text:
\section{Introduction}

The description of the properties of glass-forming liquids poses numerous conceptual and technical problems.~\cite{JCPReview1, JCPReview2} The properties of supercooled liquids obviously vary strongly with thermodynamic state, which for a one-component system corresponds to systems with specified temperature $T$ and pressure $P$ (convenient when cooling at constant pressure) or specified temperature $T$ and density $\rho$ (convenient when cooling at constant volume). Since separate variations in density $\rho$ or temperature $T$ greatly affect the dramatic slowing down of dynamics of glassy materials, the observation that dynamical properties, such as the viscosity $\eta$, the structural relaxation time $\tau$, and the diffusion constant $D$, depend only on a single control parameter, $\rho^\gamma/T$, where $\gamma$ depends on the material, is a quite remarkable finding that is important in guiding the design of new materials. Moreover, an explanation of the origins of this thermodynamic scaling is then crucial for deepening our understanding of universal characteristics of glass formation.~\cite{Tolle0, Roland0, Floudas0, RolandMacro2010}The exponent $\gamma$ of the thermodynamic scaling also provides a measure of the relative importance of the density and temperature in controlling glassy dynamics. Hence, not surprisingly, a large body of experiments~\cite{DreyfusPRE2003, RolandPRE2004, Tarjus1, Tarjus2, RolandJCP2005, RolandPRE2005, RolandJCP2006} and simulations~\cite{CoslovichJPCB2008, CoslovichJNCS2011, CoslovichJCP2009, NgaiJPCB2010, BerthierPRL2009, BerthierJCP2011, PedersenPRL2010} have probed the nature of thermodynamic scaling of glass-forming liquids since the first observation by T\"{o}lle \textit{et al.} for \textit{ortho}-terphenyl.~\cite{Tolle1} The existence of thermodynamic scaling is well established for as diverse materials as van der Waals liquids, polymers, ionic liquids, weakly hydrogen-bonded systems, etc.~\cite{Roland0, Floudas0, RolandMacro2010}

Thermodynamic scaling in glass-forming liquids is intriguing for both fundamental and practical reasons. Probing the origin of thermodynamic scaling assists attempts to establish a universal description of the dynamics of glassy materials and to improve significantly the existing models and theories. The study is also valuable since the dynamical properties at varying thermodynamic conditions can be predicted from only a few measurements if the material conforms to the thermodynamic scaling. While some have argued that thermodynamic scaling contains little physical content,~\cite{Tarjus1, Tarjus2} the opposite wide belief is that thermodynamic scaling stems from the nature of the repulsive portion of the intermolecular potential. In fact, the thermodynamic scaling exactly holds for a system interacting with an inverse power law (IPL) potential where $\gamma$ is indeed determined by the exponent of the power law.~\cite{IPL} Strong support for this interpretation emerges from computer simulations using generalized Lennard-Jones (LJ) potentials with varying steepness~\cite{CoslovichJPCB2008, CoslovichJNCS2011} that exhibit $\gamma$ as increasing with the steepness of the potential. The study of thermodynamic scaling has  triggered the proposal of several novel concepts by Dyre and coworkers, such as that of ``strongly correlating liquids'' (i.e., liquids with strong correlations between  equilibrium fluctuations of the potential energy and the virial in a canonical ensemble) and ``isomorphs'' (i.e., curves in the phase diagram along which structure, dynamics, and some thermodynamic properties are invariant in reduced units) .~\cite{Dyre1, Dyre2, Dyre3, Dyre4, Dyre5, Dyre6} The isomorph theory indicates that the scaling exponent $\gamma$ is not constant, but depends on density,~\cite{Dyre5, Dyre6, Dyre7, Dyre8} and the power-law form $\rho^\gamma$ is only a special case. However, the power-law density scaling is a useful approximation to the isomorph scaling since a number of experiments find  a weak dependence of $\gamma$ on density under certain thermodynamic conditions~\cite{Roland0, Floudas0, RolandMacro2010} and since using a constant value of $\gamma$ leads to collapse onto a master curve of the dynamics in glass-forming liquids. Furthermore, the Avramov model, which is frequently employed in describing viscosity and relaxation data of glass-forming liquids in the $T$-$P$ plane,~\cite{Avramov} has been explored by Casalini \textit{et al.}~\cite{RolandAvramov} to rationalize the thermodynamic scaling and to show that the scaling exponent $\gamma$ is related to the Gr\"{u}neisen constant. In addition, Floudas \textit{et al.}~\cite{FloudasJCP2006} note that the monomer volume and local packing play an important role in understanding the thermodynamic scaling of polymers. Recently,  Ngai \textit{et al.}~\cite{NgaiJCP2012} present evidence that thermodynamic scaling of the $\alpha$-relaxation time stems from the properties of the Johari-Goldstein $\beta$-relaxation or the primitive relaxation of the coupling model.

Despite intense recent efforts, understanding of the origins of thermodynamic scaling in glass-forming liquids is far from complete, and, in particular, an explanation of how molecular details of the polymers affect the thermodynamic scaling remains elusive. Although the thermodynamic scaling is a universal property that is common to both small molecules and polymers, a better understanding of its origins benefits from exploring the special features of polymer systems, such as the large changes in properties that may be produced by small alterations in molecular parameters. While dielectric spectroscopy experiments~\cite{CasaliniJCP2007} and molecular dynamics simulations~\cite{LJC} have probed the dependence of thermodynamic scaling on chain length for poly(methylmethacrylate) (PMMA) and Lennard-Jones chains, respectively, it is in general difficult experimentally to finely tune a single molecular parameter, and simulations are restricted to systems far above the glass transition temperature. Moreover, some striking empirical correlations between the scaling exponent and the fragility parameter~\cite{RolandPRE2004, RolandPRE2005, CasaliniJNCS2006, GrzybowskiPRE2006} also invite theoretical considerations. We address the above issues by employing the generalized entropy theory,~\cite{FreedACR2011, JacekACP2008, JacekJPCB2005a, JacekJPCB2005b, JacekJCP2005, JacekJCP2006, JackJCP2006, Evgeny} which has been previously developed to describe both the universal characteristics of glass formation and the specific properties of polymeric glass-forming liquids.

One of the strengths of the generalized entropy theory is the predictive ability to treat the influence of the short-range correlations imparted by chain connectivity, semiflexibility and molecular details on the glass formation of polymers. The previously successful applications~\cite{FreedACR2011, JacekACP2008} suggest that the theory could be utilized to investigate more specific details, such as the thermodynamic scaling of polymer melts. Hence, we assess the influence of molecular details on thermodynamic scaling of polymer melts within this molecular theory of polymer glass formation. All of the following factors, including the chain rigidity, the cohesive energy, the chain length, and the length of the side groups, are demonstrated as significantly influencing the scaling exponent $\gamma$. The computed trends are found to agree well with available experiments, although the highly steep character of the square well interactions of a lattice model leads to very large values of $\gamma$ in accord with expectations and implies that only general trends should be considered. Correlations between the scaling exponent and the fragility parameter emerge from our calculations and thus suggest a universal physical mechanism for both the thermodynamic scaling of polymer dynamics and the fragility of glass-forming  polymers.

Section II begins with a brief review of the generalized entropy theory of polymer glass formation followed by a demonstration that thermodynamic scaling is well recovered within the generalized entropy theory, provided the employed pressure is not very high. Section III examines the influence of chain rigidity, cohesive energy, the lengths of the chain backbone and the side groups on thermodynamic scaling. We discuss the correlations between the scaling exponent and the fragility parameters as well as the anticipated differences from experiment caused by the very abrupt nature of the repulsive potential inherent in lattice models.

\section{Thermodynamic scaling within the generalized entropy theory}

This section begins with a brief introduction to the generalized entropy theory of polymer glass formation and a summary of the basic features of the theory that are required for the present work. We then determine whether and under what conditions the thermodynamic scaling of relaxation times emerges from the generalized entropy theory.

\subsection{Generalized entropy theory}

The generalized entropy theory has been developed with the initial aim of providing a molecular understanding of the universal properties of glass-forming polymer fluids and of explaining the strong variations in glass transition temperature $T_g$ and in fragility between different polymer materials. To this end,  the configurational entropy, a central quantity in the theoretical descriptions of the glass transition, is evaluated from the lattice cluster theory (LCT) for semiflexible polymer chains.~\cite{LCT1, LCT2} The LCT describes the influence of molecular details by employing an extended lattice model in which monomers have internal structure reflecting their size, shape and bonding patterns. By combining the LCT with the Adam-Gibbs (AG) model,~\cite{AG} the generalized entropy theory allows describing the influence of short-range correlations, induced by chain rigidity and monomer structure, on the glass formation of polymers. Note that the theory identifies the entropy density $s_c$, i.e., the configurational entropy per lattice site, as the essential quantity for use in the AG model. Thus, LCT computations of $s_c(T)$ have enabled the direct determination of three characteristic temperatures of glass formation,~\cite{JacekACP2008, JacekJPCB2005a, JacekJPCB2005b, JacekJCP2005, JacekJCP2006} namely, the ``ideal'' glass transition temperature $T_0$ where $s_c$ extrapolates to zero, the onset temperature $T_A$ which signals the onset of non-Arrhenius behavior of the relaxation time and which is evaluated from the maximum in $s_c(T)$, and the crossover temperature $T_I$ which separates two temperature regimes with qualitatively different dependences of the relaxation time on temperature and which is evaluated from the inflection point in $Ts_c(T)$. The relaxation time $\tau$ is then obtained from $s_c$ and the AG relation,
\begin{equation}
\tau=\tau_\infty\exp[\beta\Delta\mu s_c^\ast/s_c(T)],
\end{equation}
where $\beta=1/(k_BT)$ with $k_B$ Boltzmann's constant, $\tau_\infty$ is the high temperature limit of the relaxation time, $\Delta\mu$ is the limiting temperature independent activation energy at high temperatures, and $s_c^\ast$ is the high temperature limit of $s_c(T)$. The high temperature activation energy is estimated  from the empirical relation $\Delta\mu=6k_BT_I$ and $ \tau_\infty$ is set to be $10^{-13}$ s. Thus, the structural relaxation time is computed within the generalized entropy theory without adjustable parameters beyond those used in the LCT for the thermodynamics of polymers. The temperature dependence of the relaxation time enables determination of the glass transition temperature $T_g$, the fourth characteristic temperature, from the common empirical definition $\tau(T_g)=100$ s. (The use of a Lindermann criterion yields essentially equivalent results.~\cite{JacekJPCB2005a}) Therefore, glass formation is described by the generalized entropy theory as a broad thermodynamic transition with four characteristic temperatures ($T_A$, $T_I$, $T_g$, $T_0$).

