text:
\section{INTRODUCTION}\label{Int}
	Multiferroics are a class of materials that have at least two ferroic orders (ferroelectric, magnetic, and elastic). Magnetoelectric (ME) materials are a subset of multiferroics in which ferroelectric and magnetic orders are coupled. The ME materials are classified into single-phase and composite groups in which composites show higher ME coupling values than single-phase ones\cite{spaldin2019advances,HansSchmid1994,palneedi2016status,Spaldin391,hadi,Feibeg,Kimura,eerenstein2006w}. Since in this class of materials magnetization (polarization) can be controlled by an/a electric field (magnetic field), they can be used in both electrical and magnetic areas, and have a wide range of applications, including magnetic field sensors, spintronics, data storage, actuators, photovoltaic solar cells, etc\cite{bibes2008towards,vopson2015fundamentals,Maignan,olabi2008design}.

	The ME voltage in composite magnetoelectric materials is generated by polarization change in the piezoelectric phase as a result of dynamic mechanical deformation of the magnetostrictive phase induced by the applied ac magnetic field in the presence of the dc magnetic field. In addition, the ME coupling coefficient is affected by magnetostriction and piezoelectric behavior of magnetic and electric phases, respectively. As a result, significant magnetostriction and piezoelectric coefficients are essential for obtaining a high ME voltage coefficient.

	Many studies have been conducted on piezoelectric-ferrite composites like:
	(BiBa)(FeTiZn)O$_{3}$/CoFe$_{2}$O$_{4}$\cite{papi2021dielectric}, PFN-PT/(Co,Ni)Fe$_{2}$O$_{4}$\cite{Mokhtari}, PMN-PT/CoFe$_{2}$O$_4$\cite{zabotto2020magnetodielectric}  BaTiO$_3$/CoFe$_{2}$O$_4$\cite{verma2019magnetic,etier2016direct}, PMN-PT/NiFe$_{2}$O$_4$\cite{ahlawat2013evidence}, PZT/Ni$_{0.2}$Co$_{0.8}$Fe$_{2}$O$_4$\cite{bammannavar2009magnetic},
	PZT/CoFe$_{2}$O$_4$\cite{atif2015interplay}, PVDF/CoFe$_{2}$O$_4$\cite{gonccalves2015development}, and etc.
	Among them, Pb-based ferroelectrics, such as PZT and  PMN-PT, have been frequently utilized as the ferroelectric phase in ME composites due to their excellent piezoelectric characteristics. For the magnetic phase, high magnetostrictive materials such as cobalt ferrite are commonly used in these composites.

	In this work, as piezoelectric material, we used the solid solution of lead-iron niobate and lead titanate;0.94Pb(Fe$_{1/2}$Nb$_{1/2}$)O$_3$-0.06PbTiO$_3$(PFN-PT)\cite{sitalo2011dielectric}. There is a ferroelectric-paraelectric (F-P) phase transition at approximately 125°C for this compound with x=0.06 ( morphotropic phase boundary)\cite{SINGH2010}. It also has the highest dielectric constant and piezoelectric coefficient, d$_{33}$, among other concentrations\cite{sitalo2011dielectric}. Possessing a high d$_{33}$ makes it a suitable candidate for use in magnetoelectric composites as a piezoelectric phase(d$_{33}$=600 $\frac{pC}{N}$ for x=0.06)\cite{sitalo2011dielectric}. However, the ME effect in a particulate composite of PFN-PT with magnetostrictive materials has been rarely reported\cite{Mokhtari}. On the other hand, the magnetic properties of magnetostrictive materials can be controlled by doping them. In this research, we doped zinc elements into cobalt ferrite to tune its magnetostriction properties. This let us study the affect of manipulation
	of the magnetic phase on magnetoelectric coefficient.

	In essence, in this work we select PFN-PT as the ferroelectric phase and zinc-doped CoFe$_{2}$O$_{4}$ (CFZO) as the magnetic
	phase. The structural, dielectric, magnetic, and ME voltage coefficients (a complex quantity) are
	investigated for the composites with different contents of Zn in 0.6(PFN-PT)-0.4(CF$_{2-x}$Z$_{x}$O).

	\section{EXPERIMENTAL DETAILS}\label{Exp}
	The polycrystalline solid solution of 0.94Pb(Fe$_{1/2}$Nb$_{1/2}$)O$_3$-0.06PbTiO$_3$(PFN-PT) was synthesized using the solid-state reaction method.
	The high purity raw materials of PbO (with 4Wt$\%$ excess of PbO to compensate for lead volatility during the heat treatment), Fe$_2$O$_3$, Nb$_2$O$_5$, TiO$_2$, and one Wt$\%$ Li$_2$CO$_3$ (to make a better structure of the perovskite phase and reduce electrical conductivity) were blended and ground for 1.5 h by hand in an agate mortar. The obtained powder was calcined at 900 $^{\circ}$C for four hours, and then reground and annealed in the air in two stages, 1070 and 1100 $^{\circ}$C for 4 and 6 h, respectively.

	Co(NO$_3$)$_2$.6H$_2$O, Fe(NO$_3$)$_3$.9H$_2$O, Zn(NO$_3$)$_2$.6H$_2$O, C$_6$H$_8$O$_7$.H$_2$O, and deionized water were used to synthesize nanoparticles of  CoFe$_{2-x}$Zn$_x$O$_4$(x=0,0.25,0.1,0.2,0.3) using standard sol-gel method. Then the resultant powder was calcined at 800 $^{\circ}$C for four hours.

	Finally, the Zn-doped cobalt ferrite and PFN-PT were mixed to prepare (60Wt\%) PFN-PT - (40 Wt\%) CoFe$_{2-x}$Zn$_x$O$_4$ (x=0,0.25,0.1,0.2,0.3) particulate composites. The resultant powders were ground and prepared as pellets pressed at a pressure of 300 MPa and sintered at 800 $^{\circ}$C for four hours.

	The X-ray diffraction (XRD) patterns of the samples were measured at room temperature by using an Empyrean diffractometer with Cu - K$\alpha$ radiation. The microstructure of samples was analyzed using Field Emission Scanning Electron Microscopy (FE-SEM).
	Magnetization measurements of the composites were carried out by using a vibrating sample magnetometer (VSM) at room temperature. The relative permittivity of pure PFN-PT and other composites were measured at various frequencies (10 - 650 kHz) as a function of temperature using an LCR meter (IM3570 Hioki). Polarization-electric field (P-E) loops of the samples at room temperature were performed by using a homemade setup based on the Sawyer-Tower method.
	After polling the samples in an electric field of 10 kV/cm for one hour, the transverse magnetoelectric voltage coefficient was measured at room temperature by using the lock-in amplifier technique.

	\section{Results and discussion}
    The XRD patterns of all composites, as well as polycrystalline PFN-PT solid solution and cobalt ferrite (CFO) samples (for comparison), are shown in figure. \ref{jadidxrdall}. The XRD pattern of the composite shows the structures of perovskite and spinel associated with PFN-PT and CFO, respectively. No impurity phase is observed in the XRD pattern of sintered composites which means that no significant chemical reactions occurred between the grains of ferrite and ferroelectric during the sintering.

	Figure \ref{jadidfesem} shows the FE-SEM images of the sintered pellets of the pure PFN-PT (a), as well as all composite samples (b-f). It can be seen from the images that the samples consist of polygonal micrometer grains (related to the PFN-PT) and small CFO particles that are distributed in the shape of agglomerates inside the ferroelectric matrix. FE-SEM images exhibit that the ferrite particles are uniformly spread within the ferroelectric phase, which is suitable for achieving high magnetoelectric coupling.
	Figure \ref{jadidfesem} (g) shows the EDS mapping images of the sintered pellet of the sample PFN-PT/CoFe$_{1.7}$Zn$_{0.3}$O$_4$. The elements Pb, Nb, and Ti, are more prominent in areas of the main image where ferroelectric grains are present. On the other hand,  Co, Fe, and Zn elements are more distinguished in regions of the main image where there are tiny grains of ferrite.

	\begin{figure}[]
		\begin{center}
			\includegraphics[width=10cm,angle=0]{jadidxrdall}
			\caption{XRD patterns of (PFN-PT)-(CF$_{2-x}$Z$_{x}$O) composites (x=0, x=0.025, x=0.1, x=0.2, x=0.3) as well as pure PFN-PT and CFO.
				\label{jadidxrdall}}
		\end{center}
	\end{figure}

	\begin{figure}[]
		\begin{center}
			\includegraphics[width=9cm,angle=0]{jadidfesem}
			\caption{(a-f) FE-SEM images of the sintered pellets of the pure PFN-PT as well as  (PFN-PT)-(CF$_{2-x}$Z$_{x}$O) composites samples (with x=0, x=0.025, x=0.1, x=0.2, x=0.3). (g) EDS mapping images for the sample PFN-PT- CoFe$_{1.7}$Zn$_{0.3}$O$_4$ .
				\label{jadidfesem}}
		\end{center}
	\end{figure}

	Figure \ref{allepsilon}  illustrates the temperature dependence of relative permittivity ($\epsilon_r$) and dielectric loss tangent (tan$ \delta $) at four frequencies (10, 100, 300, 650 kHz) in the temperature range of 25 - 250 $^\circ$C for pure PFN-PT (a) and composites samples (b-f). The dielectric constant of samples increases with rising temperature and reaches its maximum at $ T_{m} $ before decreasing with further temperature increases. As clearly seen from figure. \ref{allepsilon} (a), the dielectric constant of pure PFN-PT has a peak at 124.5 $^{\circ}$C. At this temperature, the dielectric constant has its maximum value and a broad peak, related to a phase transition from high-temperature paraelectric (cubic structure) to the low-temperature ferroelectric phase (tetragonal structure). Figures \ref{allepsilon} (b-f) show that by adding the magnetic phase, the dielectric constant ($\epsilon_r$) decreases and the loss tangent (tan $ \delta $) increases. This is owing to the decreased resistance of the ferrite magnetic phase as opposed to PFN-PT. The peak of the paraelectric to ferroelectric transition is also found to be moved to higher temperatures. The interdiffusion of ions between the magnetic and ferroelectric phases during the sintering process is responsible for the shift in transition temperature \cite{lin2009dielectric,schileo2018multiferroic}. As shown in figure \ref{allepsilon} (a), $ T_{m} $ for PFN-PT is frequency independent, but it moves toward higher temperatures as frequency increases for composite samples (see figure \ref{allepsilon} (b-f)).

