• <tr id="yyy80"></tr>
  • <sup id="yyy80"></sup>
  • <tfoot id="yyy80"><noscript id="yyy80"></noscript></tfoot>
  • 99热精品在线国产_美女午夜性视频免费_国产精品国产高清国产av_av欧美777_自拍偷自拍亚洲精品老妇_亚洲熟女精品中文字幕_www日本黄色视频网_国产精品野战在线观看 ?

    Superplastic behavior of a fine-grained Mg-Gd-Y-Ag alloy processed by equal channel angular pressing

    2023-12-27 12:43:44RezeiMhmudiLog
    Journal of Magnesium and Alloys 2023年10期

    A.Rezei ,R.Mhmudi,? ,R.E.Logé

    a School of Metallurgical and Materials Engineering, College of Engineering, University of Tehran, Tehran 14395-515, Iran

    b Laboratory of Thermomechanical Metallurgy - PX Group Chair, Ecole Polytechnique Fédérale de Lausanne (EPFL), CH-2002 Neuchatel, Switzerland

    Abstract An extruded Mg-6Gd-3Y-1.5Ag (wt%) alloy was processed by 6 passes of equal channel angular pressing (ECAP) at 553 K using route Bc to refine the microstructure.Electron back-scattered diffraction (EBSD) analysis showed a fully recrystallized microstructure for the extruded alloy with a mean grain size of 8.6 μm.The microstructure of the ECAP-processed alloy was uniformly refined through dynamic recrystallization (DRX).This microstructure contained fine grains with an average size of 1.3 μm,a high fraction of high angle grain boundaries (HAGBs),and nano-sized Mg5Gd-type particles at the boundaries of the DRXed grains,detected by transmission electron microscopy (TEM).High-temperature shear punch testing (SPT) was used to evaluate the superplastic behavior of both the extruded and ECAP-processed alloys by measuring the strain rate sensitivity (SRS) index (m-value).While the highest m-value for the extruded alloy was measured to be 0.24 at 673 K,the ECAP-processed alloy exhibited much higher m-values of 0.41 and 0.52 at 598 and 623 K,respectively,delineating the occurrence of superplastic flow.Based on the calculated average activation energy of 118 kJ mol-1 and m-values close to 0.5,the deformation mechanism for superplastic flow at the temperatures of 598 and 623 K for the ECAP-processed alloys was recognized to be grain boundary sliding (GBS) assisted by grain boundary diffusion.

    Keywords: Mg-Gd-Y alloys;Equal channel angular pressing;Superplasticity;Strain rate sensitivity;Grain boundary sliding.?Corresponding author.

    1.Introduction

    The increasing demand for weight-saving purposes in automobile and aerospace industries has drawn attentions to magnesium alloys,as suitable candidates having low density and high specific strength [1].However,the lack of sufficient independent slip systems of their HCP structure has restricted their formability at room temperature [2].That is why superplastic forming could be proposed as an alternative approach to address such an adversity by imposing large strains without necking,to produce near-net components having complex shapes [3].However,superplastic forming of polycrystalline materials usually requires some specific prerequisites in terms of microstructural and metallurgical features.First,a fine-grained structure consisting of grains smaller than 10 μm in size with preferably high angle grain boundaries (HAGBs)is needed,as grain boundary sliding (GBS) is the dominant deformation mechanism during superplastic flow [4–6].Secondly,as the superplastic flow is a diffusion-controlled process,the forming operation should be carried out at relatively high temperatures greater than 0.5Tm,whereTmis the absolute melting temperature [7].Finally,the microstructure must be thermally stable in order to avoid grain growth at high temperatures during superplastic forming.Therefore,superplasticity usually takes place in two-or multi-phase alloys,or in the ones containing a fine dispersion of second phases[8,9].

