the relaxation process as a function of time. Each stage of the process is numbered and separated with vertical dashed lines.</p>
Full article ">Figure 2
<p>Schematic representation of the simulated confined systems. In the figure, only the backbone carbon atoms of the chains are shown to preserve clarity. The two ending carbon atoms of each PP chain are plotted in slightly larger circles filled with <b>red</b> color. The substrates are shown in <b>black</b> circles filled with gray color at the <b>bottom</b> and <b>top</b> of the simulation box.</p>
Full article ">Figure 3
<p>Local mass density profile, <math display="inline"> <semantics> <mi>ρ</mi> </semantics> </math>, across the film thickness. The horizontal dashed line represents the mass density of the polymer from the bulk simulations. The results are calculated for the confined PP/Fe<sub>2</sub>O<sub>3</sub> system at 458 K and 1 atm.</p>
Full article ">Figure 4
<p>(<b>a</b>) Local contributions to the total mass density profile (<b>open circles</b>) from segments of the first polymer layer adjacent to the substrates (<b>red continuous line</b>); (<b>b</b>) The accumulated number of hydrogen and carbon atoms across the film thickness calculated from the number density profiles of the corresponding atoms. The results are calculated for the confined PP/Fe<sub>2</sub>O<sub>3</sub> system at 458 K and 1 atm.</p>
Full article ">Figure 5
<p>Local order parameter (<math display="inline"> <semantics> <mrow> <msub> <mi>P</mi> <mn>2</mn> </msub> </mrow> </semantics> </math>) for C–C bonds in (<b>a</b>) backbone and (<b>b</b>) with side chains as a function of distance from the surface of the substrate. The results are calculated for the confined PP/Fe<sub>2</sub>O<sub>3</sub> system at 458 K and 1 atm.</p>
Full article ">Figure 6
<p>Local order parameter (<math display="inline"> <semantics> <mrow> <msub> <mi>P</mi> <mn>2</mn> </msub> </mrow> </semantics> </math>) as a function of distance from the surface of the substrate for C–C bonds of the backbone (squares), cords connecting two C–C bonds (circles), and cords connecting three C–C bonds (triangles). The results are calculated for the confined PP/Fe<sub>2</sub>O<sub>3</sub> system at 458 K and 1 atm.</p>
Full article ">Figure 7
<p>Values of the diagonal components of the Saupe matrix, <math display="inline"> <semantics> <mrow> <msub> <mi mathvariant="bold-italic">S</mi> <mrow> <mi>ab</mi> </mrow> </msub> </mrow> </semantics> </math>, as a function of <span class="html-italic">z</span> coordinate. The results are calculated for the confined PP/Fe<sub>2</sub>O<sub>3</sub> system at 458 K and 1 atm.</p>
Full article ">Figure 8
<p>The overall alignment of PP chains along the thickness of the film either parallel (<math display="inline"> <semantics> <mrow> <msubsup> <mi mathvariant="bold-italic">C</mi> <mrow> <mi>xx</mi> </mrow> <mn>0</mn> </msubsup> <mo>+</mo> <msubsup> <mrow> <mi mathvariant="bold-italic">C</mi> </mrow> <mrow> <mi>yy</mi> </mrow> <mn>0</mn> </msubsup> </mrow> </semantics> </math>) or normal (<math display="inline"> <semantics> <mrow> <msubsup> <mi mathvariant="bold-italic">C</mi> <mrow> <mi>zz</mi> </mrow> <mn>0</mn> </msubsup> </mrow> </semantics> </math>) to the substrates expressed utilizing the concept of the conformation tensor. The results in (<b>a</b>) are calculated based on Equation (5); in (<b>b</b>), Equation (5) was reduced by the end-to-end distance of each confined chain instead of the averaged end-to-end distance of the unperturbed chains. Therefore, the ‘0’ superscript was removed from the notations of the conformation tensor and its components to emphasize this distinction. The data are calculated for each chain individually and are plotted as a function of the <span class="html-italic">z</span> coordinate of the center of mass of that respective chain. Note that the horizontal error bars are multiplied by a factor of 10 to increase their visibility. The results are calculated for the confined PP/Fe<sub>2</sub>O<sub>3</sub> system at 458 K and 1 atm.</p>
Full article ">Figure 9
<p>Instantaneous (<b>black</b> curve) and running average (<b>red</b> curve) profiles of (<b>a</b>) <math display="inline"> <semantics> <mrow> <msub> <mi>P</mi> <mrow> <mi>xx</mi> </mrow> </msub> <mo>(</mo> <mi>z</mi> <mo>)</mo> </mrow> </semantics> </math>; (<b>b</b>) <math display="inline"> <semantics> <mrow> <msub> <mi>P</mi> <mrow> <mi>yy</mi> </mrow> </msub> <mo>(</mo> <mi>z</mi> <mo>)</mo> </mrow> </semantics> </math>; (<b>c</b>) <math display="inline"> <semantics> <mrow> <msub> <mi>P</mi> <mrow> <mi>zz</mi> </mrow> </msub> <mo>(</mo> <mi>z</mi> <mo>)</mo> </mrow> </semantics> </math>; and (<b>d</b>) <math display="inline"> <semantics> <mrow> <mrow> <mo>[</mo> <mrow> <msub> <mi>P</mi> <mi mathvariant="normal">N</mi> </msub> <msub> <mrow> <mo>(</mo> <mi>z</mi> <mo>)</mo> <mo>−</mo> <mi>P</mi> </mrow> <mi mathvariant="normal">T</mi> </msub> <mo>(</mo> <mi>z</mi> <mo>)</mo> </mrow> <mo>]</mo> </mrow> </mrow> </semantics> </math>. These data are calculated for polymer atoms in the interfacial regions of the confined PP/Fe<sub>2</sub>O<sub>3</sub> system at 458 K and 1 atm.</p>
Full article ">Figure 10
<p>The profile of the difference of normal <math display="inline"> <semantics> <mrow> <mo>(</mo> <msub> <mi>P</mi> <mi mathvariant="normal">N</mi> </msub> <mo>(</mo> <mi>z</mi> <mo>)</mo> <mo>)</mo> </mrow> </semantics> </math> and tangential pressures <math display="inline"> <semantics> <mrow> <mo>(</mo> <msub> <mi>P</mi> <mi mathvariant="normal">T</mi> </msub> <mo>(</mo> <mi>z</mi> <mo>)</mo> <mo>)</mo> </mrow> </semantics> </math> across the film thickness for the confined PP/Fe<sub>2</sub>O<sub>3</sub> system at 458 K and 1 atm. The surface tension is calculated from Equation (6) to be approximately equal to ~1180 mJ·m<sup>−2</sup>.</p>
Full article ">
1800 KiB  
Article
Structure–Property Studies on a New Family of Halogen Free Flame Retardants Based on Sulfenamide and Related Structures
by Teija Tirri, Melanie Aubert, Weronika Pawelec, Anton Holappa and Carl-Eric Wilén
Polymers 2016, 8(10), 360; https://doi.org/10.3390/polym8100360 - 14 Oct 2016
Cited by 20 | Viewed by 8752
Abstract
A wide variety of molecules containing S–N or S–N–S cores were synthesized, and their flame retardant properties in polypropylene (PP), low density polyethylene (LDPE) and polystyrene (PS) were investigated. In addition, polymers or oligomers bearing the sulfenamide functionality (SN) were also synthesized. It [...] Read more.
A wide variety of molecules containing S–N or S–N–S cores were synthesized, and their flame retardant properties in polypropylene (PP), low density polyethylene (LDPE) and polystyrene (PS) were investigated. In addition, polymers or oligomers bearing the sulfenamide functionality (SN) were also synthesized. It was shown that this radical generator family based on sulfenamides is very versatile in terms of structural modifications, and the thermal decomposition range can be easily adjusted by changing the R groups attached to the core. The thermal stabilities of the different sulfenamides were examined by thermogravimetric analysis (TGA). Radicals generated by the homolytic cleavage of the S–N or S–N–S bonds at an elevated temperature can effectively interact with the intermediate products of polymer thermolysis and provide excellent flame retardant properties. The choice of most suitable SN-structure varies depending on the polymer type. For polypropylene DIN 4102-1 B2 and UL94 VTM-2 classifications were achieved with only 0.5 to 1 wt % of sulfenamide, and, in some cases, no flaming dripping was observed. Also for LDPE thin films, sulfenamides offered the DIN 4102-1 B2 rating at low dosage. In the case of polystyrene, the very stringent UL94 V-0 classification was even achieved at a loading of 5 wt % of sulfenamide. Full article
(This article belongs to the Special Issue Recent Advances in Flame Retardancy of Textile Related Products)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Grouping of sulfenamides.</p>
Full article ">Figure 2
<p>General synthetic methods developed for generating sulfenamide derivatives.</p>
Full article ">Figure 3
<p>Collected thermogravimetric analysis (TGA) graphs of sulfenamides denoted Ic, IIc, IIIa, Vb, VIa and VIb. The optimal temperature range for flame retardant (FR) decomposition between polypropylene (PP) processing (230 °C) and ignition temperatures (250–360 °C) is marked with a grey border.</p>
Full article ">Figure 4
<p>Tentative structures for polymeric compounds IIIa and IIIb.</p>
Full article ">Figure 5
<p>Possible radicals generated by thermal decomposition of IVa.</p>
Full article ">Scheme 1
<p>Synthesis of bis(2,2,6,6-tetramethyl-1-(phenylthio)piperidin-4-yl) carbonate.</p>
Full article ">Scheme 2
<p>Substituent effect on thermal stability of sulfenamide compounds.</p>
Full article ">
4816 KiB  
Article
Enhancing the Compatibility, Hydrophilicity and Mechanical Properties of Polysulfone Ultrafiltration Membranes with Lignocellulose Nanofibrils
by Zhaodong Ding, Xuejiao Liu, Yang Liu and Liping Zhang
Polymers 2016, 8(10), 349; https://doi.org/10.3390/polym8100349 - 14 Oct 2016
Cited by 55 | Viewed by 7419
Abstract
Lignocellulose nanofibrils (LCN) and cellulose nanofibrils (CNF) are popular nanometer additives to improve mechanical properties and hydrophilic abilities; moreover, lignocellulose has potential as a natural adhesion promoter in fiber-reinforced composites. LCN and CNF were blended into polysulfone (PSF) to prepare ultrafiltration membranes via [...] Read more.