	At temperatures above the transition temperature, the real dielectric constant follows the modified Curie-Weiss equation.
	\begin{equation}
		\frac{1}{\epsilon^{\prime}}-\frac{1}{\epsilon_m^{\prime}}=\frac{(T-T_{m})^{\gamma}}{C_{1}}
		\label{gammaeq}
	\end{equation}

	where $\epsilon_m^{\prime}$ is the highest dielectric permittivity at the transition temperature, $C_{1}$ is the modified Curie-Weiss constant, and $\gamma$  is the slope of log(1/$\epsilon^{\prime}$-1/$\epsilon_m^{\prime}$) vs. log ($T-T_{m}$). The value of $\gamma$ indicates the ferroelectric's degree of relaxation. Its value is 1 for normal ferroelectrics, but for relaxor ferroelectrics, $\gamma$ ranges between 1 and 2,  whereas ($\gamma$= 2) indicates the entirely diffuse phase transition (1$\leq$ $\gamma$ $\leq$ 2) \cite{xi2015effect,jan2018study,usman2013magnetic}. The graphs of ln(1/$\epsilon^{\prime}$-1/$\epsilon_m^{\prime}$) vs. ln ($T-T_{m}$) at 10 kHz are shown in the insets of figure \ref{allepsilon} (b–e). When the experimental data are fitted to Equation \ref{gammaeq}, the values $\gamma$=1.63, 1.85, 1.86, 1.92,1.91 and 1.94 were obtained for PFN-PT, x=0, 0.025, 0.1, 0.2, and 0.3 respectively.These results, when compared to pure PFN-PT with a smaller gamma, demonstrate typical relaxor behavior in the composite samples. Because of composition fluctuations and structural disorder in the cationic configuration on the sites of the crystal structure, this behavior is linked to the emergence of polar nano regions (PNRs), which are responsible for this behavior\cite{jan2018study}.

	\begin{figure*}[]
		\begin{center}
			\includegraphics[width=16.75cm,angle=0]{allepsilon}
			\caption{Temperature dependence of relative permittivity ($\epsilon^{\prime}$) (solid lines) and the corresponding dielectric loss tangent (tan$ \delta $) (dashed lines) in frequency range of 10 to 650 kHz for (PFN-PT)-(CF$_{2-x}$Z$_{x}$O) composites samples with (a) x=0, (b) x=0.025, (c) x=0.1, (d)
				x=0.2, (e) x=0.3, as well as pure PFN-PT (f).Insets show fits of data above transition temperature to modified Curie-Weiss law.
				\label{allepsilon}}
		\end{center}
	\end{figure*}

	Figure \ref{allp-eloop} exhibits the ferroelectric hysteresis loops of all samples up to the electric field of 20 kV/cm at a frequency of 50 Hz. Pure PFN-PT shows a coercive field (E$_c$) of 3.75 kV/cm and remanent polarization (P$_r$)  of 16 $\mu \textrm{C/m$^2$}$. E$_c$ and P$_r$ for composite samples are plotted in the inset of figure \ref{allp-eloop} as a function of Zn content. According to the graph, introducing the non-ferroelectric phase of ferrite to the ferroelectric phase PFN-PT reduces remanent polarization while increasing the coercive field. It is also noted that as the electric field increases due to the increased conductivity and leakage current of the ferrite magnetic phase, the composite samples are not as well-saturated as the pure sample and the loops form becomes rounder. The E$_c$ value is nearly identical for all composite samples. A high E$_c$ indicates that a larger electric field is required to rotate the orientation of the electric domains and make the sample's total polarization zero. It is primarily due to porosity within the material and the space charges that generate electric domain wall pinning at ferrite and ferroelectric grain boundaries\cite{uchino2018ferroelectric,gupta2011improved,tyagi2015large}.

	Also, the quantity of remanent polarization in the composite samples varied according to the amount of zinc impurity in the magnetic phase. As the amount of zinc in the magnetic phase increases, the remanent polarization of the composite drops. According to the dielectric properties data, this decrease in polarization can be attributed to the higher conductivity of samples with  a higher zinc content. As conductivity increases due to electric leakage current, a lower quantity of surface charge accumulates on the electrodes, reducing electric polarization.

	\begin{figure}[]
		\begin{center}
			\includegraphics[width=9cm,angle=0]{allp-eloop}
			\caption{Room temperature polarization-electric field (P-E) loops of (PFN-PT)-(CF$_{2-x}$Z$_{x}$O) composites samples, as well as pure PFN-PT, measured at a frequency of 50 Hz. Inset shows the coercive field (Ec) and remnant polarization (Pr)
				as a function of Zn content.
				\label{allp-eloop}}
		\end{center}
	\end{figure}

	The magnetic hysteresis curves for all composite samples are shown in figure \ref{malekmhloop}. Because the PFN-PT is paramagnetic at ambient temperature, it contributes only a minor amount to the magnetic hysteresis curves, and the main contribution is related to zinc-doped cobalt ferrite. The saturation magnetization ($ M_{s} $) and coercive field ($ H_{c} $) value change with zinc impurity, as shown in the inset of figure \ref{malekmhloop}.

	For composite samples, the value of $ M_{s} $ grows and then drops. The value of $ M_{s} $ is determined by the distribution of zinc in the tetrahedral and octahedral sites. According to Neel's model, the net magnetization of spinel ferrites is equal to the difference in magnetizations in two sublattices $ A $ and $ B $, which represent the tetrahedral and octahedral sites, respectively. The $ Zn^{+2} $ ion preferentially occupies tetrahedral sites. Because the $ Zn^{+2} $ ion is non-magnetic and has no magnetic moment, by zn doping the magnetization value in sublattice $ A $ drops when compared to the magnetization value in sublattice $ B $, causing the net magnetization to increase. When the $ Zn $ content increases, some $ Zn^{+2} $ ions are placed in the octahedral site, causing magnetization to decrease further. The leading cause of the decrease in magnetization is the weakening of the superexchange interaction between the A and B sites, as well as the tilting of the moments\cite{singhal2010effect}.

	The $ H_{c} $ decreases with increasing zinc impurity in the iron site, as shown in the inset of figure \ref{malekmhloop}. The $ H_{c} $ in spinel ferrites is affected by parameters such as anisotropy constant, saturation magnetization, superexchange interactions, and lattice defects\cite{rao2013improved}. The  $ H_{c} $ is directly related to anisotropy. Anisotropy reduces as zinc impurity increases. As a result, the coercive field decreases. It is significant to mention that during the heating process in the furnace, atoms of ferroelectric and ferrimagnetic phases can penetrate each other, affecting the magnetic properties of ferrite.

	\begin{figure}[]
		\begin{center}
			\includegraphics[width=9cm,angle=0]{malekmhloop}
			\caption{Room temperature magnetization loops of (PFN-PT)-(CF$_{2-x}$Z$_{x}$O) composites. Inset (i) shows the coercive field (H$_c$) and saturation magnetization (M$_s$) as a function of Zn content. Inset (ii) shows a zoomed view of the m-h loop in the vicinity of the center.
				\label{malekmhloop}}
		\end{center}
	\end{figure}

	Magnetoelectric coupling in composites is primarily created by transmitted stress caused by magneto-mechanical interaction at the interface of the piezoelectric and magnetostrictive phases\cite{velev2011multi}. The magnetoelectric voltage coefficient is stated as a complex quantity\cite{Mokhtari}:

	\begin{equation}
		\alpha_{ME}^{\ast}=\alpha_{ME}e^{-i\varphi}=\alpha^{\prime}-i\alpha^{\prime\prime}
	\end{equation}

	where $\varphi$ is the phase shift between the driving current for the
	ac magnetic field and the output ME voltage from the sample. The real and imaginary parts of the magnetoelectric coefficient are represented by $\alpha^{\prime}$ and $\alpha^{\prime\prime}$, respectively. This phase shift results in the formation of an imaginary portion, which represents the presence of energy loss during the measurement of $\alpha_{ME}^{\ast}$ for ME composites. A detailed explanation of ME measurement is described in the supplemental material of Ref\cite{Mokhtari}.

	To explore the influence of zinc substitution on magnetoelectric characteristics, after polling samples up to the $10 \frac{kV}{cm}$, the complex magnetoelectric coefficient was evaluated for composites. Figure \ref{meallcfzo} reveals the real and imaginary parts of ME  voltage coefficient for the composites as a function of DC magnetic field ($H_{DC}$) from 0 to 8 kOe in a 0.77 Oe AC magnetic field (f=978 Hz).

	In the absence of a direct magnetic field ($H_{DC}$), the real part of the ME coefficient has a non-zero value ($\alpha_{self-biased}$ ) in all samples, which is the result of the interaction between the alternating magnetic field ($H_{AC}$) and remanent magnetization of the ferrite phase.
	As seen in the figures, the magnetoelectric coefficient grows nearly linearly with increasing magnetic field ($H_{DC}$) for all samples until a specific magnetic field ($H_{peak}$) reaches its maximum value ($\alpha_{max}$). The magnetoelectric coefficient then decreases as the magnetic field increases until it reaches zero in a specific magnetic field. As the field strength increases, the value of the real magnetoelectric part changes sign and becomes negative. The values of $\alpha_{self-biased}$, $\alpha_{max}$, and $H_{peak}$ for all composite samples are presented in table \ref{metable}.

	\begin{table}
		\begin{center}
			\begin{tabular}{|c|c|c|c|}
				\hline
				{sample name} & $\alpha_{{self-biased}}(\frac{mV}{cm.Oe})$ &  $\alpha_{{max}}(\frac{mV}{cm.Oe})$& ${H}_{{peak}}(Oe)$ \\	\hline
				$ x=0 $& 2.57 & 7.16&1465\\ \hline
				$ x=0.025 $& 2.38 & 8.09&1360\\ \hline
				$ x=0.1 $& 4.20 & 12.33&755\\ \hline
				$ x=0.2 $& 4.79 & 11.2&388\\ \hline
				$ x=0.3 $& 1.41 & 4.96 &249\\ \hline
			\end{tabular}\label{metable}
			\caption{The values of $\alpha_{self-biased}$, $\alpha_{max}$, and ${H}_{peak}$ for all composites.}

		\end{center}
	\end{table}

	 As shown in the figures, the values of $\alpha^{\prime}$ and ${H}_{peak}$ strongly depend on the zinc content in the cobalt ferrite magnetic phase. According to figure \ref{meallcfzo}, the value of $\alpha_{max}$ grows with increasing Zn content up to x = 0.1 and thereafter drops. Similar to coercivity, increasing Zn content causes ${H}_{peak}$ to shift toward lower fields. Sample x=0.1 has the optimal amount of Zn and the most robust magnetoelectric coupling.

	Another significant feature visible in the curves is hysteresis behavior between the increasing and decreasing branches of the $\alpha^{\prime}$. This hysteresis behavior reflects the magnetic hysteresis behavior. As shown in the pictures, as the Zn amount increases, the hysteresis curves become narrow, which is consistent with the magnetic hysteresis behavior of the samples.

	In general, the magnetoelectric voltage coefficient in composites depends on the magnetostriction ($\lambda$) and piezomagnetic coefficient $(\frac{\partial\lambda}{\partial M})$ of the magnetostrictive phase \cite{Agarwal2012,duong2007driving}. The ME effect is proven to be driven by dynamic piezomagnetic, $q^{ac}$, rather than quasi-static magnetostriction\cite{aubert2018dynamic}. $q^{ac}$ is described by:

	\begin{equation}
		q^{ac}=\frac{{\partial\lambda^{ac}}}{{\partial H_{ac}}}|H_{dc}
	\end{equation}

	Where $q^{ac}$ is the dynamic magnetostriction induced by the vibration of magnetic moments by $H_{ac}$ while applying a constant DC magnetic field\cite{aubert2018dynamic}. Because of dynamic magnetostriction in the magnetostrictive phase, $\alpha_{self-biased}$ appears in the samples. The self-biased ME is due to the magnetic hysteretic response of the piezomagnetic phase\cite{ahlawat2017electric}. As a result, even without a direct magnetic field, all samples exhibit $\alpha_{self-biased}$.