The generalized entropy theory has previously been applied to investigate essential molecular and physical features affecting glass-formation, ~\cite{JacekACP2008, JacekJPCB2005a, JacekJPCB2005b, JacekJCP2005, JacekJCP2006, JackJCP2006} and recently to model the glass formation of poly($\alpha$-olefins).~\cite{Evgeny} These studies explain some experimentally observed trends, while many theoretical predictions are confirmed by experiments~\cite{FreedACR2011, JacekACP2008}, suggesting that the theory correctly captures general trends of glass formation in polymers.  We further extend the theory in this paper to investigate thermodynamic scaling of the dynamics of polymer melts, whether the LCT also predicts thermodynamic scaling, how the exponent $\gamma$ varies with molecular parameters, and the relation of $\gamma$ to other measurable quantities. The theory describes the polymers as involving monomers that extend over several lattice sites with connectivities corresponding to the molecular structures. The key parameters of the theory and their significance are as follows: (1) The bending energy $E_b$ describes the chain rigidity which may differ between the backbone and the side groups. The bonds are fully flexible when $E_b=0$, whereas they are completely rigid in the $E_b\rightarrow\infty$ limit. (2) The cohesive energy parameter $\epsilon$ describes the net attractive van der Waals interactions between the nearest neighbor united atom groups. (3) The monomer structure and molecular weight enter into the theory through a set of geometrical indices, providing a substantial improvement over the traditional lattice theories. Further information on the generalized entropy theory can be found in recent reviews~\cite{FreedACR2011, JacekACP2008}.

\subsection{Testing thermodynamic scaling}

\begin{figure}[tb]
 \centering
 \includegraphics[angle=0,width=0.48\textwidth]{Fig1.eps}
 \caption{The logarithm of relaxation time $\log(\tau)$ calculated from the generalized entropy theory as a function of the ratio $\phi^\gamma/T$ with $\gamma=14.0$ for various pressures. The computations are performed for a melt of chains with the structure of poly(propylene) (PP) with $z=6$, $a_{cell}=2.7$ \AA{},  $\epsilon/k_B=200$ K, $E_b/k_B=400$ K and $N=8000$. The same values of $z$, $a_{cell}$, $\epsilon$, $E_b$ and $N$ are used in the computations presented in Fig. 2. $\tau$ is given in units of seconds, which is also used in Fig. 4. Thermodynamic scaling holds well for low pressures, but relaxation times for $P\gtrsim 50$ MPa deviate from the master curve.}
\end{figure}

\begin{figure}[t]
 \centering
 \includegraphics[angle=0,width=0.48\textwidth]{Fig2.eps}
 \caption{The logarithm of glass transition temperature $\log(T_g)$ as a function of the logarithm of glass transition specific volume $\log(V_g)$. The red solid line is a linear fit to the data of slope $13.47$ for $P \leq 50.7$ MPa. A linear relationship between $\log(T_g)$ and $\log(V_g)$ indicates that the relaxation times obey thermodynamic scaling.}
\end{figure}

As a first test of whether the generalized entropy theory describes thermodynamic scaling and as a prelude to more extensive calculations below that probe the  variation of the scaling exponent with each of the individual parameters of the model, we choose a polymer system with the structure of poly(propylene) (PP) because such a structure requires the minimal number of parameters in the LCT. The following parameters are used in the calculations: the lattice coordination number ($z=6$),  the cell volume ($v_{cell}=a_{cell}^3=2.7^3$ \AA{}$^3$), the cohesive energy parameter ($\epsilon/k_B=200$ K), the bending energy ($E_b/k_B=400$ K) and the chain length ($N=8000$). Following  previous work, the computations are performed at constant pressure. Then, the relaxation time $\tau$ and volume fraction $\phi$ are obtained as a function of temperature for various pressures up to $P=293.8$ MPa and are used to analyze the nature of  thermodynamic scaling. Although recent work suggests the use of the reduced-unit relaxation time for analyzing the thermodynamic scaling,~\cite{RolandJCP2011} we employ the absolute values which also work well in most cases and which yield almost identical values of the scaling exponent. The scaling exponent $14.0$ collapses the data for $P\leq50.7$ MPa onto a master curve, but  Fig. 1 implies that deviations from a master curve appear when the pressure exceeds $\sim50$ MPa.

As noted in Ref.~\cite{PaluchJPCM2007}, another convenient method to estimate the scaling exponent is from the linear relationship between $\log(T_g)$ and $\log(V_g)$,
\begin{equation}
\log (T_g)=A-\gamma\log(V_g),
\end{equation}
that follows as a consequence of thermodynamic scaling, where $V_g$ is the specific volume (defined as $V=1/\phi$) at the glass transition temperature. Figure 2 displays the correlation between $\log (T_g)$ and $\log(V_g)$ that varies linearly only in the low-pressure regime.

According to isomorph theory~\cite{Dyre5, Dyre6, Dyre7, Dyre8}, the scaling exponent is not constant, but generally is a function of density. Thus, a natural question  is whether the departures at higher pressures in our computations arise from using a constant value of $\gamma$. We have tried to employ the density-dependent scaling exponent $\gamma(\phi)$ to collapse the data presented in Fig. 1 using $\gamma(\phi)$ obtained from the slopes in Fig. 2, but  improvements are minimal at high pressures. Additionally, our computations display a similar breakdown at higher pressures for R\"{o}ssler scaling,~\cite{Rossler, JacekACP2008} in which data for the normalized relaxation times $\tau/\tau(T_I)$ collapse to a single function of $(T_g/T)(T_I-T)/(T_I-T_g)$ (data not shown). We thus believe that the departures at higher pressures are probably due to inherent limitations of the employed lattice model. Therefore, subsequent computations are performed in the low-pressure regime and probe the calculated variation of the scaling exponent with the molecular parameters of the LCT using data for four pressures ($P=0.1$, $10.1$, $30.4$, $50.7$ MPa).

\subsection{Comparison with experiment}

\begin{figure}[tb]
 \centering
 \includegraphics[angle=0,width=0.48\textwidth]{Fig3.eps}
 \caption{Specific volumes $v$ as a function of temperature $T$ for various pressures~\cite{footnote1}. The symbols are experimental data taken from Ref.~\cite{PVT} for atactic PP with high molecular weight, and the lines are results calculated from the generalized entropy theory for a melt of chains with the PP structure with $z=6$, $E_b/k_B=409$ K and $N=8000$. The cell volume parameter $a_{cell}$ and cohesive energy $\epsilon$ are adjusted to decrease with pressure in order to better describe the experimental data. The parameters are summarized in Table I.}
\end{figure}

\begin{table}[t]
\centering
\small\addtolength{\tabcolsep}{9pt}
\caption{Cell volume parameters $a_{cell}$, cohesive energies $\epsilon$, calculated glass transition temperatures $T_g^{cal}$, and experimental glass transition temperatures $T_g^{exp}$~\cite{Pressure} for various pressures. Using the pressure dependent $a_{cell}$ and $\epsilon$ along with the bending energy $E_b/k_B=409$ K produces the calculated pressure dependence of the glass transition temperature in good agreement with experimental one.}
\begin{tabular}{@{}rrrrr@{}}
\hline\hline
$P$, MPa&$a_{cell}$, \AA{}&$\epsilon/k_B$, K&$T_g^{cal}$, K&$T_g^{exp}$, K\\
\hline
$0.1$& $3.000$ & $266$ & $258.2$ & $258.0$\\
$20$ & $2.990$ & $260$ & $262.6$ & $262.4$\\
$40$ & $2.980$ & $253$ & $266.6$ & $266.5$\\
$60$ & $2.975$ & $246$ & $270.8$ & $270.6$\\
$80$ & $2.970$ & $238$ & $274.5$ & $274.4$\\
$100$ & $2.965$ & $230$ & $278.2$ & $278.2$\\
\hline\hline
\end{tabular}
\end{table}

The above illustrative computations exhibit a much larger scaling exponent than experimentally observed for PP, where $\gamma$ is found to be around $2.0$ for atactic PP.~\cite{HollanderJNCS2001} The model parameters, $a_{cell}$ and $\epsilon$, used in these calculations are taken as independent of pressure to enable subsequent studies of how $\gamma$ varies as a single parameter is changed. However, because the experimental equation of state for PP displays the coefficient of thermal expansion and the isothermal compressibility as roughly linearly dependent on pressure, the above illustrative calculations poorly describe the equation of state of PP. The equation of state, however, may be described reasonably well when recognizing that as the pressure is elevated, the average interatomic spacings decrease, so the cell volume parameter $a_{cell}$ should diminish. Similarly, interatomic forces at elevated pressures are more repulsive on average, so the effective attractive interaction energy $\epsilon$ should decrease (be less attractive) as pressure increases. Thus, the parameters $\epsilon$ and $a_{cell}$ are chosen to obtain a reasonable fit to the equation of state data for atactic PP~\cite{PVT} and thus decrease with pressure (see Table I).  As shown in Fig. 3, the computations provide a satisfactory description of the experimental equation of state data over a reasonable range of temperatures and pressures. Deviations become evident as temperature decreases, but the overall agreement enormously improves over the treatment with pressure independent parameters. Using these parameters and a pressure independent bending energy ($E_b/k_B=409$ K), the computations perfectly reproduce the experimental data for pressure dependence of the glass transition temperature, as displayed in Table I, where the calculated glass transition temperatures $T_g^{cal}$ are presented together with the experimental glass transition temperatures $T_g^{exp}$ determined from dielectric spectroscopy experiments of Gitsas and Floudas.~\cite{Pressure} We further find that thermodynamic scaling persists for low pressures, but with the larger scaling exponent ($\gamma\approx23$ ).