    It has been shown that among different severe plastic deformation (SPD) techniques,equal channel angular pressing(ECAP) is significantly effective in refining the microstructure and imparting superplastic capability in various Mg alloys.Figueiredo and Langdon [10] reported a maximum tensile elongation of 3050% at the temperature of 473 K and strain rate of 1.0×10-4s-1for an extruded ZK60 alloy after 2 ECAP passes at 473 K under route Bc.In another study,the maximum elongation of 840% was achieved at 473 K for an Mg-9% Al alloy,having a grain size of about 0.7 μm,after 2 ECAP passes at 473 K under route Bc,whereas the as-cast and extruded conditions did not exhibit superplastic behavior [11].Recently,the superplastic behavior of an Mg-6.5Y-1.2Er-1.6Zn-xAg (x=0 and 1 wt%) alloy after 16 ECAP passes at 693 K has been investigated [12].The Ag-containing alloy showed a maximum elongation of 495% and strain rate sensitivity (SRS) index of 0.46,indicating the occurrence of GBS and superplastic flow,whereas the base alloy did not exhibit superplastic characteristics.Vávra et al.[13] reported high strain rate superplasticity for a solution treated commercial WE43 magnesium alloy processed by 8 ECAP passes using route Bc through a decreasing processing temperature method from 603 to 558 K.The highest elongation of about 1230% at a strain rate 10-2s-1for the two testing temperatures of 623 and 673 K was attributed to improved GBS due to the significantly fine grain size of 340 nm achieved after ECAP process.They also showed that at the testing temperature of 673 K,the SRS indices were well above 0.5 in the high strain rate domain of 6 × 10-3to 2 × 10-1s-1.

    Among various classes of Mg alloys,the Mg-Gd-Y systems,known as GW series,are prominent for their high thermal stability and enhanced mechanical properties at both ambient and high temperature,caused by Gd and Y elements in the solid solution and also formation of heat-resistant second phases [14–16].Therefore,superplastic forming in Mg-Gd-Y alloys would be of great interest for producing wrought components with potential applications in high temperature services.However,scarce studies reported on the superplastic behavior of fine-grained Mg-Gd-Y alloys processed by SPD techniques.For instance,Yang et al.[17] reported superplastic behavior for an Mg-9.4Gd-4.1Y-1.2Zn-0.4Zr alloy with the grain size of about 3 μm processed by friction stir processing (FSP) in the high strain rate regime,having an exceptional maximum elongation of 3570% at the testing temperature of 698 K along with the SRS index of 0.6 at the temperatures of 673 K and 698 K.Alizadeh et al.[18] compared the superplasticity of an Mg-5Gd-4Y (GW54) alloy processed by 8 turns of high pressure torsion (HPT) at room temperature and 4 passes of ECAP at 623 K by measuring the SRS indices through shear punch test (SPT).They obtained the SRS index of 0.5 at the testing temperature of 623 K for the HPT-processed alloy,whereas the (SRS) index of 0.46 was achieved at the much higher testing temperature of 723 K for the ECAP-processed alloy.The significant difference in the optimum superplastic temperature was attributed to the much finer grain size of 72 nm for the HPT-processed alloy,as compared to grain size of 2.2 μm for the one processed by ECAP.Rezaei et al.[19] used the same testing procedure to investigate superplastic capability of an extruded Mg-6Gd-3Y-0.5Ag alloy processed by different passes of simple shear extrusion (SSE)and found the largest SRS index of 0.45 at 623 K along with an activation energy of 112 kJ mol-1for the alloy processed by 6 passes of SSE,indicating a superplastic flow controlled by GBS.

    During the recent years,many studies have acknowledged the validity of SPT results in evaluating the superplastic capability through measuring SRS indices for various fine-grained Mg alloys in the extruded state [20,21] and also after being processed by different SPD techniques such as ECAP[22–25],HPT [26,27],SSE [28,29],multi directional forging(MDF) [30,31],FSP [32] and constrained groove pressing(CGP) [33].Thereby,the aim of this study was set to investigate the superplastic flow in a fine-grained Mg-Gd-Y-Ag alloy processed by ECAP via SPT at high temperatures and different shear strain rates,and to correlate the measured SRS indices to the microstructural features observed before and after SPT.