	The variation in magnetostriction behavior among the composites in the presence of a magnetic field accounts for the variance in magnetoelectric behavior. Many investigations have been published on the magnetostriction curves of pure cobalt ferrite and cobalt ferrite doped with zinc\cite{somaiah2012magnetic,nlebedim2014dependence,anantharamaiah2017tuning}. The magnetostriction of zn-doped cobalt ferrite increases initially and decreases with increasing magnetic field. The magnetostriction of a zn-doped cobalt ferrite polycrystal sample is a combination of $\lambda_{100}<0 $ and $\lambda_{111}>0 $, where $\lambda_{100}$ and $\lambda_{111}$ correspond to magnetostriction in the easy and hard magnetic directions, respectively. The dominant contribution of $\lambda_{100}$ drives the increasing magnetostriction behavior in low fields. In contrast, the decreasing behavior of magnetostriction in high fields is due to the higher contribution of $\lambda_{111}$\cite{nlebedim2010effect,atif2013influence,anantharamaiah2016enhancing}. As the amount of the zinc element in the iron sites increases, the peak value of the magnetostriction curve decreases. Zinc substitution in cobalt ferrite causes part of magnetization vectors to change their directions from the easy axis (100) to the hard axis (111). Less magnetocrystalline anisotropy is a consequence of these changes in the direction of the magnetization vectors, which is in agreement with the results of the magnetic hysteresis curves. It turns out that the Zn-substituted samples magnetostriction peak (x=0.025,0.1,0.2,0.3) occurs at lower magnetic fields than the sample without Zn (x=0)\cite{somaiah2012magnetic,anantharamaiah2017tuning}.

	The value of $\alpha^{\prime}$, as previously mentioned, is proportional to the strain sensitivity $(\frac{\partial\lambda}{\partial M})$. Indeed, the larger the slope of the magnetostriction curve versus the magnetic field, the larger the coupling coefficient. In this investigation, the sample with the highest magnetoelectric coupling is $X=0.1$. In  prior investigations, the strain sensitivity of ferrite $CoFe_{1.9}Zn_{0.1}O $ confirmed that this impurity had the highest strain sensitivity\cite{somaiah2012magnetic,anantharamaiah2017tuning}.

	In order to gain further insight, we can interpret the magnetic field dependency of $\alpha^{\prime}$ by using the $\lambda (H)$ trend. As was already discussed, $\lambda^{dc} $ tends to grow as the magnetic field increases. In the case of high fields, the behavior of $\alpha^{\prime}$  is controlled by the type of the magnetic phase and the percentage of zinc impurity. When the DC magnetic field is strong enough to rotate the magnetic domains (${H}_{{peak}}$), the ac magnetic field can cause the maximum length change in the magnetic phase, yielding the highest value of $\alpha^{\prime}$. With further increasing the magnetic field, the value of $\alpha^{\prime}$ becomes zero $(\frac{\partial\lambda}{\partial H}=0)$ and then the sign of $\alpha^{\prime}$ changes from positive to negative, which is due to the negative sign of $(\frac{\partial\lambda}{\partial H})$ for zinc-doped cobalt ferrite \cite{somaiah2012magnetic,anantharamaiah2017tuning}. There have rarely been reports on negative ME voltage coefficients\cite{etier2013magnetoelectric,naveed2017effect,srinivasan2005dynamic}.

	Figure \ref{meallcfzo} also includes the samples' imaginary part of the ME coefficient ($\alpha^{\prime\prime}$). ME responses have rarely been studied in terms of their imaginary part\cite{Zhou2008,zhai2007large,guo2013frequency}. The imaginary part of the ME coefficient represents the energy dissipation in the system. As can be seen from the figure, the $\alpha^{\prime\prime}$ has a peak close to the ${H}_{{peak}}$. As mentioned earlier, $\alpha_{max}$ is obtained when the magnetic domains collectively rotate, producing the highest energy dissipation in the magnetic phase. It implies that the peak of $\alpha^{\prime\prime}$ should occur in the vicinity of  ${H}_{peak}$, where the peak of the real part occurs. This is true for all samples, as evidenced by the curves.

	\begin{figure}[]
		\begin{center}
			\includegraphics[width=9cm,angle=0]{meallcfzo}
			\caption{Real and imaginary part of transverse ME voltage coefficient ($\alpha^*_{31}$) as a function of DC magnetic field for (PFN-PT)-(CF$_{2-x}$Z$_{x}$O) composites (x=0, x=0.025, x=0.1, x=0.2, x=0.3), h$_{ac}$=0.77 Oe, and f=978 Hz.
				\label{meallcfzo}}
		\end{center}
	\end{figure}

	\section{Conclusion}

	To sum up, the composite 0.94PbFe$_{0.5}$Nb$_{0.5}$O$_{3}$-0.06PbTiO$_{3}$ and CoFe$_{2-x}$Zn$_{x}$O$_{4}$  were prepared for  x=0, 0.025, 0.1, 0.2, 0.3 and a weight percentage of 60-40 (60 percent ferroelectric and 40 percent ferrite). The XRD characterization revealed the formation of perovskite and spinel structures for ferroelectric and ferrite phases, respectively. In addition, FE-SEM and EDS mapping images revealed a homogeneous and suitable distribution of the magnetic phase within the ferroelectric matrix. The ferroelectric to paraelectric phase transition occurs at 124.5°C in the dielectric constant curve for the pure PFN-PT. The dielectric constant is reduced by adding the ferrite phase. The electric hysteresis loop for the pure PFN-PT is well-saturated in the $ 20\frac{kV}{cm} $ field. The remanent polarization is reduced by including the non-ferroelectric ferrite phase.
	Furthermore, the value of the coercive field increases with the addition of ferrite, which is caused by the domain wall pinning. The magnetic hysteresis curves revealed that the coercive field value reduces as the zinc impurity increases. For each composite, the real and imaginary parts of the magnetoelectric coefficient were measured. All the composite samples possess $\alpha_{self-biased}$. The highest ME voltage coefficient value of 12.33 $\frac{mV}{cm.Oe}$ at DC magnetic field of 755 Oe was achieved for x = 0.1 sample. The measurements revealed that the magnetoelectric coefficient is highly dependent on the zinc content. In fact, with the substitution of the zinc in the iron sites, the strain value ($\lambda(H)$) and strain sensitivity $(\frac{\partial\lambda}{\partial H})$ of ferrite vary, and consequently, the value of the magnetoelectric coefficient changes based on these two parameters.

	\section{Acknowledgement}
	The Isfahan University of Technology supported this work
	(IUT).

	\section*{References}

\section{INTRODUCTION}\label{Int}
	Multiferroics are a class of materials that have at least two ferroic orders (ferroelectric, magnetic, and elastic). Magnetoelectric (ME) materials are a subset of multiferroics in which ferroelectric and magnetic orders are coupled. The ME materials are classified into single-phase and composite groups in which composites show higher ME coupling values than single-phase ones\cite{spaldin2019advances,HansSchmid1994,palneedi2016status,Spaldin391,hadi,Feibeg,Kimura,eerenstein2006w}. Since in this class of materials magnetization (polarization) can be controlled by an/a electric field (magnetic field), they can be used in both electrical and magnetic areas, and have a wide range of applications, including magnetic field sensors, spintronics, data storage, actuators, photovoltaic solar cells, etc\cite{bibes2008towards,vopson2015fundamentals,Maignan,olabi2008design}.

	The ME voltage in composite magnetoelectric materials is generated by polarization change in the piezoelectric phase as a result of dynamic mechanical deformation of the magnetostrictive phase induced by the applied ac magnetic field in the presence of the dc magnetic field. In addition, the ME coupling coefficient is affected by magnetostriction and piezoelectric behavior of magnetic and electric phases, respectively. As a result, significant magnetostriction and piezoelectric coefficients are essential for obtaining a high ME voltage coefficient.

	Many studies have been conducted on piezoelectric-ferrite composites like:
	(BiBa)(FeTiZn)O$_{3}$/CoFe$_{2}$O$_{4}$\cite{papi2021dielectric}, PFN-PT/(Co,Ni)Fe$_{2}$O$_{4}$\cite{Mokhtari}, PMN-PT/CoFe$_{2}$O$_4$\cite{zabotto2020magnetodielectric}  BaTiO$_3$/CoFe$_{2}$O$_4$\cite{verma2019magnetic,etier2016direct}, PMN-PT/NiFe$_{2}$O$_4$\cite{ahlawat2013evidence}, PZT/Ni$_{0.2}$Co$_{0.8}$Fe$_{2}$O$_4$\cite{bammannavar2009magnetic},
	PZT/CoFe$_{2}$O$_4$\cite{atif2015interplay}, PVDF/CoFe$_{2}$O$_4$\cite{gonccalves2015development}, and etc.
	Among them, Pb-based ferroelectrics, such as PZT and  PMN-PT, have been frequently utilized as the ferroelectric phase in ME composites due to their excellent piezoelectric characteristics. For the magnetic phase, high magnetostrictive materials such as cobalt ferrite are commonly used in these composites.

	In this work, as piezoelectric material, we used the solid solution of lead-iron niobate and lead titanate;0.94Pb(Fe$_{1/2}$Nb$_{1/2}$)O$_3$-0.06PbTiO$_3$(PFN-PT)\cite{sitalo2011dielectric}. There is a ferroelectric-paraelectric (F-P) phase transition at approximately 125°C for this compound with x=0.06 ( morphotropic phase boundary)\cite{SINGH2010}. It also has the highest dielectric constant and piezoelectric coefficient, d$_{33}$, among other concentrations\cite{sitalo2011dielectric}. Possessing a high d$_{33}$ makes it a suitable candidate for use in magnetoelectric composites as a piezoelectric phase(d$_{33}$=600 $\frac{pC}{N}$ for x=0.06)\cite{sitalo2011dielectric}. However, the ME effect in a particulate composite of PFN-PT with magnetostrictive materials has been rarely reported\cite{Mokhtari}. On the other hand, the magnetic properties of magnetostrictive materials can be controlled by doping them. In this research, we doped zinc elements into cobalt ferrite to tune its magnetostriction properties. This let us study the affect of manipulation
	of the magnetic phase on magnetoelectric coefficient.

	In essence, in this work we select PFN-PT as the ferroelectric phase and zinc-doped CoFe$_{2}$O$_{4}$ (CFZO) as the magnetic
	phase. The structural, dielectric, magnetic, and ME voltage coefficients (a complex quantity) are
	investigated for the composites with different contents of Zn in 0.6(PFN-PT)-0.4(CF$_{2-x}$Z$_{x}$O).