Lignocellulose nanofibrils (LCN) and cellulose nanofibrils (CNF) are popular nanometer additives to improve mechanical properties and hydrophilic abilities; moreover, lignocellulose has potential as a natural adhesion promoter in fiber-reinforced composites. LCN and CNF were blended into polysulfone (PSF) to prepare ultrafiltration membranes via the phase inversion method. These additives were characterized by Fourier transform infrared spectroscopy and transmission electron microscopy, and the rheological properties such as shear viscosity and non-Newtonian fluid index of the casting solutions were analyzed using a rotational rheometer. The performance of ultrafiltration membranes was characterized using Fourier transform infrared spectroscopy, thermogravimetric analysis and scanning electron microscopy. The pure water flux, bovine serum albumin retention ratio, water contact angle, surface energy, molecular weight cut-off, pore size and mechanical properties were measured. The equilibrium contact angle of water decreased from 63.5° on the PSF membrane to 42.1° on the CNF/PSF membrane and then decreased to 33.9° on the LCN/PSF membrane when the nanometer additives content was 0.8 wt %. The results reveal that LCN and CNF were successfully combined with PSF. Moreover, the combination of LCN/PSF ultrafiltration membranes was more promising than that of CNF/PSF ultrafiltration membranes. Full article
Show Figures

Figure 1

Figure 1
<p>The absorption promoter mechanism of lignin on cellulose adhesion to the membrane matrix.</p>
Full article ">Figure 2
<p>The possible membrane formation mechanism affected by the cellulose nanofibrils (CNF) and Lignocellulose nanofibrils (LCN).</p>
Full article ">Figure 3
<p>Transmission electron microscope images of CNF.</p>
Full article ">Figure 4
<p>Transmission electron microscope images of LCN.</p>
Full article ">Figure 5
<p>Scanning electron microscope of membranes structure.</p>
Full article ">Figure 6
<p>FTIR spectra of: (<b>a</b>) CNF; (<b>b</b>) LCN; (<b>c</b>) Sample M0 (PSF); (<b>d</b>) Sample M4 (CNF/PSF); and (<b>e</b>) Sample M10 (LCN/PSF).</p>
Full article ">Figure 7
<p>Schematic representation of the intermolecular interactions between the components in LCN/PSF ultrafiltration membranes (<b>*</b> denotes LCN, ~ denotes cellulose chains, and <b>—</b> denotes lignin chains).</p>
Full article ">Figure 8
<p>Thermal gravity analysis curves of CNF, LCN, Sample M0 (PSF), Sample M4 (CNF/PSF) and Sample M10 (LCN/PSF).</p>
Full article ">Figure 9
<p>Differential scanning calorimetry curves of CNF, LCN, Sample M0 (PSF), Sample M4 (CNF/PSF) and Sample M10 (LCN/PSF).</p>
Full article ">Figure 10
<p>Non-Newtonian fluid index of membrane solutions: Sample M0–12.</p>
Full article ">Figure 11
<p>Effect of CNF and LCN contents on contact angle and surface energy of membranes.</p>
Full article ">Figure 12
<p>Effects of the CNF and LCN content on the tensile strength and breaking elongation of the membranes.</p>
Full article ">Figure 13
<p>Pure water flux of membranes.</p>
Full article ">Figure 14
<p>Bovine serum albumin retention rejection ratio of membranes.</p>
Full article ">Figure 15
<p>Polyethylene glycol (PEG) retention rate as a function of molecular weight for Membranes: M0, M4, and M10.</p>
Full article ">
4101 KiB  
Article
Mapping the Mechanical Properties of Poly(3-hydroxybutyrate-co-3-hydroxyvalerate) Banded Spherulites by Nanoindentation
by Patricia Enrique-Jimenez, Juan F. Vega, Javier Martínez-Salazar, Fernando Ania and Araceli Flores
Polymers 2016, 8(10), 358; https://doi.org/10.3390/polym8100358 - 12 Oct 2016
Cited by 7 | Viewed by 6081
Abstract
Nanoindentation provides clear evidence that spherulite banding can be associated with a continuous modulation of mechanical properties from the more compliant peaks to the stiffer valleys. The structural arrangement in polymer-banded spherulites has intrigued scientists for many decades, and the debate has been [...] Read more.
Nanoindentation provides clear evidence that spherulite banding can be associated with a continuous modulation of mechanical properties from the more compliant peaks to the stiffer valleys. The structural arrangement in polymer-banded spherulites has intrigued scientists for many decades, and the debate has been recently intensified with the advent of new experimental evidence. The present paper approaches this issue by exploring the local mechanical properties of poly(3-hydroxybutyrate-co-3-hydroxyvalerate)-ringed spherulites via nanoindentation and discussing the confidence of the results. It was found that storage modulus and hardness across the banding morphology can be described as a sequence of regular oscillations with a periodicity that exactly matches the one observed using optical and atomic force microscopy. Results are consistent with the model of regular twisting of the lamellae, with flat-on arrangement in the low regions and edge-on lamellae in the crests. Full article
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Optical microscopy image of the banded morphology of P3HB-co-3HV after crystallization at 60 °C. Indentations of <span class="html-italic">h</span> ≈ 100 nm separated by 1 μm were produced along the distinct line. Circles identify two cracks appearing across the straight line, the blue one denoting the crack in the center of the spherulite.</p>
Full article ">Figure 2
<p>Storage modulus, <span class="html-italic">E</span>′, measured as a function of penetration depth, <span class="html-italic">h,</span> for the first six indentations of the scanning line of <a href="#polymers-08-00358-f001" class="html-fig">Figure 1</a>. Numbers indicate the distance (in µm) from each indent to the starting point.</p>
Full article ">Figure 3
<p>Plot of <span class="html-italic">E</span>′ (for <span class="html-italic">h</span> = 100 nm) as a function of the distance <span class="html-italic">d</span> to the starting point of the scanning line of <a href="#polymers-08-00358-f001" class="html-fig">Figure 1</a>. Drawn circles denote the location of cracks.</p>
Full article ">Figure 4
<p>(<b>a</b>) Optical micrograph of the area probed using an array of 21 × 21 indentations separated by 1 µm. The spherulite center is located at (0,0); (<b>b</b>) Mesh of indentation modulus values at specific <span class="html-italic">X</span> and <span class="html-italic">Y</span> positions. The color code appears on the right-hand side of the map; (<b>c</b>) <span class="html-italic">H</span> and (<b>d</b>) <span class="html-italic">E</span>′ contours, respectively, constructed by interpolating the mesh of indentation data. The color scale (in GPa) appears at the bottom of the respective plots.</p>
Full article ">Figure 5
<p>Central part: P3HB-co-3HV spherulites grown after crystallization at <span class="html-italic">T</span> = 65 °C. The images were taken using OM (top) and AFM (bottom). Enlargements of the two areas selected for analysis (20 × 20 μm<sup>2</sup>) are shown on the left- and right-hand sides, together with the <span class="html-italic">E</span>′ contours constructed by interpolating the mesh of indentation data (top) and the AFM height profiles (bottom) across the lines indicated in the enlarged AFM images. The <span class="html-italic">E</span>′ color code appearing next to the contour map on the left-hand side has also been used for the contour map on the right-hand side (units in GPa).</p>
Full article ">Figure 6
<p>(<b>a</b>) AFM image of an indentation produced on the surface of the P3HB-co-3HV spherulite of <a href="#polymers-08-00358-f005" class="html-fig">Figure 5</a>; (<b>b</b>) Profile along the blue line marked on (<b>a</b>).</p>
Full article ">Figure 7
<p>Front view: Graphical representation of a right circular conical indenter penetrating a normal (green solid line) and an oblique surface with <span class="html-italic">γ</span> = 5° (red solid line). Top view (rotated 90°): corresponding projected contact areas with the same color code. Cyan dotted lines represent the circular straight cross-section of the cone passing through the center O″ of the oblique red ellipse. Their intersection provides the semi-axis <span class="html-italic">a</span>. All vertical dotted lines are imaginary projection lines.</p>
Full article ">
2880 KiB  
Review
Recent Advances in the Design of Water Based-Flame Retardant Coatings for Polyester and Polyester-Cotton Blends
by Jenny Alongi, Federico Carosio and Paul Kiekens
Polymers 2016, 8(10), 357; https://doi.org/10.3390/polym8100357 - 11 Oct 2016
Cited by 48 | Viewed by 9269
Abstract
Over the last ten years a new trend of research activities regarding the flame retardancy of polymeric materials has arisen. Indeed, the continuous search for new flame retardant systems able to replace the traditional approaches has encouraged alternative solutions, mainly centred on nanotechnology. [...] Read more.