    2.Experimental procedure

    2.1.Materials processing

    An Mg-6 wt% Gd-3 wt% Y-1.5 wt% Ag alloy was produced by casting,using pure Mg ingot,Mg-30Gd and Mg-30Y (wt%) master alloys and pure Ag as the starting materials.The melting procedure was performed in an electrical resistant furnace at 1053 K under a covering flux to protect the melt from oxidation.The melt was poured into a pre-heated cylindrical steel mold having a diameter of 42 mm.The cast billet was then homogenized at 773 K for 10 h and then cooled in air to remove the dendritic structure formed during cooling,and ease the upcoming hot extrusion process.The actual composition of the cast billet was determined through inductively coupled plasma (ICP) spectroscopy and it was found to be 5.8 wt% Gd,2.7 wt% Y,1.4 wt% Ag and 90.1 wt% Mg.The homogenized billet was hot extruded to bars having cross section of 11 mm × 11 mm at the temperature of 673 K under a pressing velocity of 5 mm min-1with an extrusion ratio of 11.4.Afterwards,the extruded bar was cut into billets having a cross section of 10 mm × 10 mm and a length of 60 mm in order to be fed into the ECAP die.The ECAP process employed in this study was comprised of a deformation channel having a die angle of 90° and outer arc curvature of 20°,leading to an imposed equivalent mean strain of 1.02 on the workpiece per each pass.The ECAP process was carried out using route Bc at 553 K for 6 passes and pressing speed of 0.1 mm s-1,and the specimens were held for 15 min in the ECAP die between the consecutive passes before starting the pressing to achieve an isothermal state with the surrounding die.

    2.2.Microstructural characterization

    Electron back-scattered diffraction (EBSD) analysis was utilized to investigate the microstructural features for both extruded and ECAP-processed alloys in the as-processed conditions and also after SPT at high temperatures.The EBSD specimens were cut perpendicular to the extrusion direction(ED) and were then ground and polished by diamond paste suspensions.Afterwards,a final polishing stage using a solution comprised of ethanol-5% HNO3-5% ethylene glycol was performed to obtain a finished surface.The EBSD studies were performed using a field emission scanning electron microscope (FESEM),Philips XL30,equipped with an Oxford Instrument EBSD detector,where the step size and working voltage of 0.3 μm and 25 kV were applied,respectively.The EBSD data were processed using MTEX software.Boundaries having misorientation angles in the range of 2° to 15°were considered as the low angle grain boundaries (LAGBs),while those with misorientation angles of greater than 15°were identified as the high angle grain boundaries (HAGBs).Grain orientation spread (GOS) concept was used to determine the recrystallization fraction (fREX),so that the grains with GOS greater than 2° were detected as deformed grains,and those having GOS lower than 2° were considered to be recrystallized grains.Kernel average misorientation (KAM)maps along with their distribution diagrams were also obtained from the EBSD data with selecting a threshold misorientation angle ofθth=5° and a neighboring number ofnequal to 5 for the pixels at the center of kernel grid.

    Transmission electron microscopy (TEM) was performed using an FEI Tecnai Osiris instrument to investigate the microstructural features of the ECAP-processed alloy at higher magnifications.The TEM specimens were cut normal to ED,thinned mechanically to a thickness of 100 μm,and electropolished by a twin-jet facility,using an electrolyte consisting of ethanol-5% HNO3-5% HCl at 273 K and a voltage of 12 V.All the TEM studies were done under the working voltage of 200 kV.