	\section{EXPERIMENTAL DETAILS}\label{Exp}
	The polycrystalline solid solution of 0.94Pb(Fe$_{1/2}$Nb$_{1/2}$)O$_3$-0.06PbTiO$_3$(PFN-PT) was synthesized using the solid-state reaction method.
	The high purity raw materials of PbO (with 4Wt$\%$ excess of PbO to compensate for lead volatility during the heat treatment), Fe$_2$O$_3$, Nb$_2$O$_5$, TiO$_2$, and one Wt$\%$ Li$_2$CO$_3$ (to make a better structure of the perovskite phase and reduce electrical conductivity) were blended and ground for 1.5 h by hand in an agate mortar. The obtained powder was calcined at 900 $^{\circ}$C for four hours, and then reground and annealed in the air in two stages, 1070 and 1100 $^{\circ}$C for 4 and 6 h, respectively.

	Co(NO$_3$)$_2$.6H$_2$O, Fe(NO$_3$)$_3$.9H$_2$O, Zn(NO$_3$)$_2$.6H$_2$O, C$_6$H$_8$O$_7$.H$_2$O, and deionized water were used to synthesize nanoparticles of  CoFe$_{2-x}$Zn$_x$O$_4$(x=0,0.25,0.1,0.2,0.3) using standard sol-gel method. Then the resultant powder was calcined at 800 $^{\circ}$C for four hours.

	Finally, the Zn-doped cobalt ferrite and PFN-PT were mixed to prepare (60Wt\%) PFN-PT - (40 Wt\%) CoFe$_{2-x}$Zn$_x$O$_4$ (x=0,0.25,0.1,0.2,0.3) particulate composites. The resultant powders were ground and prepared as pellets pressed at a pressure of 300 MPa and sintered at 800 $^{\circ}$C for four hours.

	The X-ray diffraction (XRD) patterns of the samples were measured at room temperature by using an Empyrean diffractometer with Cu - K$\alpha$ radiation. The microstructure of samples was analyzed using Field Emission Scanning Electron Microscopy (FE-SEM).
	Magnetization measurements of the composites were carried out by using a vibrating sample magnetometer (VSM) at room temperature. The relative permittivity of pure PFN-PT and other composites were measured at various frequencies (10 - 650 kHz) as a function of temperature using an LCR meter (IM3570 Hioki). Polarization-electric field (P-E) loops of the samples at room temperature were performed by using a homemade setup based on the Sawyer-Tower method.
	After polling the samples in an electric field of 10 kV/cm for one hour, the transverse magnetoelectric voltage coefficient was measured at room temperature by using the lock-in amplifier technique.

	\section{Results and discussion}
    The XRD patterns of all composites, as well as polycrystalline PFN-PT solid solution and cobalt ferrite (CFO) samples (for comparison), are shown in figure. \ref{jadidxrdall}. The XRD pattern of the composite shows the structures of perovskite and spinel associated with PFN-PT and CFO, respectively. No impurity phase is observed in the XRD pattern of sintered composites which means that no significant chemical reactions occurred between the grains of ferrite and ferroelectric during the sintering.

	Figure \ref{jadidfesem} shows the FE-SEM images of the sintered pellets of the pure PFN-PT (a), as well as all composite samples (b-f). It can be seen from the images that the samples consist of polygonal micrometer grains (related to the PFN-PT) and small CFO particles that are distributed in the shape of agglomerates inside the ferroelectric matrix. FE-SEM images exhibit that the ferrite particles are uniformly spread within the ferroelectric phase, which is suitable for achieving high magnetoelectric coupling.
	Figure \ref{jadidfesem} (g) shows the EDS mapping images of the sintered pellet of the sample PFN-PT/CoFe$_{1.7}$Zn$_{0.3}$O$_4$. The elements Pb, Nb, and Ti, are more prominent in areas of the main image where ferroelectric grains are present. On the other hand,  Co, Fe, and Zn elements are more distinguished in regions of the main image where there are tiny grains of ferrite.

	\begin{figure}[]
		\begin{center}
			\includegraphics[width=10cm,angle=0]{jadidxrdall}
			\caption{XRD patterns of (PFN-PT)-(CF$_{2-x}$Z$_{x}$O) composites (x=0, x=0.025, x=0.1, x=0.2, x=0.3) as well as pure PFN-PT and CFO.
				\label{jadidxrdall}}
		\end{center}
	\end{figure}

	\begin{figure}[]
		\begin{center}
			\includegraphics[width=9cm,angle=0]{jadidfesem}
			\caption{(a-f) FE-SEM images of the sintered pellets of the pure PFN-PT as well as  (PFN-PT)-(CF$_{2-x}$Z$_{x}$O) composites samples (with x=0, x=0.025, x=0.1, x=0.2, x=0.3). (g) EDS mapping images for the sample PFN-PT- CoFe$_{1.7}$Zn$_{0.3}$O$_4$ .
				\label{jadidfesem}}
		\end{center}
	\end{figure}

	Figure \ref{allepsilon}  illustrates the temperature dependence of relative permittivity ($\epsilon_r$) and dielectric loss tangent (tan$ \delta $) at four frequencies (10, 100, 300, 650 kHz) in the temperature range of 25 - 250 $^\circ$C for pure PFN-PT (a) and composites samples (b-f). The dielectric constant of samples increases with rising temperature and reaches its maximum at $ T_{m} $ before decreasing with further temperature increases. As clearly seen from figure. \ref{allepsilon} (a), the dielectric constant of pure PFN-PT has a peak at 124.5 $^{\circ}$C. At this temperature, the dielectric constant has its maximum value and a broad peak, related to a phase transition from high-temperature paraelectric (cubic structure) to the low-temperature ferroelectric phase (tetragonal structure). Figures \ref{allepsilon} (b-f) show that by adding the magnetic phase, the dielectric constant ($\epsilon_r$) decreases and the loss tangent (tan $ \delta $) increases. This is owing to the decreased resistance of the ferrite magnetic phase as opposed to PFN-PT. The peak of the paraelectric to ferroelectric transition is also found to be moved to higher temperatures. The interdiffusion of ions between the magnetic and ferroelectric phases during the sintering process is responsible for the shift in transition temperature \cite{lin2009dielectric,schileo2018multiferroic}. As shown in figure \ref{allepsilon} (a), $ T_{m} $ for PFN-PT is frequency independent, but it moves toward higher temperatures as frequency increases for composite samples (see figure \ref{allepsilon} (b-f)).

	At temperatures above the transition temperature, the real dielectric constant follows the modified Curie-Weiss equation.
	\begin{equation}
		\frac{1}{\epsilon^{\prime}}-\frac{1}{\epsilon_m^{\prime}}=\frac{(T-T_{m})^{\gamma}}{C_{1}}
		\label{gammaeq}
	\end{equation}

	where $\epsilon_m^{\prime}$ is the highest dielectric permittivity at the transition temperature, $C_{1}$ is the modified Curie-Weiss constant, and $\gamma$  is the slope of log(1/$\epsilon^{\prime}$-1/$\epsilon_m^{\prime}$) vs. log ($T-T_{m}$). The value of $\gamma$ indicates the ferroelectric's degree of relaxation. Its value is 1 for normal ferroelectrics, but for relaxor ferroelectrics, $\gamma$ ranges between 1 and 2,  whereas ($\gamma$= 2) indicates the entirely diffuse phase transition (1$\leq$ $\gamma$ $\leq$ 2) \cite{xi2015effect,jan2018study,usman2013magnetic}. The graphs of ln(1/$\epsilon^{\prime}$-1/$\epsilon_m^{\prime}$) vs. ln ($T-T_{m}$) at 10 kHz are shown in the insets of figure \ref{allepsilon} (b–e). When the experimental data are fitted to Equation \ref{gammaeq}, the values $\gamma$=1.63, 1.85, 1.86, 1.92,1.91 and 1.94 were obtained for PFN-PT, x=0, 0.025, 0.1, 0.2, and 0.3 respectively.These results, when compared to pure PFN-PT with a smaller gamma, demonstrate typical relaxor behavior in the composite samples. Because of composition fluctuations and structural disorder in the cationic configuration on the sites of the crystal structure, this behavior is linked to the emergence of polar nano regions (PNRs), which are responsible for this behavior\cite{jan2018study}.

	\begin{figure*}[]
		\begin{center}
			\includegraphics[width=16.75cm,angle=0]{allepsilon}
			\caption{Temperature dependence of relative permittivity ($\epsilon^{\prime}$) (solid lines) and the corresponding dielectric loss tangent (tan$ \delta $) (dashed lines) in frequency range of 10 to 650 kHz for (PFN-PT)-(CF$_{2-x}$Z$_{x}$O) composites samples with (a) x=0, (b) x=0.025, (c) x=0.1, (d)
				x=0.2, (e) x=0.3, as well as pure PFN-PT (f).Insets show fits of data above transition temperature to modified Curie-Weiss law.
				\label{allepsilon}}
		\end{center}
	\end{figure*}

	Figure \ref{allp-eloop} exhibits the ferroelectric hysteresis loops of all samples up to the electric field of 20 kV/cm at a frequency of 50 Hz. Pure PFN-PT shows a coercive field (E$_c$) of 3.75 kV/cm and remanent polarization (P$_r$)  of 16 $\mu \textrm{C/m$^2$}$. E$_c$ and P$_r$ for composite samples are plotted in the inset of figure \ref{allp-eloop} as a function of Zn content. According to the graph, introducing the non-ferroelectric phase of ferrite to the ferroelectric phase PFN-PT reduces remanent polarization while increasing the coercive field. It is also noted that as the electric field increases due to the increased conductivity and leakage current of the ferrite magnetic phase, the composite samples are not as well-saturated as the pure sample and the loops form becomes rounder. The E$_c$ value is nearly identical for all composite samples. A high E$_c$ indicates that a larger electric field is required to rotate the orientation of the electric domains and make the sample's total polarization zero. It is primarily due to porosity within the material and the space charges that generate electric domain wall pinning at ferrite and ferroelectric grain boundaries\cite{uchino2018ferroelectric,gupta2011improved,tyagi2015large}.

	Also, the quantity of remanent polarization in the composite samples varied according to the amount of zinc impurity in the magnetic phase. As the amount of zinc in the magnetic phase increases, the remanent polarization of the composite drops. According to the dielectric properties data, this decrease in polarization can be attributed to the higher conductivity of samples with  a higher zinc content. As conductivity increases due to electric leakage current, a lower quantity of surface charge accumulates on the electrodes, reducing electric polarization.

	\begin{figure}[]
		\begin{center}
			\includegraphics[width=9cm,angle=0]{allp-eloop}
			\caption{Room temperature polarization-electric field (P-E) loops of (PFN-PT)-(CF$_{2-x}$Z$_{x}$O) composites samples, as well as pure PFN-PT, measured at a frequency of 50 Hz. Inset shows the coercive field (Ec) and remnant polarization (Pr)
				as a function of Zn content.
				\label{allp-eloop}}
		\end{center}
	\end{figure}

	The magnetic hysteresis curves for all composite samples are shown in figure \ref{malekmhloop}. Because the PFN-PT is paramagnetic at ambient temperature, it contributes only a minor amount to the magnetic hysteresis curves, and the main contribution is related to zinc-doped cobalt ferrite. The saturation magnetization ($ M_{s} $) and coercive field ($ H_{c} $) value change with zinc impurity, as shown in the inset of figure \ref{malekmhloop}.