Over the last ten years a new trend of research activities regarding the flame retardancy of polymeric materials has arisen. Indeed, the continuous search for new flame retardant systems able to replace the traditional approaches has encouraged alternative solutions, mainly centred on nanotechnology. In this context, the deposition of nanostructured coatings on fabrics appears to be the most appealing and performance suitable approach. To this aim, different strategies can be exploited: from the deposition of a single monolayer consisting of inorganic nanoparticles (single-step adsorption) to the building-up of more complex architectures derived from layer by layer assembly (multi-step adsorption). The present paper aims to review the application of such systems in the field of polyester and polyester-cotton blend fabrics. The results collated by the authors are discussed and compared with those published in the literature on the basis of the different deposition methods adopted. A critical analysis of the advantages and disadvantages exhibited by these approaches is also presented. Full article
(This article belongs to the Special Issue Recent Advances in Flame Retardancy of Textile Related Products)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Schematic representation of single- and multi-step deposition techniques presented in this review.</p>
Full article ">Figure 2
<p>TTI values of nanoparticle (NP)-treated polyethylene terephthalate (PET) fabrics (<b>A</b>) and treated initially by plasma and then with CNa suspension (<b>B</b>) [<a href="#B33-polymers-08-00357" class="html-bibr">33</a>,<a href="#B35-polymers-08-00357" class="html-bibr">35</a>]. Data obtained by cone calorimetry at 35 kW/m<sup>2</sup>.</p>
Full article ">Figure 3
<p>FPI values of NP-treated PET fabrics (<b>A</b>) and treated initially by plasma and then with CNa suspension (<b>B</b>) [<a href="#B33-polymers-08-00357" class="html-bibr">33</a>,<a href="#B35-polymers-08-00357" class="html-bibr">35</a>]. Data obtained by cone calorimetry at 35 kW/m<sup>2</sup>.</p>
Full article ">Figure 4
<p>Heat Release Rate (HRR) curves of PET, COT, PET-COT_85:15 PET-COT_65:35 fabrics. Data obtained by cone calorimetry under 35 kW/m<sup>2</sup>.</p>
Full article ">Figure 5
<p>TTI and PHRR values of NP-treated PET-COT_85:15 (<b>A</b>,<b>B</b>, respectively) and NP-treated PET-COT_65:35 fabrics (<b>C</b>,<b>D</b>, respectively). Data obtained by cone calorimetry at 35 kW/m<sup>2</sup>.</p>
Full article ">Figure 6
<p>FPI values of NP-treated PET-COT_85:15 (<b>A</b>) and NP-treated PET-COT_65:35 fabrics (<b>B</b>). Data obtained by cone calorimetry at 35 kW/m<sup>2</sup>.</p>
Full article ">Figure 7
<p>TTI values (<b>A</b>) and HRR curves (<b>B</b>) of PET-COT_65:35 fabrics treated with different POSS amounts and a phosphorus-based FR. Data obtained by cone calorimetry at 35 kW/m<sup>2</sup>.</p>
Full article ">Figure 8
<p>TTI and PHRR values of 171 g/m<sup>2</sup> PET fabrics treated with 5, 10, and 20 BL of silica/silica nanoparticles deposited by dipping (<b>A</b>) [<a href="#B25-polymers-08-00357" class="html-bibr">25</a>]. Comparison between same LbL architectures deposited by dipping and spray on 490 g/m<sup>2</sup> PET (<b>B</b>) [<a href="#B26-polymers-08-00357" class="html-bibr">26</a>]. Data obtained by cone calorimetry at 35 kW/m<sup>2</sup>.</p>
Full article ">Figure 9
<p>FPI values of untreated and LbL-treated PET fabrics (<b>A</b>: ref. [<a href="#B25-polymers-08-00357" class="html-bibr">25</a>], <b>B</b>: [<a href="#B26-polymers-08-00357" class="html-bibr">26</a>] and <b>C</b>: [<a href="#B27-polymers-08-00357" class="html-bibr">27</a>]). Data obtained by cone calorimetry at 35 kW/m<sup>2</sup>.</p>
Full article ">Figure 10
<p>TTI and PHRR values of PET fabrics treated with 5 and 10 BL of ZrP coupled with PDAC, POSS or silica [<a href="#B25-polymers-08-00357" class="html-bibr">25</a>]. Data obtained by cone calorimetry under 35 kW/m<sup>2</sup>.</p>
Full article ">Figure 11
<p>TTI and PHRR values of PET fabrics treated with 1, 5 and 10 QL of char-former assemblies at 35 and 50 kW/m<sup>2</sup> (<b>A</b>,<b>B</b>, respectively) [<a href="#B29-polymers-08-00357" class="html-bibr">29</a>].</p>
Full article ">Figure 12
<p>TTI (<b>A</b>) and PHRR (<b>B</b>) values of PET-COT fabrics treated with 1, 5 and 10 QL at 25, 35, and 50 kW/m<sup>2</sup> [<a href="#B29-polymers-08-00357" class="html-bibr">29</a>].</p>
Full article ">Figure 13
<p>TTI and PHRR values of PET fabrics treated with 10 and 20 BL of Chi/APP or silica/APP assemblies at 35 kW/m<sup>2</sup> [<a href="#B30-polymers-08-00357" class="html-bibr">30</a>]. Data obtained by cone calorimetry at 35 kW/m<sup>2</sup>.</p>
Full article ">
3133 KiB  
Article
The Effect of Crystallinity on Compressive Properties of Al-PTFE
by Bin Feng, Xiang Fang, Huai-Xi Wang, Wen Dong and Yu-Chun Li
Polymers 2016, 8(10), 356; https://doi.org/10.3390/polym8100356 - 11 Oct 2016
Cited by 51 | Viewed by 9127
Abstract
Al-PTFE (Al-polytetrafluoroethene) is an important kind of Reactive Material (RM), however only limited importance was placed to the effect of crystallinity of PTFE on the mechanical and reactive behavior. This paper investigated the influence of crystallinity on the compression behavior of Al-PTFE at [...] Read more.
Al-PTFE (Al-polytetrafluoroethene) is an important kind of Reactive Material (RM), however only limited importance was placed to the effect of crystallinity of PTFE on the mechanical and reactive behavior. This paper investigated the influence of crystallinity on the compression behavior of Al-PTFE at strain rates range from 10?2 to 3 × 103 s?1. Two kinds of samples were prepared by different sintering procedures to acquire different crystallinity. The samples’ crystallinity was characterized by the density method and X-ray diffraction method. The samples were tested using an electro-hydraulic press for quasi-static loading, and split Hopkinson pressure bars (SHPBs) for high strain rates. Low crystalline samples have consistently higher strength and toughness than the high crystalline samples. The phenomenon was explained by an “elastic-plastic network” model combined with the effect of chain entanglement density. A bilinear dependence of true stress on log ? ? was observed, and Johnson-Cook models were fitted separately according to the different strain rate sensitivity. Finally, a close connection between fracture and initiation of Al-PTFE was confirmed in quasi-static tests, SHPB tests, and drop weight tests. It was hypothesized that the high temperature at the crack tips of PTFE is an important promoting factor of initiation. Full article
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>The sintering procedure of low and high crystalline Al-PTFE samples.</p>
Full article ">Figure 2
<p>Schematic illustration of the SHPB system.</p>
Full article ">Figure 3
<p>X-ray diffraction patterns of low and high crystalline Al-PTFE.</p>
Full article ">Figure 4
<p>Stress-strain curves of (<b>a</b>) low crystalline and (<b>b</b>) high crystalline Al-PTFE tested in compression at room temperature.</p>
Full article ">Figure 5
<p>One-wave versus two-wave analysis and strain rate of Al-PTFE (<b>a</b>) with pulse shaping and (<b>b</b>) without pulse shaping.</p>
Full article ">Figure 6
<p>Comparison of stress-strain curves between low crystalline and high crystalline Al-PTFE at (<b>a</b>) strain rate of 0.01 s<sup>−1</sup>; (<b>b</b>) strain rate of about 1000 s<sup>−1</sup>; and (<b>c</b>) strain rate of about 2300 s<sup>−1</sup>. The point where the reaction took place is marked.</p>
Full article ">Figure 7
<p>Comparison of true stress as a function of log (strain rate) between low crystalline and high crystalline Al-PTFE.</p>
Full article ">Figure 8
<p>Comparison of Johnson-Cook model to (<b>a</b>) low crystalline and (<b>b</b>) high crystalline Al-PTFE experimental data.</p>
Full article ">Figure 9
<p>Recovered Al-PTFE samples after compression. (<b>a</b>) High crystalline sample after quasi-static compression; (<b>b</b>) Low crystalline sample after quasi-static compression; (<b>c</b>) Low crystalline sample after SHPB tests; (<b>d</b>) High crystalline sample after drop weight tests.</p>
Full article ">
23981 KiB  
Article
Biphasic Polyurethane/Polylactide Sponges Doped with Nano-Hydroxyapatite (nHAp) Combined with Human Adipose-Derived Mesenchymal Stromal Stem Cells for Regenerative Medicine Applications
by Krzysztof Marycz, Monika Marędziak, Jakub Grzesiak, Anna Lis and Agnieszka Śmieszek
Polymers 2016, 8(10), 339; https://doi.org/10.3390/polym8100339 - 11 Oct 2016
Cited by 20 | Viewed by 7644
Abstract
Cartilage and bone tissue injuries are common targets in regenerative medicine. The degeneration of cartilage tissue results in tissue loss with a limited ability to regenerate. However, the application of mesenchymal stem cells in the course of such condition makes it possible to [...] Read more.