As discussed below, the computed scaling exponent generally significantly exceeds all available experimental data where $\gamma$ lies in the range from $0.13$ to $8.5$ for most materials.~\cite{Roland0, Floudas0} The qualitative argument that the magnitude of scaling exponent $\gamma$ reflects the steepness of the repulsive part of the potential suggests that our lattice model for polymers correspond to a system with a very steep potential and, therefore, that the generalized entropy theory can only capture qualitative trends for $\gamma$ of polymer melts. In fact, the lattice model is widely believed as implicitly assuming a square well potential and thus corresponds to a system described by a power law (i.e., $r^{-n}$, where $r$ is the separation between two particles) fluid with an infinite exponent $n$. The treatment of correlations (such as chain connectivity, semiflexibility and monomer molecular structure) by the lattice cluster theory presumably softens the repulsions, but the scaling exponent $n$ tends towards an infinity for a monomeric system where the effective repulsion is steepest.

\section{Results and discussion}

This section provides a systematic investigation of the influence of the bending energy, cohesive energy, backbone and side chain lengths on the thermodynamic scaling of polymer melts, with particular focus on how these molecular factors influence the scaling exponent $\gamma$ which provides an important measure reflecting the degree to which volume effects govern the temperature and pressure dependence of the relaxation times. Whereas correlations determined experimentally suffer from the fact that several molecular parameters change simultaneously as the chemical species varies, calculations may be performed varying one parameter at a time. Thus, we examine the presence of a correlation between the fragility and the scaling exponent when only a single parameter is varied. For this reason, the calculations consider the pressure independent $a_{cell}$ and $\epsilon$ to enable varying one of them independently, with the recognition that the general trends would be the same.

\subsection{Influence of the bending energy}

\begin{figure}[tb]
 \centering
 \includegraphics[angle=0,width=0.48\textwidth]{Fig4.eps}
 \caption{(a) The logarithm of relaxation time $\log(\tau)$ as a function of the ratio $\phi^\gamma/T$ for various $E_b$. (b) The logarithm of glass transition temperature $\log(T_g)$ as a function of the logarithm of glass transition specific volume $\log(V_g)$ for various $E_b$. The solid lines in (b) are linear fits. The computations are performed for the PP structure with $z=6$, $a_{cell}=2.7$ \AA{}, $\epsilon/k_B=200$ K and $N=8000$. The same values of $z$, $a_{cell}$, $\epsilon$ and $N$ are used in the computations presented in Figs. 5 and 7.}
\end{figure}

\begin{figure}[tb]
 \centering
 \includegraphics[angle=0,width=0.48\textwidth]{Fig5.eps}
 \caption{Scaling exponents $\gamma$, estimated from two independent methods, as a function of bending energy $E_b$. The red squares and blue circles are obtained from relaxation times and Eq. (2), respectively.}
\end{figure}

\begin{figure}[b]
 \centering
 \includegraphics[angle=0,width=0.48\textwidth]{Fig6.eps}
 \caption{Scaling exponents $\gamma$ as a function of side group bending energy $E_b^s$ for various fixed backbone bending energies $E_b^b$. The calculations consider a poly($1$-pentene) (PPe) structure with $z=6$, $a_{cell}=2.7$ \AA{}, $\epsilon/k_B=200$ K and $N=8000$.}
\end{figure}

The degree of chain rigidity is modeled in terms of the bending energy $E_b$ in the generalized entropy theory and has been shown to strongly affect the fragility and the glass transition temperature.~\cite{FreedACR2011, JacekACP2008} We now consider how the bending energy influences the thermodynamic scaling for a polymer system with the PP structure because its treatment requires only a single backbone bending energy. The cell volume parameter, cohesive energy and chain length are fixed. $\tau$, $T_g$ and $V_g$ are then computed as a function of $T$ along four isobars ($P=0.1$, $10.1$, $30.4$, $50.7$ MPa). The results displayed in Fig. 4 use the two independent approaches introduced in Subsec. II (B) to estimate the scaling exponent. Both methods find scaling for pressures up to $50.7$ MPa. Figure 5 presents the computed scaling exponent as a function of bending energy from the two methods which again generate almost identical results. Thus, the calculated scaling exponent is presented using the more convenient linear relation between $\log (T_g)$ and $\log(V_g)$.

Figure 5 clearly indicates that the scaling exponent decreases with the backbone stiffness and tends to saturate at large bending energies. While the PP structure is chosen above for illustrating the effect of the backbone bending energy, the side groups can have a separate bending energy when the length of the side groups $n$ is sufficiently large ($n\geq2$). Since the relative flexibility of the backbone and side groups has been shown to strongly correlate with the fragility of polymer glasses,~\cite{FreedACR2011, Evgeny} it is instructive to examine the influence of the side group rigidities. We thus consider a melt of polymers with the structure of poly($1$-pentene) (PPe) as an illustration since this structure has been employed by Dudowicz \textit{et al.}~\cite{JacekACP2008, JacekJPCB2005a, JacekJPCB2005b, JacekJCP2005, JacekJCP2006} to investigate the universal properties of glass formation for three different classes of polymers. We first find that the scaling exponent still decreases as the backbone bending energy grows for fixed side group bending energies (data not shown). The results displayed in Fig. 6 show that the side group bending energy has a similar effect on the scaling exponent for fixed backbone bending energies. Hence, the scaling exponent diminishes as either the backbone or side chain stiffen. Our computations thus indicate that the density effect on the dynamics of polymers is enhanced as the chain becomes flexible, a trend in good agreement with experiments; e.g., the scaling exponent is $1.25$ for PMMA,~\cite{Tarjus1} while it significantly increases for more flexible polymers such as poly(methylphenylsiloxane), where $\gamma$ is equal to $5.6$.~\cite{PaluchJCP2002}

\begin{figure}[tb]
 \centering
 \includegraphics[angle=0,width=0.48\textwidth]{Fig7.eps}
 \caption{(a) Isochoric fragility parameter $m_V$ as a function of bending energy $E_b$. (b) The product of isobaric expansion coefficient $\alpha_P$ at the glass transition point and glass transition temperature $T_g$ as a function of bending energy $E_b$ at constant pressure ($P=0.1$ MPa). The lines are a guide to the eye.}
\end{figure}

Fragility is a basic property of glass-forming liquids, and its relation to experimental data for thermodynamic scaling has been discussed.~\cite{RolandPRE2004, RolandPRE2005, CasaliniJNCS2006, GrzybowskiPRE2006} It is straightforward to show that thermodynamic scaling implies,
\begin{equation}
\frac{m_V}{m_P}=\frac{1}{1+\gamma \alpha_P T_g},
\end{equation}
where $m_V=\partial \log (\tau)/\partial (T_g/T)|_{V, T=T_g}$ is the isochoric fragility parameter, $m_P=\partial \log (\tau)/\partial (T_g/T)|_{P, T=T_g}$ the isobaric fragility parameter and $\alpha_P=(1/V)(\partial V/\partial T)|_{P, T=T_g}$ the isobaric expansion coefficient at the glass transition temperature. Moreover, $m_V/m_P$ can be directly related to the ratio of the isochoric activation energy $E_V=R \partial \log (\tau)/\partial (T^{-1})|_V$ to the isobaric activation enthalpy $H_P=R \partial \log (\tau)/\partial (T^{-1})|_P$ with $R$ the gas constant, i.e.,
\begin{equation}
\frac{m_V}{m_P}=\left . \frac{E_V}{H_P} \right |_{T=T_g}.
\end{equation}

Since the computations are performed at constant pressure, $m_P$ and $\alpha_P$ can be directly determined according to their original definition. Then, the isochoric fragility parameter $m_V$ is calculated from Eq. (3) using the values of $m_P$ and $\alpha_P$ at $P=0.1$ MPa, or equivalently from $m_V=\partial \log (\tau)/\partial (\Gamma/\Gamma_g)|_{\Gamma=\Gamma_g}$, where $\Gamma=\phi^\gamma/T$ and the glass transition point $\Gamma_g$ is similarly defined by $\tau(\Gamma_g)=100$ s. Both methods produce identical results. As illustrated in Fig. 7 (a), larger bending energy yields increased $m_V$, as is indeed already evident from the curves in Fig. 4(a). Thus, the variation of the bending energy affects both $m_V$ and $m_P$ similarly. This result is not surprising in view of the positive correlation between $m_P$ and $m_V$ found empirically~\cite{RolandPRE2005, GrzybowskiPRE2006} and from our computations described in Subsec. III (E). The generalized entropy theory also reveals that the packing efficiency provides a general determinant of the fragility of polymers.~\cite{FreedACR2011, JacekACP2008} Thus, the density scaling for the dynamics of glassy polymers and the magnitude of the scaling exponent may also be a consequence of the packing efficiency since the strong correlation between fragility and the scaling exponent is established in Subsec. III (E).

Experiments find that $\alpha_P T_g$ is approximately constant for most glassy materials~\cite{RolandPRE2004, RolandPRE2005} so that a master curve can be constructed between $E_V/H_P$ and $\gamma$ based on Eqs. (3) and (4) for a variety of glassy materials. While such an empirical finding is very appealing, our computations indicate that it breaks down when a single molecular parameter is varied. As an illustration,  Figure 7(b) exhibits $\alpha_P T_g$ as monotonically increasing with $E_b$.  Similarly, $\alpha_P T_g$ systematically changes with other molecular parameters, such as cohesive energy, chain length and side group length, when the other parameters are held constant. Therefore, a master curve between $E_V/H_P$ and $\gamma$ cannot be established within the generalized entropy theory. It should be emphasized that empirically observed correlations between $E_V/H_P$ and $\gamma$ reflect its approximate nature.