	For composite samples, the value of $ M_{s} $ grows and then drops. The value of $ M_{s} $ is determined by the distribution of zinc in the tetrahedral and octahedral sites. According to Neel's model, the net magnetization of spinel ferrites is equal to the difference in magnetizations in two sublattices $ A $ and $ B $, which represent the tetrahedral and octahedral sites, respectively. The $ Zn^{+2} $ ion preferentially occupies tetrahedral sites. Because the $ Zn^{+2} $ ion is non-magnetic and has no magnetic moment, by zn doping the magnetization value in sublattice $ A $ drops when compared to the magnetization value in sublattice $ B $, causing the net magnetization to increase. When the $ Zn $ content increases, some $ Zn^{+2} $ ions are placed in the octahedral site, causing magnetization to decrease further. The leading cause of the decrease in magnetization is the weakening of the superexchange interaction between the A and B sites, as well as the tilting of the moments\cite{singhal2010effect}.

	The $ H_{c} $ decreases with increasing zinc impurity in the iron site, as shown in the inset of figure \ref{malekmhloop}. The $ H_{c} $ in spinel ferrites is affected by parameters such as anisotropy constant, saturation magnetization, superexchange interactions, and lattice defects\cite{rao2013improved}. The  $ H_{c} $ is directly related to anisotropy. Anisotropy reduces as zinc impurity increases. As a result, the coercive field decreases. It is significant to mention that during the heating process in the furnace, atoms of ferroelectric and ferrimagnetic phases can penetrate each other, affecting the magnetic properties of ferrite.

	\begin{figure}[]
		\begin{center}
			\includegraphics[width=9cm,angle=0]{malekmhloop}
			\caption{Room temperature magnetization loops of (PFN-PT)-(CF$_{2-x}$Z$_{x}$O) composites. Inset (i) shows the coercive field (H$_c$) and saturation magnetization (M$_s$) as a function of Zn content. Inset (ii) shows a zoomed view of the m-h loop in the vicinity of the center.
				\label{malekmhloop}}
		\end{center}
	\end{figure}

	Magnetoelectric coupling in composites is primarily created by transmitted stress caused by magneto-mechanical interaction at the interface of the piezoelectric and magnetostrictive phases\cite{velev2011multi}. The magnetoelectric voltage coefficient is stated as a complex quantity\cite{Mokhtari}:

	\begin{equation}
		\alpha_{ME}^{\ast}=\alpha_{ME}e^{-i\varphi}=\alpha^{\prime}-i\alpha^{\prime\prime}
	\end{equation}

	where $\varphi$ is the phase shift between the driving current for the
	ac magnetic field and the output ME voltage from the sample. The real and imaginary parts of the magnetoelectric coefficient are represented by $\alpha^{\prime}$ and $\alpha^{\prime\prime}$, respectively. This phase shift results in the formation of an imaginary portion, which represents the presence of energy loss during the measurement of $\alpha_{ME}^{\ast}$ for ME composites. A detailed explanation of ME measurement is described in the supplemental material of Ref\cite{Mokhtari}.

	To explore the influence of zinc substitution on magnetoelectric characteristics, after polling samples up to the $10 \frac{kV}{cm}$, the complex magnetoelectric coefficient was evaluated for composites. Figure \ref{meallcfzo} reveals the real and imaginary parts of ME  voltage coefficient for the composites as a function of DC magnetic field ($H_{DC}$) from 0 to 8 kOe in a 0.77 Oe AC magnetic field (f=978 Hz).

	In the absence of a direct magnetic field ($H_{DC}$), the real part of the ME coefficient has a non-zero value ($\alpha_{self-biased}$ ) in all samples, which is the result of the interaction between the alternating magnetic field ($H_{AC}$) and remanent magnetization of the ferrite phase.
	As seen in the figures, the magnetoelectric coefficient grows nearly linearly with increasing magnetic field ($H_{DC}$) for all samples until a specific magnetic field ($H_{peak}$) reaches its maximum value ($\alpha_{max}$). The magnetoelectric coefficient then decreases as the magnetic field increases until it reaches zero in a specific magnetic field. As the field strength increases, the value of the real magnetoelectric part changes sign and becomes negative. The values of $\alpha_{self-biased}$, $\alpha_{max}$, and $H_{peak}$ for all composite samples are presented in table \ref{metable}.

	\begin{table}
		\begin{center}
			\begin{tabular}{|c|c|c|c|}
				\hline
				{sample name} & $\alpha_{{self-biased}}(\frac{mV}{cm.Oe})$ &  $\alpha_{{max}}(\frac{mV}{cm.Oe})$& ${H}_{{peak}}(Oe)$ \\	\hline
				$ x=0 $& 2.57 & 7.16&1465\\ \hline
				$ x=0.025 $& 2.38 & 8.09&1360\\ \hline
				$ x=0.1 $& 4.20 & 12.33&755\\ \hline
				$ x=0.2 $& 4.79 & 11.2&388\\ \hline
				$ x=0.3 $& 1.41 & 4.96 &249\\ \hline
			\end{tabular}\label{metable}
			\caption{The values of $\alpha_{self-biased}$, $\alpha_{max}$, and ${H}_{peak}$ for all composites.}

		\end{center}
	\end{table}

	 As shown in the figures, the values of $\alpha^{\prime}$ and ${H}_{peak}$ strongly depend on the zinc content in the cobalt ferrite magnetic phase. According to figure \ref{meallcfzo}, the value of $\alpha_{max}$ grows with increasing Zn content up to x = 0.1 and thereafter drops. Similar to coercivity, increasing Zn content causes ${H}_{peak}$ to shift toward lower fields. Sample x=0.1 has the optimal amount of Zn and the most robust magnetoelectric coupling.

	Another significant feature visible in the curves is hysteresis behavior between the increasing and decreasing branches of the $\alpha^{\prime}$. This hysteresis behavior reflects the magnetic hysteresis behavior. As shown in the pictures, as the Zn amount increases, the hysteresis curves become narrow, which is consistent with the magnetic hysteresis behavior of the samples.

	In general, the magnetoelectric voltage coefficient in composites depends on the magnetostriction ($\lambda$) and piezomagnetic coefficient $(\frac{\partial\lambda}{\partial M})$ of the magnetostrictive phase \cite{Agarwal2012,duong2007driving}. The ME effect is proven to be driven by dynamic piezomagnetic, $q^{ac}$, rather than quasi-static magnetostriction\cite{aubert2018dynamic}. $q^{ac}$ is described by:

	\begin{equation}
		q^{ac}=\frac{{\partial\lambda^{ac}}}{{\partial H_{ac}}}|H_{dc}
	\end{equation}

	Where $q^{ac}$ is the dynamic magnetostriction induced by the vibration of magnetic moments by $H_{ac}$ while applying a constant DC magnetic field\cite{aubert2018dynamic}. Because of dynamic magnetostriction in the magnetostrictive phase, $\alpha_{self-biased}$ appears in the samples. The self-biased ME is due to the magnetic hysteretic response of the piezomagnetic phase\cite{ahlawat2017electric}. As a result, even without a direct magnetic field, all samples exhibit $\alpha_{self-biased}$.

	The variation in magnetostriction behavior among the composites in the presence of a magnetic field accounts for the variance in magnetoelectric behavior. Many investigations have been published on the magnetostriction curves of pure cobalt ferrite and cobalt ferrite doped with zinc\cite{somaiah2012magnetic,nlebedim2014dependence,anantharamaiah2017tuning}. The magnetostriction of zn-doped cobalt ferrite increases initially and decreases with increasing magnetic field. The magnetostriction of a zn-doped cobalt ferrite polycrystal sample is a combination of $\lambda_{100}<0 $ and $\lambda_{111}>0 $, where $\lambda_{100}$ and $\lambda_{111}$ correspond to magnetostriction in the easy and hard magnetic directions, respectively. The dominant contribution of $\lambda_{100}$ drives the increasing magnetostriction behavior in low fields. In contrast, the decreasing behavior of magnetostriction in high fields is due to the higher contribution of $\lambda_{111}$\cite{nlebedim2010effect,atif2013influence,anantharamaiah2016enhancing}. As the amount of the zinc element in the iron sites increases, the peak value of the magnetostriction curve decreases. Zinc substitution in cobalt ferrite causes part of magnetization vectors to change their directions from the easy axis (100) to the hard axis (111). Less magnetocrystalline anisotropy is a consequence of these changes in the direction of the magnetization vectors, which is in agreement with the results of the magnetic hysteresis curves. It turns out that the Zn-substituted samples magnetostriction peak (x=0.025,0.1,0.2,0.3) occurs at lower magnetic fields than the sample without Zn (x=0)\cite{somaiah2012magnetic,anantharamaiah2017tuning}.

	The value of $\alpha^{\prime}$, as previously mentioned, is proportional to the strain sensitivity $(\frac{\partial\lambda}{\partial M})$. Indeed, the larger the slope of the magnetostriction curve versus the magnetic field, the larger the coupling coefficient. In this investigation, the sample with the highest magnetoelectric coupling is $X=0.1$. In  prior investigations, the strain sensitivity of ferrite $CoFe_{1.9}Zn_{0.1}O $ confirmed that this impurity had the highest strain sensitivity\cite{somaiah2012magnetic,anantharamaiah2017tuning}.

	In order to gain further insight, we can interpret the magnetic field dependency of $\alpha^{\prime}$ by using the $\lambda (H)$ trend. As was already discussed, $\lambda^{dc} $ tends to grow as the magnetic field increases. In the case of high fields, the behavior of $\alpha^{\prime}$  is controlled by the type of the magnetic phase and the percentage of zinc impurity. When the DC magnetic field is strong enough to rotate the magnetic domains (${H}_{{peak}}$), the ac magnetic field can cause the maximum length change in the magnetic phase, yielding the highest value of $\alpha^{\prime}$. With further increasing the magnetic field, the value of $\alpha^{\prime}$ becomes zero $(\frac{\partial\lambda}{\partial H}=0)$ and then the sign of $\alpha^{\prime}$ changes from positive to negative, which is due to the negative sign of $(\frac{\partial\lambda}{\partial H})$ for zinc-doped cobalt ferrite \cite{somaiah2012magnetic,anantharamaiah2017tuning}. There have rarely been reports on negative ME voltage coefficients\cite{etier2013magnetoelectric,naveed2017effect,srinivasan2005dynamic}.