Cartilage and bone tissue injuries are common targets in regenerative medicine. The degeneration of cartilage tissue results in tissue loss with a limited ability to regenerate. However, the application of mesenchymal stem cells in the course of such condition makes it possible to manage this disorder by improving the structure of the remaining tissue and even stimulating its regeneration. Nevertheless, in the case of significant tissue loss, standard local injection of cell suspensions is insufficient, due to the low engraftment of transplanted cells. Introduction of mesenchymal stem cells on the surface of a compatible biomaterial can be a promising tool for inducing the regeneration by both retaining the cells at the desired site and filling the tissue gap. In order to obtain such a cell-biomaterial hybrid, we developed complex, biphasic polymer blend biomaterials composed of various polyurethane (PU)-to-polylactide (PLA) ratios, and doped with different concentrations of nano-hydroxyapatite (nHAp). We have determined the optimal blend composition and nano-hydroxyapatite concentration for adipose mesenchymal stem cells cultured on the biomaterial. We applied biological in vitro techniques, including cell viability assay, determination of oxidative stress factors level, osteogenic and chondrogenic differentiation potentials as well as cell proteomic analysis. We have shown that the optimal composition of biphasic scaffold was 20:80 of PU:PLA with 20% of nHAp for osteogenic differentiation, and 80:20 of PU:PLA with 10% of nHAp for chondrogenic differentiation, which suggest the optimal composition of final biphasic implant for regenerative medicine applications. Full article
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>SEM image of the surface and cross-section of TPU/PLA/nHAp films, scale bar = 200 µm.</p>
Full article ">Figure 2
<p>SEM images of the surfaces and cross-sections of TPU/PLA/nHAP sponges, magnification 200×, scale bar = 200 µm.</p>
Full article ">Figure 3
<p>Elemental mapping on the TPU/PLA/nHAP film surface: C (red), N (green), O (blue), Ca (cyan), and P (magenta), magnification 500×.</p>
Full article ">Figure 4
<p>Elemental mapping on the TPU/PLA/nHAP sponge surface: C (red), N (green), O (blue), Ca (cyan), and P (magenta), magnification 500×.</p>
Full article ">Figure 5
<p>Compressive stress—strain curve for TPU/PLA/nHAp nanocomposite sponges: G1—TPU80/PLA20/nHAp10, G2—TPU/PLA/nHAp20, G3—TPU20/PLA80/nHAp10, and G4—TPU20/PLA80/nHAp20.</p>
Full article ">Figure 6
<p>Representative TGA and DSC curves of TPU (<b>A</b>); PLA (<b>B</b>) and TPU/PLA 80/20 (<b>C</b>); TPU/PLA 20/80 (<b>D</b>) blends.</p>
Full article ">Figure 7
<p>The presence of nHAp particles in the 80/20 ((<b>A</b>) no nHAp added; (<b>B</b>) 10 wt % of nHAp added; (<b>C</b>) 20 wt % of nHAp added) and 20/80 ((<b>D</b>) no nHAp added; (<b>E</b>) 10 wt % of nHAp added; (<b>F</b>) 20 wt % of nHAp added) blends, as revealed by FIB milling and imaging at 2 kV using EsB<sup>®</sup> detector; colour images demonstrate the distribution of calcium (red) and phosphorus (green) in regions corresponding to SEM images; scale bars on each micrograph indicate 100,000× magnification.</p>
Full article ">Figure 7 Cont.
<p>The presence of nHAp particles in the 80/20 ((<b>A</b>) no nHAp added; (<b>B</b>) 10 wt % of nHAp added; (<b>C</b>) 20 wt % of nHAp added) and 20/80 ((<b>D</b>) no nHAp added; (<b>E</b>) 10 wt % of nHAp added; (<b>F</b>) 20 wt % of nHAp added) blends, as revealed by FIB milling and imaging at 2 kV using EsB<sup>®</sup> detector; colour images demonstrate the distribution of calcium (red) and phosphorus (green) in regions corresponding to SEM images; scale bars on each micrograph indicate 100,000× magnification.</p>
Full article ">Figure 8
<p>The histograms from flow cytometric analysis showing the presence of CD44 (<b>A</b>); CD73 (<b>B</b>); CD90 (<b>C</b>); CD105 (<b>D</b>); and the absence of CD34 (<b>E</b>); and CD45 (<b>F</b>).</p>
Full article ">Figure 9
<p>The results of the BrdU assay showing the differences in cell proliferation between experimental groups during the whole experiment ((<b>A</b>) chondrogenic culture; (<b>B</b>) osteogenic culture, ns—non-stimulated control, materials described in <a href="#polymers-08-00339-t003" class="html-table">Table 3</a>).</p>
Full article ">Figure 10
<p>Levels of superoxide dismutase (SOD), reactive oxygen species (ROS) and nitric oxide (NO) in cells cultured in chondrogenic (<b>A</b>) and osteogenic (<b>B</b>) conditions and in non-stimulated control conditions (ns) in all tested biomaterials (4, 6, 8, 9, described in <a href="#polymers-08-00339-t003" class="html-table">Table 3</a>); * <span class="html-italic">p</span> &lt; 0.05.</p>
Full article ">Figure 11
<p>Scanning electron micrographs presenting cells cultured on each biomaterial (4, 6, 8, 9—rows, described in <a href="#polymers-08-00339-t003" class="html-table">Table 3</a>) at different culture conditions (columns); mag. 5000×, scale bars indicated on micrographs.</p>
Full article ">Figure 12
<p>The results from SEM-EDX measurements of calcium and phosphorus concentrations deposited on each biomaterial during osteogenic differentiation (materials described in <a href="#polymers-08-00339-t003" class="html-table">Table 3</a>).</p>
Full article ">Figure 13
<p>The levels of analysed proteins in chondrogenic and standard (ns) conditions in each tested biomaterial; * <span class="html-italic">p</span> &lt; 0.05 (materials described in <a href="#polymers-08-00339-t003" class="html-table">Table 3</a>).</p>
Full article ">Figure 14
<p>The levels of analysed proteins in the conditioned culture media under osteogenic conditions and standard conditions (non-stimulated control, ns); * <span class="html-italic">p</span> &lt; 0.05, *** <span class="html-italic">p</span> &lt; 0.001 (materials described in <a href="#polymers-08-00339-t003" class="html-table">Table 3</a>).</p>
Full article ">Scheme 1
<p>Schematic illustration of the solvent casting method used for TPU/PLA/HAP nanocomposite fabrication destined for biological evaluation.</p>
Full article ">Scheme 2
<p>Schematic illustration of the solvent casting/salt leaching method used for porous TPU/PLA/HAP nanocomposite fabrication destined for physical evaluation.</p>
Full article ">Scheme 3
<p>Schematic illustration of the solvent casting/salt leaching method used for TPU/PLA/nHAp biphasic scaffold fabrication.</p>
Full article ">
6281 KiB  
Article
The Effect of Injection Molding Temperature on the Morphology and Mechanical Properties of PP/PET Blends and Microfibrillar Composites
by Maja Kuzmanović, Laurens Delva, Ludwig Cardon and Kim Ragaert
Polymers 2016, 8(10), 355; https://doi.org/10.3390/polym8100355 - 9 Oct 2016
Cited by 56 | Viewed by 11970
Abstract
Within this research the effect of injection molding temperature on polypropylene (PP)/poly(ethylene terephthalate) (PET) blends and microfibrillar composites was investigated. Injection molding blends (IMBs) and microfibrillar composites (MFCs) of PP/PET have been prepared in a weight ratio 70/30. The samples were processed at [...] Read more.