\subsection{Influence of the cohesive energy}

\begin{figure}[tb]
 \centering
 \includegraphics[angle=0,width=0.48\textwidth]{Fig8.eps}
 \caption{Scaling exponent $\gamma$ and isochoric fragility parameter $m_V$ as a function of cohesive energy $\epsilon$. The computations are performed for a polymer melt with the PP structure with $z=6$, $a_{cell}=2.7$ \AA, $E_b/k_B=400$ K and $N=8000$.}
\end{figure}

The cohesive energy parameter $\epsilon$ describes the net attractive interactions between nearest neighbor united atom groups and strongly affects the equation of state. The previous analyses of the generalized entropy theory~\cite{Evgeny} show that the glass transition temperature increases, while the fragility decreases, as the cohesive energy grows. Again, this is rationalized in the generalized entropy theory in terms of the packing efficiency of the polymers since larger attractive interactions are expected to induce the polymers to pack more efficiently. The influence of the cohesive energy parameter on the thermodynamic scaling of polymers is examined for a high molar mass polymer with the PP structure for varying cohesive energies while keeping other parameters fixed. The resulting scaling exponent $\gamma$ and isochoric fragility parameter $m_V$ are presented as a function of $\epsilon$ in Fig. 8. Not surprisingly, $\gamma$ significantly increases when $\epsilon/k_B$ grows from $100$ K to $300$ K. Thus, our results confirm the importance of the packing efficiency in determining the density-temperature scaling on the dynamics of supercooled polymer melts. Moreover, $m_V$ changes in the opposite direction, indicating again a negative correlation between the scaling exponent and the fragility.

\subsection{Influence of the chain length}

\begin{figure}[b]
 \centering
 \includegraphics[angle=0,width=0.48\textwidth]{Fig9.eps}
 \caption{Scaling exponent $\gamma$ and isochoric fragility parameter $m_V$ as a function of chain length $N$. The computations are performed for a polymer melt with the PP structure with $z=6$, $a_{cell}=2.7$ \AA, $\epsilon/k_B=200$ K, $E_b/k_B=400$ K and $N=8000$. The smallest value for $N$ is $8$.}
\end{figure}

Experiments in general reveal that longer chain polymers exhibit higher glass transition temperatures and higher fragilities. Such a trend has been successfully reproduced by the generalized entropy theory.~\cite{JacekACP2008, Evgeny} These results indicate that the chain length also serves as an important molecular parameter to control the properties of glassy polymers. Recently, Casalini \textit{et al.}~\cite{CasaliniJCP2007} have experimentally detected the impact of varying chain length on thermodynamic scaling by analyzing data for the relaxation times of PMMA samples with four molecular weights. The scaling exponent decreases from $3.7$  to $1.8$ when the chain length grows from $N=3$ to $N=1500$,  while the isochoric fragility varies in the opposite direction. Thus, increasing chain length reduces the importance of the density (or volume) in determining the dynamics of polymers. Figure 9 presents the variation of the scaling exponent and the isochoric fragility parameter with chain length $N$ using calculations for a polymer melt with the PP structure for different chain lengths.  Although the generalized entropy theory can, in principle, be applied to treat monomeric systems with $N=1$,  the mean-field approximations embodied in the LCT are less faithful for such small $N$. Thus,  the computations consider $N \geq 8$. Figure 9 exhibits the scaling exponent as first quickly decreasing with increasing $N$ and then remaining nearly constant at sufficiently large $N$, while the isochoric fragility parameter again proceeds in the opposite direction. This computed trend is in accord with experimental observations described above. The predicted saturation of $\gamma$ and $m_V$ at large $N$ is physically reasonable since there must be a lower bound on $N$ above which most of the properties of polymer melts become insensitive to the change of chain length. Interestingly, recent computer simulations~\cite{LJC} indicate that the scaling exponent increases with chain length for a flexible LJ chain model. However, such a simple model probably does not account for the complicated effects in polymers and may not capture the correct trends for a real polymer material. Instead, our computations provide theoretical agreement for the experimental findings.

\subsection{Influence of the side group length}

\begin{figure}[tb]
 \centering
 \includegraphics[angle=0,width=0.48\textwidth]{Fig10.eps}
 \caption{Scaling exponent $\gamma$ and isochoric fragility parameter $m_V$ as a function of side group length $n$. The computations are performed for the poly($\alpha$-olefin) structure with $z=6$,  $a_{cell}=2.9$ \AA{}, $\epsilon/k_B=200$ K, $E_b^b/k_B=560$ K, $E_b^s/k_B=100$ K and $N=8000$.}
\end{figure}

The side group length $n$ strongly affects the properties of polymers. The dependence of the glass transition temperature and the fragility on the side chain length has been extensively examined in previous works.~\cite{JacekACP2008, JacekJPCB2005a, JacekJPCB2005b, JacekJCP2005, JacekJCP2006} In particular, qualitatively different behaviors for the variation of the glass transition temperature with length of side chain has been revealed for different classes of polymers that are characterized by the ratio of side group to backbone bending energies. Thus, the generalized entropy theory establishes the side group length as a  powerful controllable tool for regulating the glass transition temperature and the fragility of glass-forming polymers. In a previous application of this theory, Stukalin \textit{et al.}~\cite{Evgeny} propose a set of molecular parameters to model glass formation of poly($\alpha$-olefins). We thus choose this model of poly($\alpha$-olefins) to illustrate the influence of side group length on the thermodynamic scaling of polymer melts. Figure 10 displays the computed variation of the scaling exponent and the isochoric fragility parameter with the side group length.  $\gamma$ increases with $n$, while $m_V$ again varies in the opposite direction, implying that a longer side chain leads to the enhancement of the density effect on the dynamics of poly($\alpha$-olefins). This is understandable since the side chains ($E_b^s/k_B=100$ K) are more flexible than the backbone ($E_b^b/k_B=560$ K) in this model, and thus a longer side chain improves the packing efficiency. This, in turn, exerts impacts on the scaling exponent and the fragility.

\subsection{Correlations between the scaling exponent and measures of fragility}

\begin{figure}[tb]
 \centering
 \includegraphics[angle=0,width=0.48\textwidth]{Fig11.eps}
 \caption{Correlations between isobaric fragility parameter $m_P$ at $P=0.1$ MPa and isochoric fragility parameter $m_V$ when varying individual molecular parameters. The lines are a guide to the eye.}
\end{figure}

\begin{figure}[b]
 \centering
 \includegraphics[angle=0,width=0.48\textwidth]{Fig12.eps}
 \caption{Correlations between scaling exponent $\gamma$ and isochoric fragility parameter $m_V$ when varying individual molecular parameters. The lines are linear fits according to Eq. (6) with the fitting parameters, $\gamma_0=-8.65$ and $b=847$ for chains with the poly(propylene) structure, $\gamma_0=-10.54$ and $b=852$ for poly(1-pentene), $\gamma_0=-4.52$ and $b=616$ for poly($\alpha$-olefin).}
\end{figure}

All of our computations indicate a negative correlation between the scaling exponent and the fragility, regardless of which molecular parameter is varied. Such a result is intriguing since it enables establishing correlations between the scaling exponent and the fragility and, hence, a universal physical mechanism for the fragility and the density scaling for the dynamics of polymer melts. Actually, the existence of correlations between the scaling exponent and the fragility has  previously been realized empirically.~\cite{RolandPRE2004, RolandPRE2005, CasaliniJNCS2006, GrzybowskiPRE2006} In particular, two empirical correlations have been suggested by Casalini and Roland~\cite{RolandPRE2005},
\begin{equation}
m_P=m_0+am_V,
\end{equation}
\begin{equation}
\gamma=\gamma_0+b/m_V,
\end{equation}
where $m_0$, $a$, $\gamma_0$ and $b$ are adjustable parameters. Since $m_P$ is dependent on pressure and $m_V$ is not, the coefficients in Eq. (5) vary with pressure, as noted previously.~\cite{RolandPRE2005, GrzybowskiPRE2006} Casalini and Roland~\cite{RolandPRE2005} indicate that these two correlations work well for most glass formers.

While these correlations are very appealing and have important consequences, no prior theory provides an explanation for the correlations. Our study provides the opportunity for testing the correlations, and, perhaps more importantly, for investigating how $m_P$, $m_V$ and $\gamma$ mutually correlate when a single molecular parameter is varied. Figures 11 and 12 display the $m_P-m_V$ and $\gamma-m_V^{-1}$ correlations, respectively, for varying molecular parameters. Remarkably, all of the data never fall onto a single master curve, but they can be roughly categorized into three groups. Choosing the PP structure for illustration, $m_P$ grows linearly with $m_V$ only in a restricted regime of lower values, while the linear relation between $\gamma$ and $m_V^{-1}$ appears perfect over the whole regime. Varying the bending energy, cohesive energy and chain length produces a single universal linear curve. Similar results are found for the structure of PPe. Finally, a linear relation applies for both $m_P-m_V$ and $\gamma-m_V^{-1}$ correlations when only the side group length is altered. Although a single universal relation cannot cover all cases, our computations clearly indicate the presence of correlations between the scaling exponent and fragility. Hence, our study points towards a universal understanding of the fragility and the density scaling of dynamics in polymers.

An important contribution of the generalized entropy theory is the identification of the packing efficiency as the main source of variation in the fragility of glass-forming polymers.~\cite{FreedACR2011, JacekACP2008} The packing efficiency in turn depends on chain rigidity, cohesive energy and molecular details, such as the backbone and side group lengths. Strong support for this simple picture for the origin of variations in fragility is provided by recent experiments~\cite{SokolovMac2008} and simulations.~\cite{PabloPRL2006, SokolovPCCP2013} These findings yield the immediate recognition that the effect of density on the dynamics of polymers, i.e., the magnitude of the scaling exponent, is also determined by the packing efficiency because of the strong correlations between the fragility and the scaling exponent. Hence, the influence of the bending energy, cohesive energy, backbone and side group lengths on the thermodynamic scaling can be rationalized in terms of the efficiency of packing of polymers in the melt.