	Figure \ref{meallcfzo} also includes the samples' imaginary part of the ME coefficient ($\alpha^{\prime\prime}$). ME responses have rarely been studied in terms of their imaginary part\cite{Zhou2008,zhai2007large,guo2013frequency}. The imaginary part of the ME coefficient represents the energy dissipation in the system. As can be seen from the figure, the $\alpha^{\prime\prime}$ has a peak close to the ${H}_{{peak}}$. As mentioned earlier, $\alpha_{max}$ is obtained when the magnetic domains collectively rotate, producing the highest energy dissipation in the magnetic phase. It implies that the peak of $\alpha^{\prime\prime}$ should occur in the vicinity of  ${H}_{peak}$, where the peak of the real part occurs. This is true for all samples, as evidenced by the curves.

	\begin{figure}[]
		\begin{center}
			\includegraphics[width=9cm,angle=0]{meallcfzo}
			\caption{Real and imaginary part of transverse ME voltage coefficient ($\alpha^*_{31}$) as a function of DC magnetic field for (PFN-PT)-(CF$_{2-x}$Z$_{x}$O) composites (x=0, x=0.025, x=0.1, x=0.2, x=0.3), h$_{ac}$=0.77 Oe, and f=978 Hz.
				\label{meallcfzo}}
		\end{center}
	\end{figure}

	\section{Conclusion}

	To sum up, the composite 0.94PbFe$_{0.5}$Nb$_{0.5}$O$_{3}$-0.06PbTiO$_{3}$ and CoFe$_{2-x}$Zn$_{x}$O$_{4}$  were prepared for  x=0, 0.025, 0.1, 0.2, 0.3 and a weight percentage of 60-40 (60 percent ferroelectric and 40 percent ferrite). The XRD characterization revealed the formation of perovskite and spinel structures for ferroelectric and ferrite phases, respectively. In addition, FE-SEM and EDS mapping images revealed a homogeneous and suitable distribution of the magnetic phase within the ferroelectric matrix. The ferroelectric to paraelectric phase transition occurs at 124.5°C in the dielectric constant curve for the pure PFN-PT. The dielectric constant is reduced by adding the ferrite phase. The electric hysteresis loop for the pure PFN-PT is well-saturated in the $ 20\frac{kV}{cm} $ field. The remanent polarization is reduced by including the non-ferroelectric ferrite phase.
	Furthermore, the value of the coercive field increases with the addition of ferrite, which is caused by the domain wall pinning. The magnetic hysteresis curves revealed that the coercive field value reduces as the zinc impurity increases. For each composite, the real and imaginary parts of the magnetoelectric coefficient were measured. All the composite samples possess $\alpha_{self-biased}$. The highest ME voltage coefficient value of 12.33 $\frac{mV}{cm.Oe}$ at DC magnetic field of 755 Oe was achieved for x = 0.1 sample. The measurements revealed that the magnetoelectric coefficient is highly dependent on the zinc content. In fact, with the substitution of the zinc in the iron sites, the strain value ($\lambda(H)$) and strain sensitivity $(\frac{\partial\lambda}{\partial H})$ of ferrite vary, and consequently, the value of the magnetoelectric coefficient changes based on these two parameters.

	\section{Acknowledgement}
	The Isfahan University of Technology supported this work
	(IUT).

	\section*{References}

redpajama_set_name: RedPajamaArXiv


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text:
What Facebucks Can Do for the Global Poor
Facebook's Libra would be free to use and free to roam, changing hands and crossing borders costlessly or nearly costlessly.
Annie Lowrey
Dado Ruvic / Reuters
This month, Facebook announced it was making an investment in crypto. More specifically, the company and its partners issued a long-anticipated white paper unveiling a new digital currency, a management mechanism for it, and a platform for its development. It is called Libra, a kind of half pun: The name refers to an ancient unit of measure, as well as sounding like the French and Spanish word for "free."
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Eric Posner: The trouble starts if Facebook's new currency succeeds
The central way that Libra wants to help the bottom billion is by providing cheap or free money transfers, something the world's aid groups, treasuries, central banks, and development economists all believe is an urgent goal. Remittances—when one person sends money to a person in another country, stereotypically meaning an immigrant sending money home—are an unheralded but powerful economic force. They total half a trillion dollars a year, with two-thirds of that money heading to the developing world. Already remittances are three times as large as official development aid.
But they are expensive and sometimes difficult to send, limiting their scope. Money going from, say, Toronto to a small town outside Conakry, Guinea, needs to pass through an invisible network of financial institutions, all regulated by any number of national and international bodies. That costs money. According to the World Bank, remittance processors charge a 7 percent margin, on average. Cutting remittance prices by five percentage points would save nearly $20 billion year, meaning $20 billion more for recipients.
Cryptocurrencies, like the one Facebook and its partners are building, could send this number to zero. There would be no series of global banking institutions thirsting for a cut. There would be no need for the sender or recipient to go to a brick-and-mortar bank or Western Union. There would be no need for either side of the transaction to have a bank account, or formal identification either. "No one can be denied access for any reason, whether that is lack of identifying documentation, insufficient of funds or credit, or even outright discrimination," Jerry Brito, the executive director of Coin Center, a cryptocurrency research and advocacy group, told me. "All one needs to receive and send money is an internet-connected device."
Why haven't currencies such as bitcoin already become the preferred way to send money home then? In part because the user experience is often complicated, and in part because of price volatility. What immigrant is going to risk sending $1,000 to her family if it would end up turning into $800 by the time it got there? Libra could solve both those problems, given that its value would be tied to that of a basket of assets (it is a so-called stablecoin) and given that the user experience would be designed by Silicon Valley's finest engineers.
Read: Cryptocurrency might be a path to authoritarianism
But this elegant solution still might not be a workable solution for the world's poor. For one, recipients would need to figure out how to turn their Facebucks into cash denominated in their local currency—meaning a middleman looking to take a cut would enter the picture. The recipient would not necessarily need to convert her money into quetzales or francs or rupees if local merchants accepted Libra, and creating an "ecosystem" is its self-stated goal. But cash remains the dominant technology used for payments in many developing countries.
That's not the only potential drawback. Libra wants to be the currency of the internet, free and global and liquid. But being the free and global and liquid currency of the internet means being a facilitator of tax evasion and illicit payments. It means being a shadow bank, an unregulated one with no protections for consumers, businesses, or financial institutions. It means potentially facilitating currency crises and capital flight. If Libra were to become dominant, countries would lose a little grip—or perhaps a lot of grip—on their national accounts, monetary policy, and tax authority. "It would be revolutionary if it works, but getting it to work will require the buy-in of national authorities, and I'm racking my brain to think through scenarios where national authorities would want to promote a competitor to their own national currencies," said Michael Pisa of the Center for Global Development.
Finally, there is the problem posed by Libra's relationship with Facebook, which has come under fierce scrutiny for allowing users to organize racial violence, promote hate speech, and meddle in elections, as well as for trampling its users' privacy. "It is hard to view Facebook as a benign force, given all that has emerged over the past few years about their operations in the developing world," said Jeremy Konyndyk, also of the Center for Global Development. "Facebook has shown a consistent pattern of ignoring massive negative externalities of their platform, particularly if fixing those externalities conflicts with their revenue model. We can't fully envision what those negative externalities might be under this new system—but tying people's finances to a company with a history of privacy violations, information manipulation, and cross-cultural stumbles presents major concerns." Already Congress and a number of regulatory bodies have called for scrutiny of the Libra project, with an eye to hemming in the power of the tech giant.
Still, Libra's goal remains a vitally important one: Free, fast, reliable, and safe money transfers would mean billions of dollars of support for families at the bottom of the global income distribution. Facebook's biggest contribution might be in generating more innovation in remittances, and drawing attention to the issue. That would be a worthy thing, even if its elegant solution is not the right one.
Annie Lowrey is a staff writer at The Atlantic, where she covers economic policy.

redpajama_set_name: RedPajamaCommonCrawl


Published on IPSnews, by Kalinga Seneviratne, December 31, 2008.
SINGAPORE, Dec 31 (IPS) – The year 2008 may well go down in history as a watershed in which the global financial crisis, precipitated by the collapse of Western economic models, 'decolonised' Asians minds, say observers.
… Ajay Chhibber, director of the U.N. Development Programme's regional Bureau for Asia and Pacific, agrees that Asia needs to build on the currency swap arrangements put into place during the peak of the Asian financial crisis a decade ago.
In addition, says Chhibber, there should be greater coordination in the region to increase intra-Asia trade, and also strengthen programmes to help the poorest and neediest.
In a commentary in the 'Business Week,' Chibber welcomed China's 580 million dollar economic stimulation package as a good move and Singapore's blanket guarantees on deposits which has led to Malaysia following suit.
If India can also encourage the already strong domestic demand, he believes that inter-Asian trade could help to boost the economies of countries such as Bangladesh, Cambodia, Nepal, Sri Lanka, Pakistan and Vietnam, which are heavily dependent on western markets.
Even China may quietly move to demand changes to the IMF. Fan Gang, professor of economics at Peking University, believes that China is now in a position to increase its voice on a long-standing concern of theirs – the U.S. dollar's status as global reserve currency. He says that China would like to see an amendment to IMF's mandate so that they could "discipline America's money supply and debt accumulation".
Thus, though not making a big noise in the international scene yet, Asian countries and their policymakers are slowly but surely decolonising their minds of the idea that economic expertise comes purely from the West.
"If Asian countries can work together, the region can not only deal with the financial tsunami, but lay the ground for a powerful future, one in which greater coordination prepares the path for the eagerly awaited Asian century," predicts Chhibber. (full text).


We're going to take you to Phuket's premier shooting range where you'll get the chance to fire high powered sniper rifles, shotguns, plus much more. Once we get to the range you'll notice that they've got a massive array of guns available for you to shoot. Including Beretta 9mm's, a number of shotguns and rifles and not forgetting the powerful sniper rifles.
As well as the guns they also have clay shooting, archery, indoor and outdoor ranges plus a restaurant and snooker room. Integrating a number of guns we'll clarify who has the steadiest hand and announce and presenting a gift to the Clint Eastwood of the group at the end of the day. In the event of a tie, the people involved will get one last shot at the target, with the closest becoming victorious.
How popular is the Phuket Shooting Range activity?


text:
Q: Creating a hash of subroutines, and run one I'm trying to replicate the solution given in this example.
The code is as follows:
use strict;
use warnings;

my %hash = (
  one => sub { print 'one'; },
  two => sub { print 'two'; },
);

$hash{one};

The error I'm getting when running this is:

Useless use of hash element in void context at t.pl line 9.

I've made a running example here.
Where am I going wrong?

A: When it's not a symbol defined in a sub, you need to tell perl that it's a code reference explicitly to get it to 'run' it - otherwise you have just got a code reference to an anonymous hash, which you're trying to use in a void context.
You can do this by:
$hash{one}->();

Or:
&{$hash{one}}();

Or:
$hash{one}();

A: $hash{one}() is identical to $hash{one}->() except that Perl allows closing brackets ), }, ] to be followed immediately with any opening bracket (, {, [  with the appropriate dereferencing
Some people choose to make the indirection specific with intervening arrows ->,  even surrounded with spaces
My choice is to remove indirection arrows ->, as well as any other unnecessary non-whitespace (I'm claiming "darkspace" here!) characters, as far as possible as it speeds up my comprehension of code dramatically
You can load and play with this code as much as you like
use strict;
use feature ':5.10';

my $s = [ 1, 2, 3 ];

my $subs = {
    aa => sub { [0, $s, 0] },
    bb => sub {  99 },
};

say $subs->{aa}()[1][1];

output
2

I personally think that's clearer than something like this
say $subs -> {aa} -> () -> [1] -> [1]

which takes too much scanning to read in one pass. But I would be grateful for any comments that encourage a different view

redpajama_set_name: RedPajamaStackExchange


The Winnipeg Jets have opened the Stanley Cup playoffs with back-to-back home ice losses.
Ryan O'Reilly scored the go-ahead goal 3:46 into the third period as St. Louis defeated Winnipeg 4-3 Friday at Bell MTS Place.
Oskar Sundqvist added a pair of goals for the Blues who lead the NHL's best-of-seven Western Conference quarterfinal series two game to none.
Pat Maroon also scored for St. Louis.
Blake Wheeler, Patrik Laine and Mark Scheifele replied for the Jets.
Dustin Byfuglien chipped in with a pair of assists.
Blues goaltender Jordan Binnington made 26 saves.
Winnipeg's Connor Hellebuyck faced 32 shots.
The series shifts to St. Louis for game three on Sunday and game four on Tuesday.
St. Louis at Winnipeg, 7:30 p.m.
Portage at Swan Valley, 7:30 p.m.
Toronto at Minnesota, 12:10 p.m.
Kansas City at New York, 5:35 p.m.
Baltimore at Tampa Bay, 6:10 p.m.
Seattle at Los Angeles, 9:07 p.m.
Arizona at Atlanta, 11:10 a.m.
San Francisco at Washington, 12:05 p.m.
Los Angeles at Milwaukee, 7:10 p.m.
Philadelphia at Colorado, 7:40 p.m.
Cincinnati at San Diego, 9:10 p.m.
Philadelphia at Brooklyn, 7 p.m.
Denver at San Antonio, 8 p.m.
Golden State at L.A. Clippers, 9:30 p.m.