Within this research the effect of injection molding temperature on polypropylene (PP)/poly(ethylene terephthalate) (PET) blends and microfibrillar composites was investigated. Injection molding blends (IMBs) and microfibrillar composites (MFCs) of PP/PET have been prepared in a weight ratio 70/30. The samples were processed at three different injection molding temperatures (Tim) (210, 230, 280 °C) and subjected to extensive characterization. The observations from the fracture surfaces of MFCs showed that PET fibers can be achieved by three step processing. The results indicated that Tim has a big influence on morphology of IMBs and MFCs. With increasing the Tim, distinctive variations in particle and fiber diameters were noticed. The differences in mechanical performances were obtained by flexural and impact tests. Establishing relationships between the processing parameters, properties, and morphology of composites is of key importance for the valorization of MFC polymers. Full article
(This article belongs to the Special Issue Polymeric Fibers)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Scheme of MFC preparation [<a href="#B27-polymers-08-00355" class="html-bibr">27</a>,<a href="#B28-polymers-08-00355" class="html-bibr">28</a>].</p>
Full article ">Figure 2
<p>Processing scheme of: (<b>1</b>) IMBs (Injection molding blends) and (<b>2</b>) MFCs (Microfibrillar Composites).</p>
Full article ">Figure 3
<p>Dynamic (<b>a</b>) TG curves and (<b>b</b>) dTG of PP IM, PET IM, 70PP/30PET IMB, and 70PP/30PET MFC at 210 °C.</p>
Full article ">Figure 4
<p>DSC thermograms of PP IM, PET IM, 70PP/30PET IMB, and 70PP/30PET MFC during (<b>a</b>) heating; and (<b>b</b>) cooling.</p>
Full article ">Figure 5
<p>SEM micrographs of freeze-fracture surfaces under liquid nitrogen of the 70PP/30PET (<b>a</b>) extrusion blend; (<b>b</b>,<b>c</b>) stretched blend; (<b>d</b>) IMB at 210 °C; (<b>e</b>,<b>f</b>) MFC at 210 °C.</p>
Full article ">Figure 6
<p>SEM micrographs of freeze-fracture surface under liquid nitrogen 70PP/30PET IMB at (<b>a</b>) 210 °C; (<b>b</b>) 230 °C; and (<b>c</b>) 280 °C.</p>
Full article ">Figure 7
<p>SEM micrographs of freeze-fracture surfaces in the parallel direction under liquid nitrogen of 70PP/30PET MFC at 210 °C (<b>a</b>) low magnification (×450); and (<b>b</b>) high magnification (×1000).</p>
Full article ">Figure 8
<p>SEM micrographs of freeze-fracture surfaces in the parallel direction under liquid nitrogen of 70PP/30PET MFC at 230 °C (<b>a</b>) low magnification (×600); and (<b>b</b>) high magnification (×1000).</p>
Full article ">Figure 9
<p>SEM micrographs of freeze-fracture surfaces in the parallel direction under liquid nitrogen of 70PP/30PET MFC at 280 °C (<b>a</b>) low magnification (×500); and (<b>b</b>) high magnification (×1000).</p>
Full article ">Figure 10
<p>Comparison of flexural properties of PP IM, 70PP/30PET IMBs, and 70PP/30PET MFCs at three different <span class="html-italic">T</span><sub>im</sub> (<b>a</b>) flexural modulus; (<b>b</b>) flexural strength.</p>
Full article ">Figure 11
<p>Comparison of impact energy (kJ/mm) of PP IM, 70PP/30PET IMBs, and 70PP/30PET MFCs at three different <span class="html-italic">T</span><sub>im</sub>.</p>
Full article ">
3617 KiB  
Article
Low Density Wood-Based Particleboards Bonded with Foamable Sour Cassava Starch: Preliminary Studies
by Sandra Monteiro, Jorge Martins, Fernão D. Magalhães and Luísa Carvalho
Polymers 2016, 8(10), 354; https://doi.org/10.3390/polym8100354 - 8 Oct 2016
Cited by 30 | Viewed by 7345
Abstract
This work investigates the feasibility of producing low density particleboards using an adhesive system based on sour cassava starch, taking advantage of its adhesive and self-expansion properties. Relevant properties of the produced particleboards were evaluated according to European Standards including: density, internal bond, [...] Read more.
This work investigates the feasibility of producing low density particleboards using an adhesive system based on sour cassava starch, taking advantage of its adhesive and self-expansion properties. Relevant properties of the produced particleboards were evaluated according to European Standards including: density, internal bond, moisture content and thickness swelling. Low density particleboards were produced with densities between 207 kg/m3 and 407 kg/m3. The best performance corresponded to particleboard with a density of 318 kg/m3, an internal bond strength of 0.67 N/mm2, and a thickness swelling of 8.7%. These values meet the standard requirements of general purpose lightweight boards for use in dry conditions. Heat post-treatment (24 h at 80 °C) led to lower internal bond strength, due to retrogradation (recrystallization of amylose and amylopectin chains upon cooling) causing higher rigidity of the starch binder. However, it showed to have a significant effect on decreasing the thickness swelling. Full article
(This article belongs to the Special Issue Renewable Polymeric Adhesives)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Molecular structure of (<b>a</b>) amylose and (<b>b</b>) amylopectin.</p>
Full article ">Figure 2
<p>Expansion behavior of different types of cassava starches. (<b>a</b>,<b>b</b>) Native cassava starch before and after heating, respectively; (<b>c</b>,<b>d</b>) sour cassava starch before and after heating, respectively.</p>
Full article ">Figure 3
<p>FTIR spectra of native and sour cassava starch in the (4000–500 cm<sup>−1</sup>) spectral region.</p>
Full article ">Figure 4
<p>Particleboards produced with sour cassava starch–based binder. (<b>a</b>) Outside appearance; (<b>b</b>) close-up detail; (<b>c</b>) SEM image showing wood particles and surrounding foam, 100× magnification.</p>
Full article ">Figure 5
<p>Density of dry particleboards bonded with sour cassava starch foam. White circles: without HPT; black circles: with HPT. Dashed line shows coincidence between measured and expected densities.</p>
Full article ">Figure 6
<p>Detail of internal morphology of particleboards: (<b>a</b>) expected density of 313 kg/m<sup>3</sup>, showing uniform internal structure; (<b>b</b>) expected density of 550 kg/m<sup>3</sup>, showing internal delamination.</p>
Full article ">Figure 7
<p>Internal bond of particleboards bonded with sour cassava starch foam. White circles: Without HPT; black circles: With HPT.</p>
Full article ">Figure 8
<p>Thickness swelling of particleboards bonded with sour cassava starch foam. White circles: Without HPT; black circles: With HPT.</p>
Full article ">
1763 KiB  
Article
Dynamics of DNA Squeezed Inside a Nanochannel via a Sliding Gasket
by Aiqun Huang, Walter Reisner and Aniket Bhattacharya
Polymers 2016, 8(10), 352; https://doi.org/10.3390/polym8100352 - 29 Sep 2016
Cited by 10 | Viewed by 6211
Abstract
We use Brownian dynamics (BD) simulation of a coarse-grained (CG) bead-spring model of DNA to study the nonequilibrim dynamics of a single DNA molecule confined inside a rectangular nanochannel being squeezed with a sliding gasket piston or “nanodozer”. From our simulations we extract [...] Read more.
We use Brownian dynamics (BD) simulation of a coarse-grained (CG) bead-spring model of DNA to study the nonequilibrim dynamics of a single DNA molecule confined inside a rectangular nanochannel being squeezed with a sliding gasket piston or “nanodozer”. From our simulations we extract the nonequilibrim density profile c ( x , t ) of the squeezed molecule along the channel axis (x-coordinate) and then analyze the non-equilibrium profile using a recently introduced phenomenological Nonlinear Partial Differential Equation (NPDE) model. Since the NPDE approach also fits the experimental results well and is numerically efficient to implement, the combined BD + NPDE methods can be a powerful approach to analyze details of the confined molecular dynamics. In particular, the overall excellent agreement between the two complementary sets of data provides a strategy for carrying out large scale simulation on semi-flexible biopolymers in confinement at biologically relevant length scales. Full article
(This article belongs to the Special Issue Semiflexible Polymers)
Show Figures

Figure 1

Figure 1
<p>A bead-spring model of semi-flexible chain confined inside a nanochannel of width <span class="html-italic">D</span> being pushed by a sliding gasket piston (nano-dozer). The green beads are connected via anharmonic spring potentials and interact at long-range via excluded-volume. The red wall particles are at a fixed distance from each other on a square lattice and move together at the piston velocity. The chain always remains confined inside the channel.</p>
Full article ">Figure 2
<p>(<b>a</b>) The evolution of the maximum (green), minimum (red) and the <span class="html-italic">x</span>-coordinate of the center of mass (COM) (black) (along the channel axis) during the simulation are shown, the extension of the chain The piston is approached from the <math display="inline"> <semantics> <msub> <mi>x</mi> <mi>max</mi> </msub> </semantics> </math> side. When the COM’s speed becomes the same as <math display="inline"> <semantics> <msub> <mi>V</mi> <mi>push</mi> </msub> </semantics> </math>, the steady state of the polymer chain is achieved; (<b>b</b>) The same as in (<b>a</b>) but compares the effect of two different piston speeds 0.005 and 0.002 respectively.</p>