\section{Summary}

We have employed the generalized entropy theory to investigate the influence of different molecular factors on an intriguing property, namely, the thermodynamic scaling of glass-forming polymers. Thermodynamic scaling emerges from the theory for relatively low pressures in this molecular theory of polymer glass formation. In particular, we systematically examine how the scaling exponent varies when changing a single molecular parameter, including the chain rigidity, the cohesive energy, the chain length and the side group length. All of these molecular factors have been shown to strongly affect the scaling exponent and hence the density effect on the dynamics of polymers. We explore correlations between the scaling exponent and the fragility. Instead of falling onto a single master curve, these correlations appears to depend on the molecular structure. Based on these correlations, we propose that the packing efficiency determines the magnitude of the scaling exponent and hence the relative importance of density for the dynamics of polymers, just as the packing efficiency constitutes a general determinant of fragility.

\begin{acknowledgments}
This work is supported by  the U.S. Department of Energy, Office of Basic Energy Sciences, Division of Materials Sciences and Engineering under Award DE-SC0008631. We are grateful to Jacek Dudowicz and Jack F. Douglas for several useful discussions.
\end{acknowledgments}

redpajama_set_name: RedPajamaArXiv


We want a coalition government at the Centre in 2019: Asaduddin Owaisi.
Hyderabad MP Asaduddin Owaisi on Sunday accused BJP and Congress of competing over "Hindutva politics".
Speaking at ISB leadership summit 'The Journey to 2019' on Sunday, Asaduddin Owaisi questioned spending taxpayers' money on cow protection and cleaning up Ganga for religious sentiment rather than for environmental concern.
"The Modi regime is trying to present Hindu nationalism which is exclusive rather than inclusive Indian nationalism. Following in the footsteps of BJP in welcoming and garlanding terror suspects and people involved in lynching, Congress also welcomed them. This is how both the parties are competing over Hindutva politics. There is real competition in visiting temples. If Modi goes to one temple, Rahul goes to another. Now, we have to see Modi doing Mansarovar Yatra. We don't want acceh din (good days). We are praying for burhe din (bad days) to come so that the Modi government goes," Owaisi added.
"We will support BJP government if it takes back Pandits to Kashmir. BJP hasn't taken even a Pandit back. We have been advocating against Haj subsidy for 11 years. Recently, Supreme Court struck down Haj subsidy. Haj subsidy has stopped, but Mansarovar Yatra is still on," the MP said.
"We want a coalition government at the Centre in 2019. Development takes place only in a coalition government. Regional parties should ensure that Modi doesn't become PM again or else he will create more disasters," he added.


A canopied lane to the only property--through stone walls to an 1850's farmhouse--original post and beam, wide plank floors, walls and ceiling--now a keeping room and library. Then an expansive post and beam living room with massive stone fireplace, dining room, and entertainment room. Barn doors reveal a gourmet kitchen, antiqued Laurentian granite island and Viking range. A master suite with fireplace plus two very private bedrooms with ensuite baths. 87 acres of forest, miles of stone walls and trails, much bordered by conservation land yet within a short drive to Hanover and Lebanon, NH, Dartmouth and Dartmouth-Hitchcock Medical Center, and close access to interstate. New roof and Marvin windows, new multi-zone heating system, wireless security, wi-fi and satellite connection. Few large parcels left--fewer still with so many desirable qualities in one fantastic and close-in setting. A private retreat, family compound, or develop the already-platted 12 lots.


text:
Mobile and Migrating People
According to The World Health Organisation in the year 2000 there were 750 million migrants. Often they did not have skin disease on leaving their country but acquired conditions such scabies or fungus infections from poor housing conditions and overcrowding during migration.
Warning Strife affects many nations and many countries are host to internally displaced persons. Such mobile populations have common skin infections and lack of acceptance in the community and malnourishment. The health facilities available may not have the drugs to treat the condition and consequently visits to local traditional health practitioners are common. Nomadic people such as the Massai tend to have close contact with animals and so cattle ringworm is prevalent. There are frequent changes of sexual partners in remote areas and no access to condoms. The migrant often is also often poorly adapted to food that is foreign and malnourishment is common.
Action No one person or group can be lawfully prevented from receiving primary health care services and in most countries the laws support the right to emergency care. Guidelines to management, assessment of cultural differences, cultural competence, identification of torture, dealing with immigration control have been published in The International Journal of Dermatology and are on the website.
The most helpful skill for managing migrants is to be able to communicate, to speak their language and get a full history. If, as is sadly common, you find yourself assessing skin conditions due to torture, be sure to record a full history and using photography ensure thorough documentation.
Migration from rural to urban areas and sedentary lifestyles, transition from a Mediterranean to a Western diet, control of infectious diseases and consequent longer life expectancy especially in urban areas, have all contributed to the rising prevalence of hypertension and diabetes. To get help from carers that are culturally competent and able to deal with these issues, there must be adaptation to the complexities of living which the immigrant has to deal with.
"I help at an organisation that helps people new to the UK find decent housing and helping them set up their lives here. Migration is not new and won't soon end, it's about making transitions easy."
-Mohammed

redpajama_set_name: RedPajamaCommonCrawl


Welcome! My name is Jennifer, and I'm your photographer here at Jenn B Photography. I run a cozy studio for portrait photography in the south end of Barrie – whether it's milestones, family portraits or boudoir, I handle it all!
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text:
Q: Xml.Linq: Descendants() returns nothing I am trying to read from an ncx file (i.e. xml file) using XElement:
XElement foundNode = ncx.Descendants("navPoint").Where(r => r.Attribute("class").Value == "chapter").FirstOrDefault();

As a result, foundNode is null because ncx.Descendants("navPoint") returns an empty enumeration. But the data is there:
<?xml version='1.0' encoding='utf-8'?>
<ncx xmlns="http://www.daisy.org/z3986/2005/ncx/" version="2005-1" xml:lang="en">
  <head>
    <meta content="8eab2efe-d584-478a-8c73-1304d2ae98fa" name="dtb:uid"/>
    <meta content="3" name="dtb:depth"/>
    <meta content="calibre (0.8.12)" name="dtb:generator"/>
    <meta content="0" name="dtb:totalPageCount"/>
    <meta content="0" name="dtb:maxPageNumber"/>
  </head>
  <docTitle>
    <text>Fine</text>
  </docTitle>
  <navMap>
    <navPoint class="chapter" id="27665f37-ecf5-4934-a044-4f77152e54d9" playOrder="1">
      <navLabel>
        <text>I. BLIND</text>
      </navLabel>
      <content src="Fine_split_003.html"/>

Could you please explain what is wrong here? Thanks.

A: You can also strip out namespaces or refer to elements without using the namespace by using the XElement.Name.LocalName property: Examples here

A: You need to take namespace in XML into account:
XDocument ncx = XDocument.Load("file.xml");
XNamespace df = ncx.Root.Name.Namespace;
XElement foundNode = ncx.Descendants(df + "navPoint").Where(r => r.Attribute("class").Value == "chapter").FirstOrDefault();

redpajama_set_name: RedPajamaStackExchange


text:
История почты и почтовых марок Папуа — Новой Гвинеи связана с периодами колониального раздела, управления Австралией восточной частью острова Новая Гвинея и независимости этой территории, обретённой ею в 1975 году.

Краткий обзор
Территория Новой Гвинеи на севере находилась под контролем Германской империи, и соответственно её почтовые марки находились в обращении с 1888 по 1897 год. После 1897 года для этой колонии выпускались специальные марки, на которых было указано её название. После завоевания Австралией в 1914 году на остатках немецких колониальных марок и на некоторых австралийских марках были сделаны надпечатки. После того, как Территория Новая Гвинея по мандату Лиги Наций была передана Австралии, та организовала на Новой Гвинее почтовую связь и выпуск новых почтовых марок.

На юге, в Папуа, находившемся ранее под управлением Великобритании, в период с 1885 по 1901 год использовались . После создания Австралийского союза эмиссией знаков почтовой оплаты и организацией работы почты ведала австралийская администрация, а почтовые марки печатались в Брисбене, затем в Мельбурне.

Во Вторую мировую войну Новая Гвинея была оккупирована японцами, и гражданская администрация на Папуа была распущена в начале 1942 года. В послевоенное время, с 1945 до 1953 года, использовались почтовые марки Австралии, прежде чем две объединившиеся территории получили собственные марки. Впоследствии новое государственное образование получило почтовую и эмиссионную автономию и, наконец, в сентябре 1975 года — государственную независимость.

Территория Новая Гвинея
С 1896 по 1945 год для этой территории всего было эмитировано 143 почтовых марки, 34 служебных и шесть марок для заказных писем. При этом на марках значились следующие надпечатки или надписи:
 Надпечатка на марках Германии: «Deutsch — Neu — Guinea» («Германская Новая Гвинея»). Надписи на марках: «Deutsch — Neu — Guinea» («Германская Новая Гвинея»). Надпечатка на марках Германской Новой Гвинеи: , что означает «Georgius Rex Imperator» («Георг, король и император») — в честь Георга V, короля Великобритании и императора Индии.
 Надпечатка на марках Австралии: «N. W. Pacific Islands» («Острова северо-западной части Тихого океана»). Надписи на оригинальных марках: «Territory of New Guinea» («Территория Новая Гвинея»); «Postage» («Почтовый сбор»). Надпечатки на марках: «Air mail» («Авиапочта»).

Германская колония

В Германской Новой Гвинее, на архипелаге Бисмарка и на Северных Соломоновых островах первые немецкие почтовые отделения были открыты в 1888 году. Они употребляли некоторые почтовые марки Германской империи, выпущенные в период с 1875 по 1887 год, а именно серии типов «номинал в овале» и «имперский орёл». Эти марки гасились на почтовых отправлениях круглым календарным штемпелем с названием города в верхней части и пятиконечной звездой в нижней части. Через несколько лет посередине календарного штемпеля появилась надпись «DEUTSCH- / NEU-GUINEA» («Германская / Новая Гвинея»), причём на нём можно встретить две или три звезды.