    2.3.Mechanical testing

    The SPT method was used to assess the superplastic flow behavior of the extruded and ECAP-processed alloys at high temperatures.The SPT setup used in this study involves a flat-ended cylindrical punch and a corresponding receiving die hole with the diameters of 3.1 and 3.15 mm,respectively.The SPT specimens with an initial thickness of 1 mm were cut normal to the ED using electro discharge machining,and then thinned to a thickness of 0.75 mm through grinding.Testing of the extruded alloys was carried out in a temperature range of 623-723 K,whereas the ECAP-processed samples were tested in the 573-673 K temperature range.The shear strain rate for the SPT was between 1.6 × 10-2and 1.3 × 10-1s-1.All shear punch tests were performed using a screw-driven universal testing machine equipped with a three-zone furnace.The instantaneous load-displacement data for SPT were acquired by a computer software and incorporated to construct the shear flow stress curves according to the following relationship [34]:

    Fig.1.(a) 3D schematic view of a shear-punch assembly [35],and (b) the 2D schematic illustration of a deformed SPT specimen clamped within a shear-punch assembly during testing [36].

    whereτis shear stress,Fis the applied load,Dis the average of the punch and die hole diameters andtis the initial thickness of the SPT specimen.The shear strain rate (˙γ) during SPT can also be given through the following relationship[34]:

    Fig.1a and b depicts the schematic illustration of the SPT assembly in 3D and 2D views,respectively.A deformed SPT specimen with an initial thickness oftduring testing is well illustrated in the 2D schematic view of Fig.1b.The SPT specimen is firmly clamped between two stationary holders within the shear-punch setup and the specimen is deformed by a flat-ended cylindrical punch during the application of an external load.The shear deformation zones in the deformed SPT specimen are marked by the parallel hatched lines in the schematic illustration of Fig.1b.

    Fig.2.The IPF maps of the extruded (a) and ECAP-processed (b) alloys along with their corresponding (0001) pole figures presented below them;the grain size and misorientation angle distribution diagrams for both cases of the extruded (c and e) and ECAP-processed (d and f) alloys obtained from EBSD results.

    3.Results

    3.1.Microstructural observations

    Fig.2a and b illustrate the respective IPF maps of the extruded and ECAP-processed alloys along with their (0001)basal pole figures corresponding to the TD-ND section.The extruded alloy is comprised of a fully recrystallized microstructure having equiaxed grains having a mean size of 8.6 μm (with a standard deviation of SD=±4.1 μm),whereas the microstructure of the ECAP-processed alloy is significantly refined having an overall average grain size of 1.5 μm (SD=0.8 μm),and an average grain size of 1.3 μm when only the newly formed dynamically recrystallized (DRXed) grains are considered.Both extruded and ECAP-processed alloys exhibited the respectivefREXof 95±1 and 90±2%.Fig.2c and d shows the grain size distribution diagrams obtained from the EBSD data for the extruded and ECAP-processed alloys,respectively.According to Fig.2c,the extruded alloy exhibits a wide distribution of grain size,while for the ECAP-processed alloy a noticeable shift to the smaller grain sizes along with a much narrower distribution is evident (Fig.2d).As depicted in Fig.2e and f,the misorientation angle distribution diagrams,derived from the corresponding EBSD maps,show high fractions of HAGBs of 97 and 93% for the extruded and ECAP-processed conditions,respectively.

    For a better understanding of the microstructural evolution after severe deformation,TEM investigations were performed on the ECAP-processed alloy.Fig.3a and b depict the bright field TEM micrographs at different magnifications.The development of freshly formed fine DRXed grains and formation of a series of spherical nano-particles,mostly distributed at the sites of the newly formed boundaries of these grains after ECAP,is clear in the TEM images (Fig.3b).A selected area electron diffraction(SAED)pattern taken from the aforementioned nano-particles is shown in the upper right corner of the TEM micrograph in Fig.3b,indexing an FCC structure with a zone axis ofZ=[12] and lattice parameter ofa=2.21 nm.For chemical analysis,a high angle annular dark field (HAADF) image along with its corresponding elemental maps are provided in Fig.3c,indicating a discernible segregation of Gd,Y and also Ag at the locations of the nanoparticles.Fig.3d shows an energy dispersive spectroscopy(EDS) spectrum along with its chemical analysis results that was taken from location“A”marked by a red arrow in Fig.3c.According to the EDS results obtained by TEM studies,the spherical nano-particles have a composition close to Mg5Gdtype compounds.