The Midlands is looking a great place to be right now.
The latest house price index revealed by the Office for National Statistics (ONS) show the midlands as having the most positive price rates of change over the last 12 months compared to the rest of the UK.
As well as it being a great place to live/move to, it's also a great place when it comes to job opportunities.
The statistics on our site show an increase in both the East Midlands and West Midlands average advertised salary over the past 12 months.
Birmingham, Nottingham and Leicester are just some of the areas offering lots of vacancies.
In the last year, the trend on our site shows an increase of 5% in the average advertised salary of vacancies in Nottingham, from £31,398 to £33,102.
An increase of 6% in Leicester, from £29,166 to £31,439 and an increase of 7% in Birmingham, from £33,523 to £35,630.
What can Nottingham offer you?
What can Leicester offer you?
What can Birmingham offer you?


> UAE Law FAQ > Fee for ousting a non-native partner in case there are more than partners in company?
Q) Are there specific fees for ousting a non-native partner in case there are more than partners in company?
← Is there a specific fee for the appeal following the first one?


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It is vital that any appliance involving gas is installed, maintained or repaired quickly and safely. More importantly, the company or individual working on the appliance simple must be Gas Safe registered. We are such a company.
Contact us and a professional, trained plumber will answer the phone. We can advise you on all gas related repairs, servicing and installation and any general plumbing queries.
We appreciate that often customers who need plumbing advise may be worried about the costs involved when calling out a plumber. We do not charge a call out fee in Leicester, so please ring on 0116 316 9946.
We are experienced in boiler and central heating servicing and repairs, so if you find yourself in need of a plumber, it helps to know you are in capable hands. We have many satisfied customers in Leicester who return to us after seeing how professional we are. We offer a high quality service not just to the pipes and boilers, but to our customers too.
So for a quality service call us on 0116 316 9946.


Flakesgiving is an annual event that The Breakfast Flakes created to help make a meaningful, positive impact in Billings, Montana for the holidays. Flakesgiving is not a food drive or a hot meal on location somewhere. It is much simpler than that. And therein lays the genius of Flakesgiving. It's very simple to understand. It's very simple to help and very simple to get help. This is a no questions asked way to get all of the ingredients to make a homemade Thanksgiving meal.
Mark & Paul get on the microphones and tell people how they can be nice and help their community through donating money for food or from volunteering.
Those Breakfast Flakes guys, Mark & Paul take the money and buy food – a lot of food! Flakesgiving feeds 10,000 people each year.
A bunch of volunteers show up at the Metrapark on Friday at 10am to put the food in boxes. There are 1,500 boxes of food that feed 7-10 people.
Saturday at noon, those volunteers load the rest of the boxes of food into the vehicles of people that would like to have a Flakesgiving meal.
Starting Monday November 14, 2016 Mark & Paul will start taking orders for deliveries for Flakesgiving meals. Donations really ramp up and volunteers start making sure they are ready to be at MetraPark the following Friday and/or Saturday at 10am. Mark & Paul will focus on Flakesgiving during the morning show and help listeners to know how they can donate, how they help volunteer and how they can pick up meals if they need them.
Friday 11/18/16 10am sharp – don't be late! Meal assembly: We will put together over 1,500 boxes of food. Each box of food will feed 7-10 people. Many hands make light work! Volunteers are needed on Friday. Plan on up to 2 hours but usually we get done even quicker.
Saturday 11/19/16 10am sharp – don't be late! Deliveries: Deliveries will start to roll out around 10:00am.
Saturday 11/19/16 12pm NOON sharp – don't be late! Pick up a meal: If you would like to come by and pick up a meal please plan to be at the Metra at 12:00pm sharp. Anyone is welcome to a meal, no questions asked, but it is first come – first served.
All meals go out Saturday. Deliveries first (we'll need drivers to deliver), then the main giveaway at 12 noon sharp. If somebody needs a meal, they will get one if they come to the fair grounds.
3 ways to donate: If you would like to donate money, mail a check to the address below, stop by the studio M-F 8a-5p or call our business line at 406-248-7827.
27 North 27th Street, 23rd Floor (top of the Crown Plaza Hotel).
How do I get a meal?: We won't take any delivery addresses until the week of the event which starts November 14, 2016. If you know somebody that needs one delivered who can't come pick one up call the studio 248-5665 or the office 248-7827. We will get them on the list & volunteer delivery drivers will deliver to them.
Is Flakesgiving a real charity? Yes! It is a real charity. However, unlike some charities, Flakesgiving has very low overhead. Funds go to buy food, paying the taxes required and an accountant to keep the book. Every single penny goes to feed hungry families. Mark and Paul don't take a dime and they never will.
How many people benefit from Flakesgiving? We create, distribute and deliver 1,500 complete meals. Each meal feed 7-10 people. That means over 10,000 people will eat because of Flakesgiving. It's the biggest event of its kind in the state of Montana.
What does a Flakesgiving meal come with?
Donate: The cost of this meal is about $27. Each meal feeds 7-10 people. Mark & Paul have fine-tuned this event to get the best value for the families we help. Your donations mean a lot. Change someone's holiday, give them hope, help our community in a real, tangible way.
Volunteer: We know that we've got several groups of volunteers this year and many more helping, but we can never have too many folks helping out. Volunteers are a big part of Flakesgiving. Grab your class, your team or the people in your office and come help Mark & Paul feed 10,000 people! You will be glad you did. It feels good to help so many people in such a short amount of time. We always need drivers – help us get this food to the people that cannot pick it up themselves.
Don't be late: Mark & Paul start at 10am sharp. Get to MetraPark in time to be parked, walk over & get briefed so we can start at 10am. Please don't be late.
Let's hope for generous donations and some decent weather.


Shazwani Hamid's Blog: I'm Back!
"Good morning camera! Yeayy another 30 minutes to arrive Kuala Lumpur! I can't wait!!"
Anyways, actually I really really want to update this blog tonight. There are just sooo many stories I wanted to share.. But lately, I just don't know why, the mood just isn't there.. I've been busy thinking about something else that made me stuck in here not knowing what to write! And then ended up having to press the 'Cancel' button each time I tried to update this blog! haha.
Maybe because there are just soooo many things that I still owe my blog which I haven't been able to write just yet, and that makes me don't know what and where to start first. Seriously, I owe this blog a huge amount of stories! My Bangkok trip, my internship experience-working in a fashion company (which was a year ago! haha), my Indonesia trip, even my Perth stories pun tak habis lagi! And then my Amsterdam vacation which was in 2008 pun, I still save it in the 'Draft' files. Thing is, I have uploaded all the pictures here 2 years ago, but yet, until now, I still haven't find the time to actually write something..and yet to publish it.. And then nowwww, my Umrah trip.
Hmmm... Entah bila semua tu nak tercapai kan? haha.
Adoiii cerita 2 tahun lepas pun blom publish lagi? Haha! Satu-satu Cik Wani. Kalau u update 1 hari at least 1 entry, sure boleh habis kot? Hehe. Tapi ye lah, sometimes u mesti busy apa semua kan..
update selalu pleaseee! i nak tahu mcm2 psl u.. i dah email u!!
izzati: ok ok will do!
pink: happy fasting to u too!
kak suzie:heheh..nnt saya cerita byk2 k!
Subscribe to Celcom Broadband This Raya!


During my time as a Marine Education Officer I have been invited to many open conversations, workshops and conferences, so when I was invited to attend a night of conversation around marine debris at Sealife Mooloolaba, I thought it was a great networking and information sharing opportunity. What I wasn't expecting, was that the night would cause a shift in my understanding of the importance of data collection and the sway that citizen science can have.
The night was organised by the Sunshine Coast Council and included guest speakers from Targaroa Blue, Sealife Mooloolaba, Coolum and North Shore Coastare, Reefcheck Australia and the SCRC Turtlecare program. These stakeholders have a volunteer or not-for-profit element to their conservation work and as such the passion exuded by each speaker was all encompassing.
One statement said it all.
A very bold statement which had everyone sitting up and listening with open ears. What Naomi meant was that collecting debris is an amazing opportunity to identify what is washing up, where it comes from and how it entered the marine environment.
Through this train of thought the Australia Marine Debris Initiative (AMDI) was born. The organisation has a global database in which volunteers, community groups and organisations can input data based on the size, material and type of item collected from the beaches and river clean ups. This means me, you and the little old lady down the road can contribute to the collection of scientific data.
Tangaroa Blue then uses this data to work with Industry and government organisations to create change on a large scale. Once upon a time this type of citizen science was dismissed as 'not scientific', however, it appears this broad quantitative science is gaining more traction within the scientific and government communities. The exciting thing that I discovered was that local government authorities are willing to see this as a feasible data collection means for identifying possible trends within the environmental systems.
But how is the raw data used to do this? Well, I thought the same thing until I discovered that the data can be viewed by anyone and can be collated to create reports on the website and can be (including a variety of graphs…..everyone loves a good graph) tailored for specific beaches or communities. This opens the opportunity for the identification of trends and problematic pollutants within this locality and to identify where the most common types of pollutants have originated from. Once specific pollutants or trends have been identified, this data can be used as a basis for change in the form of prevention by a strategic approach within the local community.
It is this type of focused solution planning, or pollutant focused planning, that the Sunshine Coast Council is showing an interest in. An example of the positive use of this data is with the implementation of a ban on the release of balloons at council events and in council-managed reserves by the Eurobodalla Shire Council. This was the direct result of collation of data relating to balloons found on the local beaches and the education on balloon impacts on the marine environment that was given by the local environmental officers.
This is the key shift in thinking from simply cleaning the beach (which I do not want to underestimate the importance!) to using this necessary and vital community action as an opportunity for data collection and potentially as a platform for societal change. Essentially this database and others like it are enabling members of the community access to relevant data to drive changes from a community based ground roots level.
For more information about Tangaroa Blue, the Australian Marine Debris Initiative or upcoming clean up events, visit www.tangaroablue.org.
This entry was posted in Marine Education and tagged beach clean up, citizen science, coast care, marine biology, marine debris, Marine Studies, public education, sunshine coast on March 21, 2017 by oceanlifeeducation.


text:
Q: Dependency Violation when changing/deleting a resource in terraform I am facing an issue when deploy services to AWS via Terraform. The error I got is:
module.elasticsearch.aws_security_group.es: Still destroying... [id=sg-039f33d9b29a38c46, 9m39s elapsed]
module.elasticsearch.aws_security_group.es: Still destroying... [id=sg-039f33d9b29a38c46, 9m49s elapsed]
module.elasticsearch.aws_security_group.es: Still destroying... [id=sg-039f33d9b29a38c46, 9m59s elapsed]

Error: Error deleting security group: DependencyViolation: resource sg-039f33d9b29a38c46 has a dependent object
    status code: 400, request id: cd20a8e3-231f-444f-8479-b0575a98b390

It tries to delete a security group but found out there is a dependency object which stop it deleting it. I checked on AWS console the security group has an associate network interface which I don't have permission to delete. I found below changes on terraform plan:
~ name                   = "SecuritySearchElasticSearchtest" -> "SecuritySearchElasticSearch" # forces replacement

It tries to rename a security group during deployment.
I wonder why Terraform tries to redeploy it. Why not just use the existing resources? Can I force Terraform to not replace?