В 1897 и 1898 годах на шести почтовых марках Германии впервые были сделаны надпечатки, где название колонии было напечатано по диагонали в два ряда. Лишь в 1901 году были выпущены первые марки с оригинальной надписью названия колонии. Это была немецкая колониальная серия «Яхта "Гогенцоллерн"» с изображением одноимённого имперского судна.

Австралийская оккупация
В сентябре 1914 года, когда в Европе началась Первая мировая война, австралийские войска вторглись в Германскую Новую Гвинею. В октябре и декабре 1914 года на оставшихся запасах немецких колониальных марок были сделаны надпечатки двух надписей. В верхней строке было указано: «G. R. I.» («Georgius Rex Imperator» — «Георг, король и император»). На второй строке был обозначен новый номинал в мелких единицах — производных австралийского фунта: пенсах («d.») и шиллингах («s.»).

В том же году на Науру был обнаружен запас почтовых марок германских Маршалловых островов, несмотря на то, что германским почтовикам было приказано уничтожить их. Обнаруженные марки были пересланы на Новую Гвинею, где на них были сделаны надпечатки, аналогичные надпечаткам на марках Германской Новой Гвинеи. Продажа их началась в декабре 1914 года.

С января 1915 года до 1925 года на Новой Гвинее и Науру использовались почтовые марки Австралии с надпечаткой «N. W. PACIFIC ISLANDS» («Северо-Западные тихоокеанские острова»). Это были марки из серии «Кенгуру и карта» () и с изображением Георга V.

Австралийский мандат
23 января 1925 года австралийская администрация, управлявшая Территорией Новая Гвинея по мандату Лиги Наций, выпустила первую серию почтовых марок для этой административной единицы с изображением хижин туземной деревни. В июне 1931 года в связи с первой перевозкой почты самолётом на части тиража марок этой серии была сделана надпечатка изображения самолёта и текста «AIR MAIL» («Авиапочта»).

2 августа того же года на смену рисунку с хижинами пришла серия с изображением национального символа территории — Реггиановой райской птицы и с датами «1921 / 1931», которая была напечатана в ознаменование десятой годовщины мандата Австралии. В тот же день в продаже появилась серия с надпечатками авиапочты. 30 июня 1932 года эти марки были переизданы с несколько изменённым рисунком — без указания памятных дат. Позднее для двух марок высоких номиналов (в 2 и 5 австралийских фунтов) был разработан новый рисунок — самолёт, летящий над рекой Булоло (месторождение золота, где с 1932 года велась добыча). Обе марки поступили в обращение 1 мая 1935 года.

События, связанные с британской королевской семьёй навеяли сюжеты двух последующих омнибусных выпусков, осуществлённых одновременно с территориями Науру и Папуа. В мае 1935 года на двух почтовых марках номиналами в 1 и 2 пенса из серии «Райская птица» («Raggiana Bird of Paradise») были сделаны надпечатки в честь . В 1936 году в ознаменование коронации короля Георга V увидел свет выпуск, общий для указанных трёх территорий. Это были четыре почтовые марки Новой Гвинеи с изображением профиля короля, выгравированного Фрэнком Мэнли (Frank Manley) по фотографии Бертрама Парка (Bertram Park).

1 марта 1939 года в обращение вышла новая серия авиапочтовых марок («AIRMAIL POSTAGE») с рисунком марок 1935 года, запечатлившим месторождение золота в районе Булоло.

Японское вторжение
После нападения японцев на Рабаул на Новой Британии в январе 1942 года и оккупации остальной территории новогвинейское гражданское управление было быстро распущено. Однако на филателистическом рынке известны некоторые марки Новой Гвинеи с фальшивой надпечаткой, имитирующей японскую надпечатку на почтовых марках оккупированной Голландской Ост-Индии.

Территория Папуа
За всю историю существования этой территории для неё было издано 123 оригинальных почтовых марки и 54 служебных. На этих марках в различное время использовались надписи «British New Guinea» («Британская Новая Гвинея») и «Postage» («Почтовый сбор») или надпечатки «Papua» («Папуа») и «O. S.» («Official Stamp» — «Служебная марка»).

Британская Новая Гвинея
Англичане контролировали юго-восток острова Новая Гвинея с конца 1884 года. Управление колонией осуществлялось из Квинсленда, почтовые марки которого с изображением королевы Виктории использовались в Британской Новой Гвинее с 1885 по 1901 год. На применявшихся в колонии календарных штемпелях стояла аббревиатура «B. N. G.» (то есть «British New Guinea» — «Британская Новая Гвинея»).

1 июля 1901 года вышла серия марок с названием колонии («BRITISH NEW GUINEA» — «Британская Новая Гвинея»), напечатанным на них способом глубокой печати фирмой De La Rue в Лондоне. Посередине марок была выгравирована фотография, сделанная капитаном Бартоном, секретарём наместника. На фотографии снят местный тип судна, лакатои (lakatoi) с клешнеобразными парусами, изготовленными из листьев пандануса, на фоне деревни , неподалёку от Порт-Морсби.

Территория Папуа
В 1902 году Британская Новая Гвинея перешла под управление Австралийского союза. В 1906 году новое административное подчинение было законодательно оформлено Законом Великобритании о Папуа (Papua Act), которым также вводилось новое название для этого колониального образования — Территория Папуа (). На нераспроданных запасах марок «Лакатои» была сделана надпечатка текста «PAPUA» («Папуа»). В 1906 году они вышли в обращение в Порт-Морсби, а в мае 1907 года — в Брисбене. В основе этого выпуска лежала не политическая необходимость, а скорее стремление получить доход от продажи марок филателистам.

В ноябре 1907 года рисунок «Лакатои» появился на почтовых марках с оригинальным названием «PAPUA», отпечатанных типографским способом в той же типографии, что и марки Австралии, в Мельбурне. Рисунок оставался тем же до 1932 года; единственными изменениями были вариации в номинале (при смене почтовых тарифов в 1912, 1921 и 1924 годах) и в цвете. При этом единственным изменением, к которому отрицательно отнеслась общественность, стал одноцветный выпуск 1911 года. К двухцветному рисунку снова вернулись в 1915 году; на запасах одноцветных марок была сделана надпечатка номинала в один пенни, и они были в основном распроданы коллекционерам.

В 1929 году по маршруту Австралия — Порт-Морсби, а также в некоторые другие отдалённые места колонии, такие как полицейский участок в Оровилле (Oroville) на реке Флай, состоялись первые авиарейсы, которыми был перевезён некоторый объём почты. Для этого вида почты на трёх почтовых марках типа «Лакатои» была сделана надпечатка текста «AIR MAIL» («Авиапочта») или самолёта.

Надпечатки 1929—1931 годов помогли увеличить в 2,5 раза объёмы продаж почтовых марок Папуа, прежде всего благодаря коллекционерам.

Предвоенные годы
В 1932 году, чтобы увеличить доходы колонии, руководитель администрации Хьюберт Муррей (Hubert Murray) отдал распоряжение о выпуске новой серии почтовых марок, сюжеты которых были выбраны на основании проектов и фотографий, предложенных чиновниками колониальной администрации. Были созданы пять одноцветных марок по рисункам Э. Уайтхауса (E. Whitehouse). Заключённые в орнамент работы Ф. Уильямса (F. E. Williams), два рисунка Уильямса и девять фотографий Уильямса и Альфреда Гибсона (Alfred Gibson) легли в основу одиннадцати двухцветных марок. На 16 почтовых марках были помещены сюжеты, отображавшие культуру коренного населения Папуа: парусная лодка «лакатои», жители Папуа в традиционных одеяниях, жилища и две установленные персоны — Стив, сын Оаки, в церемониальном одеянии, впоследствии госслужащий, и старшина Симои (Sergent-Major Simoi), полицейский. Серия была напечатана металлографским способом в Мельбурне и вышла в обращение 14 ноября 1932 года. Продажа марок этой серии принесла казне свыше 10 тыс. фунтов стерлингов в 1932—1933 финансовом году, что было в пять раз больше чем в 1929—1930 финансовом году, последнем, когда не выпускались новые марки.

6 ноября 1934 года пятидесятилетие объявления британского протектората было отмечено изданием четырёх памятных марок по рисункам Фрэнка Мэнли, гравёром которых был Эдвард Броуд (Edward Broad). На них были запечатлены два события, случившиеся 6 июня 1884 года: поднятие флага Великобритании над Порт-Морсби и встреча капитана Эрскина (Erskine) с корабля «Нельсон» (HMS Nelson) и нескольких вождей Новой Гвинеи.

Как и в случае с территориями Науру и Новая Гвинея, события из жизни британской королевской семьи стали поводом для двух омнибусных почтовых выпусков Папуа. В июле 1935 года были переизданы четыре почтовые марки с надпечаткой «HIS MAJESTY'S JUBILEE / 1910 1935» («Юбилей Его Величества / 1910 1935») в ознаменование 25-летия правления Георга V. По случаю коронации Георга VI в 1937 году здесь были выпущены пять марок с его профилем (фотография Б. Парка, гравюра Ф. Мэнли)

Многие переизданные в 1935 году почтовые марки, но без надпечаток, хранились в Мельбурне. В конце концов, их пустили в продажу в мае 1938 года в шести почтамтах в Австралии для коллекционеров, которые готовили памятные почтовые отправления для первого регулярного авиарейса по маршруту Новая Гвинея — Австралия.

Новый юбилей в колонии — 50-летие владения Великобритании Британской Новой Гвинеей — был отмечен почтовым выпуском 5 сентября 1938 года. Он включал пять авиапочтовых марок с видом Порт-Морсби . 6 сентября 1939 года появилась новая авиапочтовая серия по рисунку Эдварда Броуда, который изобразил двух жителей Папуа на плотах, над которыми пролетает самолёт.

Вторая мировая война
В ходе военных действий Второй мировой войны на Тихом океане, Японией были оккупированы Западная Новая Гвинея на западе острова и Территории Новая Гвинея на севере, что привело также к приостановке деятельности гражданской администрации на Папуа 12 февраля 1942 года. Даже если почта австралийской армии вначале и употребляла почтовые марки Папуа, она быстро вернулась к использованию марок Австралии. Прекращение работы гражданской почты лишило смысла переиздание почтовых марок 1932 года и выпуск в январе 1941 года авиапочтовой марки номиналом в 1 шиллинг 6 пенсов, отвечающим тарифу пересылки письма в Англию.