    3.2.High temperature flow behavior

    As illustrated in Fig.4,the high-temperature shear flow stress data were plotted against the cross-head displacement normalized to the initial thickness of the SPT specimens.Fig.4a and b illustrate the SPT curves at the constant testing temperature of 623 K and different shear strain rates,whereas Fig.4c and d represent the flow curves at the constant shear strain rate of 8.3 × 10-2s-1and different testing temperatures for the extruded and ECAP-processed alloys.It can be observed that at a constant temperature,the peak shear stress(τm) and the overall shear flow stress increase by raising the strain rate for both cases (Fig.4a and b).Furthermore,as the testing temperature increases,both peak shear stress and flow stress drop continuously at any given normalized displacement(Fig.4c and d).

    In order to measure the SRS indices (m-values),the plots of variations in normalized peak shear stress(τm/G)with temperature compensated shear strain rate (˙γ T/G) are constructed from the SPT results in a double-logarithmic scale for both extruded and ECAP-processed alloys,as depicted in Fig.5a and b,respectively.The flow behavior of metallic materials at elevated temperatures can be expressed through the wellknown power-law relationship,correlating the strain rate to flow stress and temperature according to the following equation [5]:

    whereAis a material constant,Dothe frequency factor,Gthe shear modulus,bthe Burgers vector,kthe Boltzmann’s constant,Tthe absolute temperature,dthe grain size,σthe flow stress,Qthe activation energy,Rthe universal gas constant,pthe exponent of inverse grain size andnthe stress exponent.The above power-law relationship can be considered in the shear mode in order to be applied to the SPT result so that it can be written and rearranged as follows [18]:

    whereA′is a material constant andmthe SRS index equal to the inverse of stress exponent.By considering the above relationship,the SRS index can be calculated at a constant temperature through differentiating Eq.(4):

    Torbati-Sarraf et al.[27] for the first time evaluated the validity of SRS index obtained from SPT results through measuring them-value at the two testing temperatures of 473 and 523 K for an ultrafine-grained ZK60 magnesium alloy processed by 5 turns of HPT at room temperature under an applied constant pressure of 2 GPa.They compared the results with the corresponding values achieved from hot tensile testing at the same temperatures.It was reported that,a highm-value of 0.47,measured from tensile testing at 523 K for the HPT-processed alloy,was very close to the corresponding value of 0.49 obtained from the SPT results at the same testing temperature.Moreover,a maximum elongation to failure of 940% was achieved at 523 K from tensile testing that is in agreement with the respective highm-values of 0.47 and 0.49 obtained from tensile and SPT results,indicative of superplastic flow and GBS.In another case,Esfandyarpour et al.[37] also assessed the capability of SPT in evaluating the hot deformation behavior of a rolled Sn-5Sb alloy in a temperature range of 298 to 400 K,and compared the results with the ones obtained by hot tensile testing.It was found out that there is reasonable consistency between the hot deformation parameters such as stress exponent (inverse ofm-value) and activation energy values in both cases.Therefore,considering these cases,it can be deduced that them-values measured through the SPT results are as effective and valid as the those obtained from conventional tensile testing method to assess the superplastic behavior,or in general the hot flow behavior of metallic materials.

    To account for the temperature dependency of the elastic constants in measuring ofm-value at each temperature,the shear modulus,G,was calculated in MPa from the following relationship [38]:

    Fig.3.Bright field TEM micrographs of the ECAP-processed alloy at different magnifications (a and b) with the SAED pattern obtained from the round nano-particles shown in the top right corner of (b) indexing an FCC structure with a zone axis of Z=[12];the HAADF image and the corresponding elemental maps of the nano-particles (c) along with the EDS analysis result (d) taken from a particle from location “A” marked in (c).