A: First Let's explain the problem you're dealing with
The problem: You're trying to apply some change on a resource in terraform though this resource is associated and connected to another resources. In this case, aws security group id reference is mapped and connected to another security groups and therefore  a DependencyViolation error is shown.
For example:
sg_a ( ingress: x, y, z       | outgress:all )
sg_b ( ingress: a, b, c, sg_a | outgress:all )

When sg_a is being removed the reference inbound still exists on sg_b and dependent on it. You applying your change and getting timeout message like:
...
module.some_module.aws_security_group: Still destroying... [id=sg-a, 10m elapsed]
module.some_module.aws_security_group: Still destroying... [id=sg-a, 13m elapsed]
module.some_module.aws_security_group: Still destroying... [id=sg-a, 14m elapsed]
module.some_module.aws_security_group: Still destroying... [id=sg-a, 15m elapsed]

Error: Error deleting security group: DependencyViolation: resource sg-a has a dependent object
status code: 400, request id: abc-123-zxc-567```

According to the reference the dependency violation timeout comes after 15 minutes.

delete - (Default 15m) How long to retry on DependencyViolation errors
during security group deletion from lingering ENIs left by certain AWS
services such as Elastic Load Balancing. NOTE: Lambda ENIs can take up
to 45 minutes to delete, which is not affected by changing this
customizable timeout (in version 2.31.0 and later of the Terraform AWS
Provider) unless it is increased above 45 minutes.

Solution: The best way dealing with this violation dependency is refreshing the external resources using and depends on this dependency (in our example sg_b should not use sg_a , this ingress should be removed, afterwards applying your changes on terraform again and sg_a will be deleted.
in our example (remove sg_a ingress reference from sg_b security group) :
sg_a ( ingress: x, y, z | outgress:all )
sg_b ( ingress: a, b, c | outgress:all )

Now you can run terraform apply:
sg_b ( ingress: a, b, c | outgress:all )

A: You can try to remove that SG from state by making command like
terraform state rm module.elasticsearch.aws_security_group.es
and then you can try to import that resource by making command
terraform import module.elasticsearch.aws_security_group.es <security_group_id>
please also keep in mind that in your terraform code name of security group should be SecuritySearchElasticSearchtest if you want terraform to avoid destroying that SG


text:
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Thoughts of Dog 2020 Day-to-Day Calendar
Based on the popular @dog_feelings Twitter feed, this desk calendar offers daily, sweet, funny reflections on life from the pup-spective of a good doggo. Created by today's hottest internet-dog-humor king, Matt Nelson of WeRateDogs, this calendar will warm the hearts of dog lovers as they are reminded each day that good dogs, above all else,…
Life's Little Instruction 2020 Day-to-Day Calendar
By H. Jackson Brown
The Life's Little Instruction 2020 Day-to-Day Calendar: Classics Volume V features both new and favorite instructions by H. Jackson, Brown, Jr., that will help you live a happy and meaningful life. Each page of this calendar includes a classic and much-loved instruction or one recently written by H. Jackson Brown, Jr. Since 1993, the author's…
Cat Shaming 2021 Day-to-Day Calendar
By Pedro Andrade
Why is it that cats never look or act guilty for the wrongs they commit? Featuring hilarious owner-contributed photos, the Cat Shaming 2021 Day-to-DayCalendar provides plenty of commiseration and comic relief for cat lovers everywhere. Each page of this calendar shows a different photo of a cat with a sign describing behaviors that cat owners…
Zits 2020 Day-to-Day Calendar
By Jerry Scott, Jim Borgman
Sometimes teens and their parents have different ideas about things. Take Jeremy Duncan's bedroom, for example. He'd like to have a fridge to save on steps to the kitchen, while parents Walt and Connie are measuring and dreaming up plans for the space after Jeremy graduates and goes off to college. Or summer plans. They…
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Nobody does trash talk like the Bard. Build up your battle vocab with Shakespearean Insults 2020 Day-to-Day Calendar and verbally vanquish any modern-day rogues, rascals, vixens, and joltheads you encounter. Each page of this calendar features a witty jab, piercing remark, or scathing smackdown from one of Shakespeare's plays that will amuse theater geeks, literature…
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Jeremy Duncan is a typical teenager—more interested in pizza, guitar solos, and his girlfriend than cleaning his room, keeping a job, or making post-high school plans. Walt and Connie are his parents—bewildered at how quickly the family goes through groceries, always trying to connect with their busy, ear bud-wearing son, and, as far as Jeremy…
Texts from Mittens 2021 Day-to-Day Calendar
By Angie Bailey
What would life be like if cats had smart phones and could text their owners what they were thinking? This calendar will show you. Based on the popular blog and book of the same name, the Texts from Mittens 2021 Calendar features imaginary, humorous, sarcastic, and sweet conversations shared between "Mitty," the box-loving, over-anxious, self-absorbed…
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Have you ever wondered what dogs would say if they had smart phones and could text us their every thought—good or bad? You're about to find out. Based on the popular textfromdog.tumblr.com, each full-color page of the Texts from Dog 2021 Calendar features imaginary, comical, and crass SMS exchanges shared between Dog, a foul-mouthed British…
Laugh-Out-Loud Jokes 2021 Day-to-Day Calendar
By Rob Elliott
From knock-knock jokes to bad Dad jokes and pun-derful Q&A, the Laugh-Out-Loud Jokes 2021 Day-to-Day Calendar is jam-packed with 1,000 corny jokes. Based on the best-selling book series, Laugh-Out-Loud-Jokes for Kids by Rob Elliott, this calendar features a year's worth of family-friendly fun for all ages! Features Include: Tear-off pages Day/date reference on each page…


text:
Q: How to emulate window functions in MySQL < 8.0 I have tables like these:
INSERT INTO listings
(id, external_id, variation_id, product_id) VALUES
(101, '9900001', '9900001var1', 1),
(102, '9900001', '9900001var2', 4),
(103, '9900002', '9900002var1', 1),
(104, '9900002', '9900002var2', 2),
(105, '9900003', '9900003var1', 3),
(106, '9900003', '9900003var2', 4);

INSERT INTO products
(id, price) VALUES
(1, 101),
(2, 100),
(3, 100),
(4, 102);

Which means that there are 3 listings (9900001, 9900002, 9900003) with 2 products each (1, 4), (1, 2) and (3, 4) respectively.
What I need is to retrieve one single row for each listing, with the id (not the price) of the product with the highest price in that listing.
So, the desired output would be:
id    | external_id | variation_id | product_id
[ANY]   9900001       [ANY]          4
[ANY]   9900002       [ANY]          1
[ANY]   9900003       [ANY]          4

The closest I got to the desired answer was with this query:
SELECT
    p.id AS product_id_max,
    p.price AS product_price_max,
    MAX(p.price) AS product_price_max_max,
    listings.*
            FROM listings
            INNER JOIN (

              -- Subquery tested above:
              SELECT DISTINCT pp3.* FROM
                (SELECT MAX(p2.price) as max_price
                FROM products p2
                INNER JOIN listings l2 ON l2.product_id = p2.id
                GROUP BY l2.external_id) pp2
              INNER JOIN
                (SELECT p3.* FROM products p3 ) pp3
              ON
                pp2.max_price = pp3.price
              ORDER BY pp3.price DESC

            ) AS p
            ON p.id = listings.product_id
            -- WHERE MAX(p.price) = p.price
            GROUP BY external_id
            -- HAVING MAX(p.price) = p.price
            ORDER BY product_price_max DESC

Uncommenting the WHERE clause throws an error, uncommenting the HAVING clause returns less rows than desired.  Leavin both commented give the correct rows but wrong values in the product_id column.
Fiddle:  http://sqlfiddle.com/#!9/d58d665/54/0

A: I figured it out:
SELECT
    listings.*,
    max_p.product_id AS max_product_id
            FROM listings
            INNER JOIN (

              SELECT DISTINCT max_external_id as external_id, pp3.id as product_id FROM
                (SELECT MAX(p2.price) as max_price, l2.external_id as max_external_id
                FROM products p2
                INNER JOIN listings l2 ON l2.product_id = p2.id
                GROUP BY l2.external_id) pp2
              INNER JOIN
                (SELECT p3.* FROM products p3 ) pp3
              ON
                pp2.max_price = pp3.price
              ORDER BY pp3.price DESC

            ) AS max_p
            ON max_p.external_id = listings.external_id
            GROUP BY listings.external_id

As tested here:
http://sqlfiddle.com/#!9/d58d665/53/0


text:
using System;
using System.Collections.Generic;
using System.Linq;

namespace AdventOfCode.Core
{
    public interface IValueProvider
    {
        ushort? GetValue(Circuit circuit);
        void Reset();
    }

    public class ConstantProvider : IValueProvider
    {
        public ushort Value { get; }

        public ConstantProvider(ushort value)
        {
            Value = value;
        }

        public ushort? GetValue(Circuit circuit)
        {
            return Value;
        }

        public void Reset()
        {
            // no op
        }

        public override string ToString()
        {
            return Value.ToString();
        }
    }

    public class NamedNodeProvider : IValueProvider
    {
        public string Name { get; }

        public NamedNodeProvider(string name)
        {
            Name = name;
        }

        private ushort? _value;

        public ushort? GetValue(Circuit circuit)
        {
            if (_value.HasValue)
                return _value;

            return _value = circuit.GetWireValue(Name);
        }

        public void Reset()
        {
            _value = null;
        }

        public override string ToString()
        {
            return Name;
        }
    }

    public static class ValueProviderFactory
    {
        public static IValueProvider Create(string input)
        {
            ushort value;
            if (ushort.TryParse(input, out value))
                return new ConstantProvider(value);

            return new NamedNodeProvider(input);

        }
    }
}

redpajama_set_name: RedPajamaGithub