Территория Папуа — Новая Гвинея
По окончании Второй мировой войны в 1945 году и до 1 марта 1953 года на территориях Новой Гвинеи и Папуа в почтовом обращении были марки Австралии.

Для объединённой в 1949 году новой территории позднее, 30 октября 1952 года, была выпущена новая серия почтовых марок на местную тематику и с надписью «Territory of Papua and New Guinea» («Территория Папуа — Новая Гвинея»). Эта серия дополнялась вплоть до 1960 года.

С 1961 года стали выходить памятные марки территории. Помимо местной культуры, экономики, флоры и фауны, сюжеты почтовых марок отражали события постепенного нарастания политической автономии, предоставлявшейся этой территории: создание Законодательного совета (Legislative Council) в 1961 году, участие территории в политических событиях и спортивных мероприятиях Океании и Содружества наций. Начиная с 1960-х годов, при осуществлении почтовых эмиссий с государственной типографией Австралии стали конкурировать европейские печатные компании, такие как Courvoisier и Enshedé. Courvoisier впервые изготовила марки территории, выполненные способом гелиогравюры.

За период с 1952 по 1963 год было выпущено 55 оригинальных почтовых марок и 13 доплатных, на которых употреблялись надписи: «Papua and New Guinea» («Папуа и Новая Гвинея») и «Postage» («Почтовый сбор»). Доплатные марки печатались в 1960 году; в 1966 году их применение было прекращено.

В 1969 году в рисунок одной из марок территории  вкралась ошибка: у изображённой на миниатюре спортивной яхты не было руля и штурвала.

26 января 1972 года на марках одновременно с изображением нового флага и герба территории появилось и новое название страны «Papua New Guinea» («Папуа Новая Гвинея») .

На серии из пяти марок, эмитированной 21 апреля 1975 года, представлены монеты для новой валюты государства — кина и тоэа. В августе появились четыре марки, посвящённые пятым Южнотихоокеанским играм на Гуаме, которые стали последними, выпущенными до провозглашения независимости.

Независимость. Тематика
Независимость Папуа — Новой Гвинеи была провозглашена 16 сентября 1975 года, и к этой дате были изготовлены две марки с картой и флагом нового государства , а также первый почтовый блок . С тех пор страна выпускает собственные почтовые марки и блоки. Тематика современных марок характеризуется достаточным разнообразием и включает традиционные сцены из жизни местного населения, события из жизни английского королевского дома, флору, фауну, транспорт, спорт и другие популярные темы.

Сводные данные
Ниже в таблице приведены сводные данные о почтовых марках, находившихся в обращении на Папуа — Новой Гвинее в течение филателистической истории этого острова, с учётом названия страны и обозначения валюты, указанных на марках.

См. также

Примечания

Литература

 Commonwealth Stamp Catalogue Australia. — : Stanley Gibbons, 2007:
 New Guinea. — P. 118—120 (оккупация и Территория Новая Гвинея, ранее под германским правлением);
 Papua (British New Guinea). — P. 135—138 (Территория Папуа, ранее Британская Новая Гвинея);
 Papua New Guinea. — P. 138—142 (до своей независимости).
 Demont M. Les Lakatoi de Papouasie (1901—1932). — Club philatélique franco-britannique, n. d. [middle of the 1990s].
 Scott 2007. Standard Postage Stamp Catalogue. — New York, NY, USA: Scott, 2006.

Ссылки

Германская Новая Гвинея
Британская Новая Гвинея
Папуа — Новая Гвинея
Ошибки на почтовых марках

redpajama_set_name: RedPajamaWikipedia


Our client known as to uncover out if we could uncover her the truth. She was convinced her husband was having an affair and needed to get the proof to convince their loved ones that he was cheating. They've an arranged marriage and both his household and hers wouldn't accept he was cheating Our client was certain that he had met this woman at work. There had been quite few females at his function and she was fairly positive it was one woman in certain. Soon after talking her situation via with us we decided that surveillance could be the best selection for her.
As the client's husband had been coming house from function late on particular days we decided to follow him from function on 1 of these evenings. Our client told us that he would not leave work early as none of the woman that worked there would leave function just before 1730 hrs.
He left the office with yet another man and two ladies they drove in separate vehicles a man and woman in each and every automobile. They stopped at a Gourmet Pub and went inside. Our operatives followed them in, one wearing a physique cam. They had a couple of drinks at the bar and then the other man and 1 of the ladies left. Her husband and also the other woman then ordered some food and sat down in a quiet corner. Our operatives managed to get a table close enough to have the ability to record their conversation. They had been quite amorous and also the conversation suggested they had been seeing each other for very some time.
We presented our findings to our client and although she quite upset she now had some proof and engaged us to do two much more evenings just to make sure. We did get more proof on the other nights and our client was in a position to take on the household.


text:
Four Mothers is a 1941 American drama film and sequel to Four Daughters (1938) and Four Wives (1939). The film stars Claude Rains, Jeffrey Lynn, May Robson and featuring the Lane Sisters: Priscilla Lane, Rosemary Lane and Lola Lane. It was directed by William Keighley and is based on the story "Sister Act" by Fannie Hurst. The film was released by Warner Bros. on January 4, 1941. The Lane sisters appeared in all three films and also appeared together in the 1939 film Daughters Courageous.

Plot
In this final installment of Warner Brothers' Four Daughters series, the entire Lemp family loses its investment in son-in-law Ben Crowley's (Frank McHugh) out-of-state realty project when a hurricane destroys the development site. So Ben suggests they localize and develop their own property to sell, but no one in town will help finance the venture after the hurricane debacle. So in order to get their hands on some much-needed cash, the Lemp family patriarch, Adam (Claude Rains), sells the house in which he raised his daughters. To his shock, however, he learns the person who bought it is planning to raze the old structure to make way for an apartment building.

To do his part in bringing in more dollars for the family, son-in-law Felix (Jeffery Lynn) travels to Chicago for a job conducting an orchestra. Meanwhile, Kay (Rosemary Lane), the only Lemp daughter who is childless, is upset that husband Clint (Eddie Albert) spends more time at work than with her at home. Things get worse after his lab research leads him closer to the cause of Pneumoconiosis at the town's smelting plant. Eventually, Kay has had it. She too leaves for Chicago—to seek a job in radio. But for both Felix and Kay, the big city proves to hold no suitable alternative to either their financial or family woes. So they both return home.

After moving into an apartment with his sister Etta (May Robson), Adam is invited to conduct for the Beethoven Music Festival at the Hollywood Bowl in Los Angeles. The whole family travels there to proudly watch him. They then return home for the opening of Lemp Acres, the new property Ben has started and developed for the family. Upon Adam's arrival, he finds he has regained the respect of the town—so much so that the townspeople financed the moving of his old house to Lemp Acres, and all is the same as it once was. In the end, as the four daughters hold one of their musical practice sessions, Kay realizes she is finally pregnant.

Cast

References

External links

1941 films
1941 drama films
American black-and-white films
American drama films
American sequel films
1940s English-language films
Films about families
Films directed by William Keighley
Warner Bros. films
Films scored by Heinz Roemheld
Films based on works by Fannie Hurst
1940s American films


text:
using namespace std;
using namespace ngraph;

constexpr NodeTypeInfo op::v0::GenerateMask::type_info;

op::v0::GenerateMask::GenerateMask(const Output<Node>& training,
                                   const Shape& shape,
                                   const element::Type& element_type,
                                   uint64_t seed,
                                   double prob,
                                   bool use_seed)
    : Op({training})
    , m_element_type(element_type)
    , m_shape(shape)
    , m_use_seed(use_seed)
    , m_seed(seed)
    , m_probability(prob)
{
    set_argument(1, make_shared<op::v0::Constant>(element::u64, Shape{shape.size()}, shape));
    set_argument(
        2, make_shared<op::v0::Constant>(element::i32, Shape{}, std::vector<int32_t>{use_seed}));
    set_argument(3,
                 make_shared<op::v0::Constant>(element::u64, Shape{}, std::vector<uint64_t>{seed}));
    set_argument(4,
                 make_shared<op::v0::Constant>(element::f64, Shape{}, std::vector<double>{prob}));
    add_provenance_group_member(input_value(1).get_node_shared_ptr());
    add_provenance_group_member(input_value(2).get_node_shared_ptr());
    add_provenance_group_member(input_value(3).get_node_shared_ptr());
    add_provenance_group_member(input_value(4).get_node_shared_ptr());
    constructor_validate_and_infer_types();
}

shared_ptr<Node> op::v0::GenerateMask::clone_with_new_inputs(const OutputVector& new_args) const
{
    check_new_args_count(this, new_args);
    return make_shared<v0::GenerateMask>(
        new_args.at(0), m_shape, m_element_type, m_seed, m_probability, m_use_seed);
}

void ngraph::op::v0::GenerateMask::validate_and_infer_types()
{
    NODE_VALIDATION_CHECK(this,
                          get_input_partial_shape(0).compatible(PartialShape{}),
                          "Training node should be a scalar flag indicating a mode");