Full article ">Figure 3
<p>The steady state chain density <math display="inline"> <semantics> <mrow> <mi>c</mi> <mo>(</mo> <mi>x</mi> <mo>,</mo> <mi>t</mi> <mo>)</mo> </mrow> </semantics> </math> along the channel axis for (<b>a</b>) a piston velocity <math display="inline"> <semantics> <mrow> <msub> <mi>V</mi> <mi>push</mi> </msub> <mo>=</mo> <mn>0.05</mn> </mrow> </semantics> </math>; (<b>b</b>) <math display="inline"> <semantics> <mrow> <msub> <mi>V</mi> <mi>push</mi> </msub> <mo>=</mo> <mn>0.02</mn> </mrow> </semantics> </math>; (<b>c</b>) <math display="inline"> <semantics> <mrow> <msub> <mi>V</mi> <mi>push</mi> </msub> <mo>=</mo> <mn>0.01</mn> </mrow> </semantics> </math> and (<b>d</b>) <math display="inline"> <semantics> <mrow> <msub> <mi>V</mi> <mi>push</mi> </msub> <mo>=</mo> <mn>0.005</mn> </mrow> </semantics> </math>. (units of bond length per snapshot). The red lines are Brownian dynamics (BD) simulation output and the black lines represent the linear ramp steady-state profile predicted by the Nonlinear Partial Differential Equation (NPDE) model. Note that the linear ramp is convolved with a Gaussian function to represent the effect of thermal fluctuations that create an effective broadening of the profile shape. The extracted extension and ramp-slopes from the NPDE model fits (<b>a</b>–<b>d</b>) are shown in (<b>e</b>,<b>f</b>). The inset to (<b>e</b>) shows the same data on a log-log scale against a power law <math display="inline"> <semantics> <mrow> <mo>∼</mo> <msubsup> <mi>V</mi> <mrow> <mi>push</mi> </mrow> <mrow> <mo>−</mo> <mn>0</mn> <mo>.</mo> <mn>5</mn> </mrow> </msubsup> </mrow> </semantics> </math> (dashed-line). The bold line in (<b>f</b>) is a best linear fit showing that the extracted slopes are linearly proportional to the pushing speed.</p>
Full article ">Figure 4
<p>Time evolution of the normalized chain density <math display="inline"> <semantics> <mrow> <mi>c</mi> <mrow> <mo>(</mo> <mi>x</mi> <mo>,</mo> <mi>t</mi> <mo>)</mo> </mrow> <mo>/</mo> <msub> <mi>c</mi> <mn>0</mn> </msub> </mrow> </semantics> </math> along the channel axis for various times during compression with a sliding gasket moving at speed <math display="inline"> <semantics> <mrow> <msub> <mi>V</mi> <mi>push</mi> </msub> <mo>=</mo> <mn>0.05</mn> </mrow> </semantics> </math>. The channel width <math display="inline"> <semantics> <mrow> <mi>D</mi> <mo>=</mo> <mn>16</mn> </mrow> </semantics> </math> and the persistence length <math display="inline"> <semantics> <mrow> <msub> <mi>L</mi> <mi>p</mi> </msub> <mo>=</mo> <mn>2.5</mn> </mrow> </semantics> </math>. Time-values are shown in snapshot units, with one snapshot corresponding to 1000 iterations. The red circles correspond to the BD simulation data; the black solid lines correspond to the fitted prediction from the NPDE model. The NPDE model is solved with a <math display="inline"> <semantics> <mrow> <msub> <mi>D</mi> <mi>o</mi> </msub> <mo>=</mo> <mn>0.74</mn> </mrow> </semantics> </math> (bond unit squared per snapshot, obtained from the ramp-slope in steady-state); this <math display="inline"> <semantics> <msub> <mi>D</mi> <mi>o</mi> </msub> </semantics> </math> value leads to a <math display="inline"> <semantics> <mrow> <mi>τ</mi> <mo>=</mo> <mn>75,000</mn> </mrow> </semantics> </math> (snap-shot units). The best-fit <math display="inline"> <semantics> <mrow> <mi>β</mi> <mo>=</mo> <mn>0.07</mn> </mrow> </semantics> </math>. The <span class="html-italic">σ</span> values were determined from a fit of a uniform concentration profile model to the profile at <math display="inline"> <semantics> <mrow> <mi>t</mi> <mo>=</mo> <mn>0</mn> </mrow> </semantics> </math>. For the edge near the gasket, <math display="inline"> <semantics> <mrow> <mi>σ</mi> <mo>=</mo> <mn>0.008</mn> <msub> <mi>r</mi> <mi>o</mi> </msub> </mrow> </semantics> </math>. For the edge opposite the gasket, <math display="inline"> <semantics> <mrow> <mi>σ</mi> <mo>=</mo> <mn>0.05</mn> <msub> <mi>r</mi> <mi>o</mi> </msub> </mrow> </semantics> </math>.</p>
Full article ">Figure 5
<p>The corresponding snapshots of the simulated chain configuration for different <math display="inline"> <semantics> <mrow> <mi>c</mi> <mo>(</mo> <mi>x</mi> <mo>,</mo> <mi>t</mi> <mo>)</mo> </mrow> </semantics> </math> in <a href="#polymers-08-00352-f004" class="html-fig">Figure 4</a>.</p>
Full article ">Figure 6
<p>Time evolution of the normalized chain density <math display="inline"> <semantics> <mrow> <mi>c</mi> <mrow> <mo>(</mo> <mi>x</mi> <mo>,</mo> <mi>t</mi> <mo>)</mo> </mrow> <mo>/</mo> <msub> <mi>c</mi> <mn>0</mn> </msub> </mrow> </semantics> </math> along the channel axis during bead retraction. The channel width <math display="inline"> <semantics> <mrow> <mi>D</mi> <mo>=</mo> <mn>16</mn> </mrow> </semantics> </math> and the persistence length <math display="inline"> <semantics> <mrow> <msub> <mi>L</mi> <mi>p</mi> </msub> <mo>=</mo> <mn>2.5</mn> </mrow> </semantics> </math>. The chain profile is compressed by moving the gasket at a sliding speed <math display="inline"> <semantics> <mrow> <msub> <mi>V</mi> <mi>push</mi> </msub> <mo>=</mo> <mn>0.05</mn> </mrow> </semantics> </math>; the bead is then retracted at speed <math display="inline"> <semantics> <mrow> <msub> <mi>V</mi> <mi>retract</mi> </msub> <mo>=</mo> <mn>4</mn> <msub> <mi>V</mi> <mi>push</mi> </msub> </mrow> </semantics> </math>, inducing relaxation of the profile. Time-values are shown in snapshot units, with one snapshot corresponding to 1000 iterations. The red circles correspond to the BD simulation data; the black solid lines correspond to the fitted prediction from the NPDE model. The dashed blue curves for <math display="inline"> <semantics> <mrow> <mi>t</mi> <mo>&gt;</mo> <mn>400</mn> </mrow> </semantics> </math> correspond to fits to a parabolic concentration model. The NPDE model is solved with a <math display="inline"> <semantics> <mrow> <msub> <mi>D</mi> <mi>o</mi> </msub> <mo>=</mo> <mn>0.74</mn> </mrow> </semantics> </math> (obtained from the ramp-slope in steady-state); this <math display="inline"> <semantics> <msub> <mi>D</mi> <mi>o</mi> </msub> </semantics> </math> value leads to a <math display="inline"> <semantics> <mrow> <mi>τ</mi> <mo>=</mo> </mrow> </semantics> </math> 75,000. The best-fit <math display="inline"> <semantics> <mrow> <mi>β</mi> <mo>=</mo> <mn>0.26</mn> </mrow> </semantics> </math>. The value of <math display="inline"> <semantics> <mrow> <mi>σ</mi> <mo>=</mo> <mn>0.013</mn> <msub> <mi>r</mi> <mi>o</mi> </msub> </mrow> </semantics> </math>, determined from a fit of a broadened ramp profile model to the profile at <math display="inline"> <semantics> <mrow> <mi>t</mi> <mo>=</mo> <mn>0</mn> </mrow> </semantics> </math>.</p>
Full article ">Figure 7
<p>The chain extension and maximum concentration for a dynamic compression (<b>a</b>,<b>b</b>) and retraction (relaxation) process (<b>c</b>,<b>d</b>). The red line corresponds to BD results; the black curve corresponds to NPDE model output corresponding to the profile fits shown in <a href="#polymers-08-00352-f004" class="html-fig">Figure 4</a> and <a href="#polymers-08-00352-f006" class="html-fig">Figure 6</a>. The maximum profile concentration for the BD output for the transient compression process is obtained by taking a three-point running average of the simulation data to suppress concentration fluctuations at the peak position. The maximum profile concentration for the BD output for the retraction process is obtained by performing a fit of the concentration profile to a parabolic concentration model. The approach minimizes the influence of thermal fluctuations on the concentration maximum as the profile approaches equilibrium.</p>
Full article ">Figure 8
<p>The red circles are results of coarse-graining BD-simulations for the retraction profile. The bold black curve is the NPDE model output with the degree of extensional fluctuations determined from the initial profile (<math display="inline"> <semantics> <mrow> <mi>σ</mi> <mo>=</mo> <mn>0.013</mn> <msub> <mi>r</mi> <mi>o</mi> </msub> </mrow> </semantics> </math>); the dashed bold curve is the NPDE model output with the degree of extensional fluctuations determined by fits to the equilibrium profile (<math display="inline"> <semantics> <mrow> <mi>σ</mi> <mo>=</mo> <mn>0.06</mn> <msub> <mi>r</mi> <mi>o</mi> </msub> </mrow> </semantics> </math>). The degree of thermal broadening clearly increases at longer times as the profile approaches equilibrium.</p>
Full article ">
434 KiB  
Article
Microstructure of Sheared Entangled Solutions of Semiflexible Polymers
by Marc Lämmel, Evelin Jaschinski, Rudolf Merkel and Klaus Kroy
Polymers 2016, 8(10), 353; https://doi.org/10.3390/polym8100353 - 28 Sep 2016
Cited by 3 | Viewed by 5987
Abstract
We study the influence of finite shear deformations on the microstructure and rheology of solutions of entangled semiflexible polymers theoretically and by numerical simulations and experiments with filamentous actin. Based on the tube model of semiflexible polymers, we predict that large finite shear [...] Read more.