    NODE_VALIDATION_CHECK(
        this, m_element_type.is_static(), "Output element type must not be dynamic.");

    set_output_type(0, m_element_type, m_shape);
}

// V1 version starts
constexpr NodeTypeInfo op::v1::GenerateMask::type_info;

op::v1::GenerateMask::GenerateMask(const Output<Node>& training,
                                   const Output<Node>& shape,
                                   const element::Type& element_type,
                                   uint64_t seed,
                                   double prob,
                                   bool use_seed)
    : Op({training, shape})
    , m_element_type(element_type)
    , m_use_seed(use_seed)
    , m_seed(seed)
    , m_probability(prob)
{
    set_argument(
        2, make_shared<op::v0::Constant>(element::i32, Shape{}, std::vector<int32_t>{use_seed}));
    set_argument(3,
                 make_shared<op::v0::Constant>(element::u64, Shape{}, std::vector<uint64_t>{seed}));
    set_argument(4,
                 make_shared<op::v0::Constant>(element::f64, Shape{}, std::vector<double>{prob}));
    add_provenance_group_member(input_value(2).get_node_shared_ptr());
    add_provenance_group_member(input_value(3).get_node_shared_ptr());
    add_provenance_group_member(input_value(4).get_node_shared_ptr());
    constructor_validate_and_infer_types();
}

shared_ptr<Node> op::v1::GenerateMask::clone_with_new_inputs(const OutputVector& new_args) const
{
    check_new_args_count(this, new_args);
    return make_shared<v1::GenerateMask>(
        new_args.at(0), new_args.at(1), m_element_type, m_seed, m_probability, m_use_seed);
}

const Shape op::v1::GenerateMask::get_mask_shape() const
{
    Shape shape;
    if (auto const_op = as_type<op::v0::Constant>(input_value(1).get_node()))
    {
        shape = const_op->get_shape_val();
    }
    return shape;
}

void ngraph::op::v1::GenerateMask::validate_and_infer_types()
{
    NODE_VALIDATION_CHECK(this,
                          get_input_partial_shape(0).compatible(PartialShape{}),
                          "Training node should be a scalar flag indicating a mode");

    NODE_VALIDATION_CHECK(
        this, m_element_type.is_static(), "Output element type must not be dynamic.");

    PartialShape mask_shape{PartialShape::dynamic()};

    if (input_value(1).get_node_shared_ptr()->is_constant())
    {
        mask_shape = get_mask_shape();
    }

    set_input_is_relevant_to_shape(1);
    set_output_type(0, m_element_type, mask_shape);
}

redpajama_set_name: RedPajamaGithub


text:
Struggling Lincoln firms could get £10,000 to prop up business - here's what you need to know
The council is offering a grant
Calvin Robinson, Local Democracy Reporter
Nicholas FletcherReporter
Lincoln's High Street empty (Image: Paul Whitelam)
Desperate business owners in Lincoln have been thrown a lifeline by city bosses who are now offering up a £10,000 grant for struggling firms.
City of Lincoln Council has offered the grant to small businesses as part of Government support amid the pandemic.
It comes as many companies across Lincolnshire have lost income or have been forced to close due to the virus.
In order to qualify, a business must be based in England, be in receipt of small business rates relief, rural rate relief or tapered relief and be a business in an occupied property as of March 11, 2020.
Man named and charged with assault on emergency worker
Police release warning after reports of teenagers 'coughing at members of the public'
The funding is expected to be available by April 1, 2020.
You can find out if your business is eligible and apply for the grant by filling out this form
The announcement comes as the coronavirus outbreak has affected companies and employees across the county.
This could save some businesses from closure (Image: PA)
The spread of the virus raised concern that some businesses will "go to the wall" without support.
Insurers came under fire for "avoiding pay out" to companies and were called on the back business in the county.
Stewart Hardy, who runs Hardy's Animal Farm in Ingoldmells, warned that failure to help would lead to some companies going under.
Biggest jump yet in coronavirus cases in Lincolnshire
Anger as group of youths spotted in field flouting coronavirus social distancing rules
"There will be a lot of businesses who go to the wall," he said.
"If they do not go under, they will take on a debt burden which makes growth difficult."
Meanwhile, Rishi Sunak, Chancellor of the Exchequer, announced a number of measures to support employers in a £330 billion fiscal stimulus package.
It includes a coronavirus business interruption scheme, as well as other grants to help small business.
The government also said it will pay 80 per cent of wages to employees affected by Covid-19.
Support for those who are self-employed has also been announced.
Ingoldmells


The ehci driver is a USBA (Solaris USB Architecture) compliant nexus driver that supports the Enhanced Host Controller Interface Specification 2.0, an industry standard developed by Intel.
A USB 2.0 host controller includes one high-speed host controller and zero or more USB 1.1 host controllers. The high-speed host controller implements an EHCI (Enhanced Host Controller Interface) that is used for all high-speed communications to high-speed-mode devices.
All USB 2.0 devices connected to the root ports of the USB 2.0 host controller and all devices connected to a high- speed-mode hub should be routed to the EHCI host controller.
All full- and low-speed devices connected to the root ports of the USB 2.0 host controller should be routed to the companion USB 1.1 host controllers. (OHCI or UHCI host controller).
The ehci supports bulk, interrupt, control and iso chronous transfers (on USB1.x devices behind a USB2.0 hub).
There was an unrecoverable USB hardware error reported by the ehci controller. Reboot the system. If this problem persists, contact your system vendor.
No SOF interrupts have been received. This USB EHCI controller is unusable.
High speed USB devices prior to revision 0.95 are not supported.
The driver was unable to take control of the EHCI hardware from the system's BIOS. This failure is ignored. To abort the attach on this take-over failure, comment out a property in ehci.conf. (x86 only).
Low speed device is not supported.
Full speed device is not supported.
The driver detected a low or full speed device on its root hub port. Per USB 2.0 specification, the device should be routed to a companion host controller (OHCI or UHCI). However, no attached companion host controller appears to be available. Therefore, low and full speed devices are not supported.
Low speed endpoint's poll interval of <n> ms is below threshold. Rounding up to 8 ms.
Low speed endpoints are limited to polling intervals between 8 ms and 255 ms. If a device reports a polling interval that is less than 8 ms, the driver uses 8 ms instead.
Low speed endpoint's poll interval is greater than 255 ms.
The low speed device's polling interval is out of range. The host controller does not allocate bandwidth for this device. This device is not usable.
Full speed endpoint's poll interval must be between 1 and 255 ms.
The full speed device's polling interval is out of range. The host controller does not allocate bandwidth for this device. This device is not usable.
High speed endpoint's poll interval must be between 1 and 16 units.
The high speed device's polling interval is out of range. The host controller will not allocate bandwidth for this device. This device will not be usable. Refer to the USB specification, revision 2.0 for the unit definition.
ehci_modify_qh_status_bit: Failed to halt qh=<address>.
Error recovery failed. Please disconnect and reinsert all devices or reboot.
Note - Due to recently discovered incompatibilities with this USB controller, USB2.x transfer support has been disabled. However, this device continues to function as a USB1.x controller. Information on enabling USB2.x support is provided in this man page. Please refer to www.sun.com/io for Solaris Ready products and to www.sun.com/bigadmin/hcl for additional compatible USB products.


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Every region of Spain has its speciality and although Andalucía often comes under fire for having the worst cooking in the country, it does turn out the occasional gem. These shrimp fritters are a staple of the Atlantic Coast around Cádiz, particularly the town of El Puerto de Santa María, or the Port of Sherry, as it is popularly known. Salty, crunchy, with a whack of sweetness from the prawns, these are among the finest tapas in the land. It goes without saying that served with a snifter of bone-dry fino or manzanilla they make a very good start to any party. My thanks to Rick Stein for kindly letting me recreate his recipe here.
Cut the prawns into ½ cm thick pieces. Sift the flour, baking powder and a pinch of salt into a bowl. Make a well in the centre and add the water and wine. Mix together to make a thick, creamy batter. Fold in the prawns, spring onions and parsley. Pour ½ cm of olive oil into a frying pan and place over a high heat. Leave until a drop of the batter sizzles immediately then, in small batches of 2 to 3 at a time, drop large spoonfuls of the batter into the pan, spreading each one out a little with the back of the spoon to get lovely thin, crispy edges as they cook. Turn the fritters every now and then for about 2 minutes, or until puffed up and golden on both sides. Remove with a slotted spoon and drain on a tray lined with kitchen paper. Eat immediately.


On a few occasions, just a few… I fought back with rude sarcastic tones and huffy behavior, sometimes appearing sweet but it was quite sour I assure you.
I was young. I was young to autism. I wanted everyone to understand and the stares infuriated me. I loathed the situation I was in. It was me against all the ignorant… the general public that knew nothing about autism.
I don't know exactly when it all changed…when my frame of mind changed.
That was my first act of acceptance. Once I got over that hump aka "Mount Everest," the stares began to bother me less and less.
I found myself wanting to speak more freely, more openly to others. I found myself using the stares for my own purpose… the purpose of educating and advocating.
If I don't act on a stare, I see it now as a missed opportunity.
In the beginning, I didn't like the stares. I mostly ignored them.
This entry was posted in Melanie's Insights and tagged ASD, autism, autism blog, autism spectrum disorders, pdd-nos. Bookmark the permalink.


Some do not like to cook on Christmas Day and others have nowhere to go, so I compiled a list for those who would like to go out for a meal this Christmas.
Some franchisee owned locations will be open and some will be closed.
Additionally, many Chinese restaurants are normally open as are hotel dining rooms.
Good luck, buon appetito, and ... Merry Christmas!


The Better Bowls Workshop will take place on this Saturday (6th October) starting at 10 am and finishing at 4pm.
and I believe Jimmy is having to work (don't worry Jimmy, you will grow out of this work thing) but I would rather not replace him as this still leaves 5 on the workshop with the space for Jimmy to join us for part of the day if he can/ wants to.
As is the case for my previous bowls courses, bring your own lunch, £10 for the course, but more importantly your ideas, wood blanks (or buy a blank form the club's stock) or a previous bowl you have made. Some of your earlier bowls can be remade as we tend to make them fairly chunky and now have the skill to 'lighten' them with a slightly improved form, with thinner walls and space for decoration. Lets see your previous bowls at the start of the session and we can see how much better our bowls are at the end of the workshop.
This is not a course, but a workshop, so we have no set 'lesson plan' or formal 'aims and objectives' I will provide a setting where we can learn from each other, but also give what guidance and experience I can from the 12 years that I have been making bowls, plates and boxes. We will have fun, gain confidence, become wiser, safer and more adventurous.
Looking forward to it Rolf and turning again not been on the lathe since start of summer. I've got a right chunk that needs 'fixed' lol.