We study the influence of finite shear deformations on the microstructure and rheology of solutions of entangled semiflexible polymers theoretically and by numerical simulations and experiments with filamentous actin. Based on the tube model of semiflexible polymers, we predict that large finite shear deformations strongly affect the average tube width and curvature, thereby exciting considerable restoring stresses. In contrast, the associated shear alignment is moderate, with little impact on the average tube parameters, and thus expected to be long-lived and detectable after cessation of shear. Similarly, topologically preserved hairpin configurations are predicted to leave a long-lived fingerprint in the shape of the distributions of tube widths and curvatures. Our numerical and experimental data support the theory. Full article
(This article belongs to the Special Issue Semiflexible Polymers)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Shear alignment of tube segments. (<b>a</b>) Strain-dependence of the nematic order parameter <math display="inline"> <semantics> <mrow> <mi>S</mi> <mo stretchy="false">(</mo> <mi>γ</mi> <mo stretchy="false">)</mo> </mrow> </semantics> </math>: affine scaling, as obtained for two- and three-dimensional solutions of phantom rods (<a href="#sec4dot4-polymers-08-00353" class="html-sec">Section 4.4</a>), and the numerical estimate from the unit-cell model [<a href="#B21-polymers-08-00353" class="html-bibr">21</a>] (see <a href="#sec4dot5-polymers-08-00353" class="html-sec">Section 4.5</a>). Up to strains of order one, the results are well captured by the linear asymptotic scaling of Equation (<a href="#FD3-polymers-08-00353" class="html-disp-formula">3</a>), while <math display="inline"> <semantics> <mrow> <mi>S</mi> <mo stretchy="false">(</mo> <mi>γ</mi> <mo stretchy="false">)</mo> </mrow> </semantics> </math> flattens out for larger strains, implying that perfect shear alignment is hard to achieve, even if quite substantial strains are imposed; (<b>b</b>) The angular distribution of the two-dimensional phantom-rod solution, according to Equation (<a href="#FD19-polymers-08-00353" class="html-disp-formula">19</a>). With increasing strain the bimodal structure becomes more pronounced.</p>
Full article ">Figure 2
<p>How shear affects packing structure in the unit-cell model [<a href="#B21-polymers-08-00353" class="html-bibr">21</a>]. In contrast to the most probable tube conformations, rare hairpin configurations are buckled and pulled tighter by increasing shear (as sketched in the insets). They are responsible for the tails emerging upon increasing strain <span class="html-italic">γ</span> in the concentration-independent master curves of the reduced probability distribution functions (<b>a</b>) <math display="inline"> <semantics> <mrow> <msub> <mi>p</mi> <mi>γ</mi> </msub> <mrow> <mo stretchy="false">(</mo> <mi>r</mi> <mo stretchy="false">)</mo> </mrow> <mo>≡</mo> <mover> <mi mathvariant="script">R</mi> <mo stretchy="true">¯</mo> </mover> <mrow> <mo stretchy="false">(</mo> <mi>γ</mi> <mo stretchy="false">)</mo> </mrow> <mi>P</mi> <mrow> <mo stretchy="false">[</mo> <mi>r</mi> <mover> <mi mathvariant="script">R</mi> <mo stretchy="true">¯</mo> </mover> <mrow> <mo stretchy="false">(</mo> <mi>γ</mi> <mo stretchy="false">)</mo> </mrow> <mo stretchy="false">]</mo> </mrow> </mrow> </semantics> </math> for the tube width and (<b>b</b>) <math display="inline"> <semantics> <mrow> <msub> <mi>p</mi> <mi>γ</mi> </msub> <mrow> <mo stretchy="false">(</mo> <mi>c</mi> <mo stretchy="false">)</mo> </mrow> <mo>≡</mo> <mover> <mi mathvariant="script">C</mi> <mo stretchy="true">¯</mo> </mover> <mrow> <mo stretchy="false">(</mo> <mi>γ</mi> <mo stretchy="false">)</mo> </mrow> <msub> <mi>P</mi> <mi>γ</mi> </msub> <mrow> <mo stretchy="false">[</mo> <mi>c</mi> <mover> <mi mathvariant="script">C</mi> <mo stretchy="true">¯</mo> </mover> <mrow> <mo stretchy="false">(</mo> <mi>γ</mi> <mo stretchy="false">)</mo> </mrow> <mo stretchy="false">]</mo> </mrow> </mrow> </semantics> </math> for the tube curvature.</p>
Full article ">Figure 3
<p>Nematic alignment and tube deformation. (<b>a</b>) Dependence of the mean tube radius <math display="inline"> <semantics> <mover> <mi>R</mi> <mo stretchy="true">¯</mo> </mover> </semantics> </math> on the nematic order as predicted by the binary-collision approximation (BCA) calculation, Equation (<a href="#FD2-polymers-08-00353" class="html-disp-formula">2</a>), and the unit-cell model. The four experimental data points correspond to four different F-actin concentrations <span class="html-italic">c</span>. Our Monte-Carlo/Brownian-Dynamics (MC/BD) simulations of pre-aligned polymer solutions and F-actin experiments show no sign of the strong strain-induced tube dilation predicted by the unit-cell model but agree with the BCA predictions for moderately pre-aligned tubes, corresponding to shear alignment by a strain of about <math display="inline"> <semantics> <mrow> <mi>γ</mi> <mo>=</mo> <mn>1</mn> <mo>.</mo> <mn>5</mn> <mo>⋯</mo> <mn>2</mn> <mo>.</mo> <mn>5</mn> </mrow> </semantics> </math>. We interpret this as an indication that the average tube deformations had mostly relaxed between the cessation of shear and the start of the measurements, while the inflicted shear alignment was largely conserved. Note that the statistical errors of the tube size is very small (≈ 1%) for both the experiments and the simulations; (<b>b</b>) Polymer solutions were prepared in two different sample geometries for each <span class="html-italic">c</span>, a narrow capillary and a wider micro chamber, to get strongly sheared networks and weakly sheared reference samples, yielding values for <math display="inline"> <semantics> <mrow> <mover> <mi>R</mi> <mo stretchy="true">¯</mo> </mover> <mrow> <mo stretchy="false">(</mo> <mi>S</mi> <mo stretchy="false">)</mo> </mrow> </mrow> </semantics> </math> and <math display="inline"> <semantics> <mrow> <mover> <mi>R</mi> <mo stretchy="true">¯</mo> </mover> <mrow> <mo stretchy="false">(</mo> <mi>S</mi> <mo>≈</mo> <mn>0</mn> <mo stretchy="false">)</mo> </mrow> </mrow> </semantics> </math>, respectively. Their ratio is shown in panel (<b>a</b>) against the values for <span class="html-italic">S</span> in the capillary.</p>
Full article ">Figure 4
<p>Reduced tube-width distribution: differently prepared F-actin experiments collapse onto a single master curve <math display="inline"> <semantics> <mrow> <mi>p</mi> <mrow> <mo stretchy="false">(</mo> <mi>r</mi> <mo stretchy="false">)</mo> </mrow> <mo>=</mo> <mover> <mi>R</mi> <mo stretchy="true">¯</mo> </mover> <mi>P</mi> <mrow> <mo stretchy="false">(</mo> <mi>r</mi> <mover> <mi>R</mi> <mo stretchy="true">¯</mo> </mover> <mo stretchy="false">)</mo> </mrow> </mrow> </semantics> </math>, independent of both concentration and the degree of nematic order of the solution. The scaling and the shape of the equilibrium master curve, Equation (<a href="#FD12-polymers-08-00353" class="html-disp-formula">12</a>), are predicted by the tube model, evaluated in the binary-collision approximation (BCA). Its deformation due to shearing is estimated using the unit-cell model. Small deviations between the data and the equilibrium theory are consistent with the predicted effect of a remnant strain <math display="inline"> <semantics> <mrow> <mi>γ</mi> <mo>=</mo> <mn>1</mn> <mo>.</mo> <mn>5</mn> </mrow> </semantics> </math> (dashed lines) and interpreted as indicative of long-lived deformations of rare hairpin configurations.</p>
Full article ">Figure 5
<p>Reduced tube-width distribution obtained from the hybrid Monte-Carlo/Brownian-dynamics computer simulations [<a href="#B51-polymers-08-00353" class="html-bibr">51</a>,<a href="#B52-polymers-08-00353" class="html-bibr">52</a>,<a href="#B53-polymers-08-00353" class="html-bibr">53</a>]. As expected from the BCA prediction, data for various polymer length concentrations <span class="html-italic">ρ</span> collapse onto a single master curve.</p>
Full article ">Figure 6
<p>Unit-cell model by Fernández et al. [<a href="#B21-polymers-08-00353" class="html-bibr">21</a>]. (<b>a</b>) The test tube is deformed by two confining tubes (Sketch adapted from Reference [<a href="#B21-polymers-08-00353" class="html-bibr">21</a>]); (<b>b</b>) The zero-strain values of the average tube radius <math display="inline"> <semantics> <mrow> <mover> <mi mathvariant="script">R</mi> <mo stretchy="true">¯</mo> </mover> <mrow> <mo stretchy="false">(</mo> <mi>γ</mi> <mo>=</mo> <mn>0</mn> <mo stretchy="false">)</mo> </mrow> </mrow> </semantics> </math> and the mean curvature <math display="inline"> <semantics> <mrow> <mover> <mi mathvariant="script">C</mi> <mo stretchy="true">¯</mo> </mover> <mrow> <mo stretchy="false">(</mo> <mi>γ</mi> <mo>=</mo> <mn>0</mn> <mo stretchy="false">)</mo> </mrow> </mrow> </semantics> </math> varies with the unit-cell conformation, which is characterized by the deflection <math display="inline"> <semantics> <msub> <mi>x</mi> <mrow> <mi mathvariant="normal">c</mi> <mn>0</mn> </mrow> </msub> </semantics> </math>. Shearing of the network is mimicked by an affine displacement of the contact points with (or centers of) the confining tubes. There is a trade-off between bending and confinement, since a more strongly bent conformation allows for a wider tube, which, on average, gives rise to a strain-induced tube dilation and bending, quantified by (<b>c</b>) the average tube radius <math display="inline"> <semantics> <mrow> <mover> <mi mathvariant="script">R</mi> <mo stretchy="true">¯</mo> </mover> <mrow> <mo stretchy="false">(</mo> <mi>γ</mi> <mo stretchy="false">)</mo> </mrow> </mrow> </semantics> </math> and (<b>d</b>) the mean curvature <math display="inline"> <semantics> <mrow> <mover> <mi mathvariant="script">C</mi> <mo stretchy="true">¯</mo> </mover> <mrow> <mo stretchy="false">(</mo> <mi>γ</mi> <mo stretchy="false">)</mo> </mrow> </mrow> </semantics> </math> with strain <span class="html-italic">γ</span>; (<b>e</b>) The total free energy <math display="inline"> <semantics> <mrow> <mi mathvariant="script">F</mi> <mo stretchy="false">(</mo> <mi>γ</mi> <mo stretchy="false">)</mo> </mrow> </semantics> </math> increases upon shearing as required by mechanical stability. All curves were computed numerically from the full non-linear theory.</p>
Full article ">
5104 KiB  
Article
Study of Non-Isothermal Crystallization of Polydioxanone and Analysis of Morphological Changes Occurring during Heating and Cooling Processes
by Yolanda Márquez, Lourdes Franco, Pau Turon, Juan Carlos Martínez and Jordi Puiggalí
Polymers 2016, 8(10), 351; https://doi.org/10.3390/polym8100351 - 28 Sep 2016
Cited by 19 | Viewed by 8220
Abstract
Non-isothermal crystallization kinetics of polydioxanone (PDO), a polymer with well-established applications as bioabsorbable monofilar suture, was investigated by Avrami, Mo, and isoconversional methodologies. Results showed Avrami exponents appearing in a relatively narrow range (i.e., between 3.76 and 2.77), which suggested a three-dimensional spherulitic [...] Read more.
Non-isothermal crystallization kinetics of polydioxanone (PDO), a polymer with well-established applications as bioabsorbable monofilar suture, was investigated by Avrami, Mo, and isoconversional methodologies. Results showed Avrami exponents appearing in a relatively narrow range (i.e., between 3.76 and 2.77), which suggested a three-dimensional spherulitic growth and instantaneous nucleation at high cooling rates. The nucleation mechanism changed to sporadic at low rates, with both crystallization processes being detected in the differential scanning calorimetry (DSC) cooling traces. Formation of crystals was hindered as the material crystallized because of a decrease in the motion of molecular chains. Two secondary nucleation constants were derived from calorimetric data by applying the methodology proposed by Vyazovkin and Sbirrazzuoli through the estimation of effective activation energies. In fact, typical non-isothermal crystallization analysis based on the determination of crystal growth by optical microscopy allowed secondary nucleation constants of 3.07 × 105 K2 and 1.42 × 105 K2 to be estimated. Microstructure of sutures was characterized by a stacking of lamellae perpendicularly oriented to the fiber axis and the presence of interlamellar and interfibrillar amorphous regions. The latter became enhanced during heating treatments due to loss of partial chain orientation and decrease of electronic density. Degradation under various pH media revealed different macroscopic morphologies and even a distinct evolution of lamellar microstructure during subsequent heating treatments. Full article
(This article belongs to the Special Issue Biodegradable Polymers)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Differential scanning calorimetry (DSC) traces corresponding to heating runs of commercial granulated polydioxanone (PDO) (<b>a</b>) and PDO sutures (<b>d</b>), the cooling run of the melted granulated PDO (<b>b</b>) and the subsequent heating run (<b>c</b>). Glass transition can be detected in the magnification given in the inset in (<b>c</b>). All scans were performed at a rate of 3 °C/min.</p>
Full article ">Figure 2
<p>Exothermic DSC traces performed with PDO at the indicated cooling rates. The dashed ellipse contains the high temperature crystallization peak detected at high cooling rates, whereas the dashed arrow indicates the evolution of the main crystallization peak.</p>
Full article ">Figure 3
<p>(<b>a</b>) Time evolution of relative crystallinity at the indicated cooling rates for non-isothermal crystallization of PDO; (<b>b</b>) Avrami analyses of non-isothermal crystallizations of PDO.</p>
Full article ">Figure 4
<p>Plots of log (<span class="html-italic">φ</span>) versus log (<span class="html-italic">t</span> − <span class="html-italic">t</span><sub>0</sub>) for non-isothermal crystallization of PDO performed at the indicated crystallinities.</p>
Full article ">Figure 5
<p>(<b>a</b>) Plots of ln[d<span class="html-italic">χ</span>/dt]<span class="html-italic"><sub>χ</sub></span> versus 1/<span class="html-italic">T</span> for non-isothermal crystallization of PDO at the indicated cooling rates. Data corresponding to relative degrees of crystallinity of 0.8, 0.5 and 0.1 are represented by blue, green and red symbols, respectively; (<b>b</b>) Dependence of the activation energy of crystallization (●) and average temperature (○) on crystallinity; (<b>c</b>) Experimental <span class="html-italic">E</span><span class="html-italic"><sub>χ</sub></span> versus <span class="html-italic">T</span> plot and simulated curves according to Equation (6). Red and violet dashed lines indicate the simulated curves for regimes III and II, respectively. Arrows indicate the expected temperatures for the maximum crystallization rates (i.e., effective activation energy equal to zero).</p>
Full article ">Figure 6
<p>Optical micrograph of PDO spherulites formed during a non-isothermal crystallization from the melt state performed at a cooling rate of 20 °C/min. Yellow arrows point to spherulites formed at low temperatures. Inset shows a micrograph taken with a first-order red tint plate to determine the birefringence sign.</p>
Full article ">Figure 7
<p>(<b>a</b>) Variation in spherulite radius with temperature during heating at the indicated rates; (<b>b</b>) Spherulitic growth rates determined by the equations deduced for the heating runs. Theoretical curves are also drawn (dashed lines) for comparative purposes; (<b>c</b>) Plot of ln<span class="html-italic">G</span> + <span class="html-italic">U</span>*/<span class="html-italic">R</span>(<span class="html-italic">T</span><sub>c</sub> − <span class="html-italic">T</span><sub>∞</sub>) versus 1/<span class="html-italic">T</span><sub>c</sub>(Δ<span class="html-italic">T</span>)<span class="html-italic">f</span> to determine the <span class="html-italic">K</span><sub>g</sub> secondary nucleation parameters of PDO.</p>
Full article ">Figure 8
<p>Dependence of effective activation energy on crystallization temperature for regimes II (<sup>■</sup>) and III (•). Extrapolated data for regimes II and III are indicated by dotted and dashed lines, respectively.</p>
Full article ">Figure 9
<p>Variation of intensity (<span class="html-italic">Iq</span><sup>2</sup>) (full symbols) and scattering vector (<span class="html-italic">q</span>) (empty symbols) of SAXS (small-angle X-ray scattering) peaks observed in the diffraction profiles taken during heating (10 °C/min) at room temperature (red) and during cooling (2 °C/min) from the melt state (blue).</p>
Full article ">Figure 10
<p>(<b>a</b>) SAXS patterns of a granulated PDO sample taken at 25 and 102 °C during a heating run performed at 10 °C/min; (<b>b</b>) Change in the correlation function during the heating run. For the sake of completeness the pattern and correlation function obtained at room temperature after cooling (10 °C/min) a previously molten sample are also shown.</p>
Full article ">Figure 11
<p>(<b>a</b>) SAXS patterns of a PDO suture taken at representative temperatures during a heating run at 10 °C/min. Blue and red arrows indicate meridional and equatorial reflections, respectively; (<b>b</b>) Correlation function of diffraction patterns corresponding to: the initial suture, a suture heated (10 °C/min) just before melting and a melt crystallized (cooling rate of 10 °C/min) suture at room temperature.</p>
Full article ">Figure 12
<p>Correlation functions of patterns obtained at the indicated temperatures during the cooling run (2 °C/min) from the melt state. The correlation function of the pattern obtained at room temperature after cooling at 10 °C/min is also shown for comparative purposes.</p>
Full article ">Figure 13
<p>SAXS patterns taken at representative temperatures of 25 °C (<b>a</b>); 102 °C (<b>b</b>) and 107 °C (<b>c</b>) during a heating run at 10 °C/min of a PDO suture previously degraded in a pH 11 hydrolytic medium for 36 days. The pattern obtained at room temperature after cooling (10 °C/min) and the optical micrograph of the degraded suture are shown in (<b>d</b>,<b>e</b>), respectively.</p>
Full article ">Figure 14
<p>SAXS patterns taken at representative temperatures of 25 °C (<b>a</b>); 102 °C (<b>b</b>) and 112 °C (<b>c</b>) during a heating run at 10 °C/min of a PDO suture previously degraded in a pH 7 hydrolytic medium for 36 days. The pattern obtained at room temperature after cooling (10 °C/min) and the optical micrograph of the degraded suture are shown in (<b>d</b>,<b>e</b>), respectively.</p>
Full article ">
Previous Issue
Next Issue
Back to TopTop