    Fig.4.Shear stress vs.normalized displacement curves obtained from SPT at a constant temperature of T=623 K and different shear strain rates for both the extruded (a) and ECAP-processed (b) alloys,and also at a constant shear strain rate of ˙γ=8.3 × 10-2 s-1 but at different testing temperatures for the extruded (c) and ECAP-processed (d) alloys.

    According to Eq.(5),the slope of each line in the diagrams of Fig.5 represents the measured SRS index for the corresponding testing temperature.Fig.6 plots and summarizes the changes ofm-values with testing temperature,where it can be deduced that the variations ofm-values with temperature for both extruded and ECAP-processed alloys exhibit a bell-shape behavior,i.e.,first the SRS index increases,reaching a maximum value,and then drops continuously with temperature.Based on the data presented in Figs.5 and 6,however,the major differences between the flow behavior of the extruded and ECAP-processed alloys lie in the values of SRS indices.For instance,at the temperature of 623 K,the extruded alloy possesses a SRS index of 0.11,while that of the ECAPprocessed alloy is 0.52.This difference will be discussed in the terms of microstructural features in the discussion section.

    For determining the mechanism of deformation,calculation of the activation energy is inevitable.By considering the power-law relationship of Eq.(4),the activation energyQ,at a constant temperature-compensated shear strain rate,can be calculated as:

    The variation of normalized peak shear stress with the inverse of temperature at different constant temperaturecompensated shear strain rates is plotted for the ECAPprocessed alloy,as shown in Fig.7.The plot of (τm/G) vs.(1/T) was constructed between the two temperatures of 598 and 623 K,corresponding to the largestm-values of 0.41 and 0.52,respectively.Therefore,the calculated activation energy ofQcould only be representative of the occurrence of GBS and superplastic flow,where it can be compared with the ideal activation energy of grain boundary diffusion for Mg.Accordingly,an average apparent activation value ofQave=118 kJ mol-1was achieved.

    Fig.5.The variation of normalized peak shear stress (τm/G) with temperature compensated shear strain rate (˙γ T/G) at different testing temperatures obtained from the SPT results for both the extruded (a) and ECAP-processed(b) alloys.

    Fig.6.The variation of strain rate sensitivity index (m-value) with the testing temperature obtained from the SPT results for the extruded and ECAPprocessed alloys.

    The microstructural features of the shear deformation zones after SPT for the extruded and ECAPed alloys at the temperatures of 623 and 673 K and a shear strain rate of 3.3 × 10-2s-1were examined via EBSD analysis and the results are illustrated in the form of IPF maps and their corresponding KAM data,as shown in Figs.8 and 9.The significant differences in the microstructure after SPT at 623 K for the extruded and ECAP-processed alloys are visible in the IPF maps of Fig.8a and b.The extruded alloy is mostly comprised of large grains elongated along a direction inclined about~45° relative to the loading axis of SPT,and a small fraction of very fine DRXed grains mainly distributed at the grain boundaries of the deformed grains (Fig.8a).In contrast,in the case of ECAP-processed alloy,after SPT at the same temperature,the microstructure consists of fine equiaxed grains with no sign of directionality even after straining (Fig.8b).According to the EBSD results,the average size of the fine DRXed grains for the ECAP-processed alloy after SPT at 623 K is 1.3 μm,without significant change compared to the as-processed alloy.The respectivefREXof 16 and 86%are obtained for the extruded and ECAPed alloy after SPT at 623 K.The corresponding KAM map of the extruded alloy shown in Fig.8c represents a noticeable level of in-grain misorientation gradients,whereas the ECAP-processed alloy exhibits an almost strain-free microstructure,mostly containing fine DRXed grains.This discrepancy in KAM values can also be observed in the histograms of Fig.8e and f,where a drastic shift to the lower KAM angles can be observed for the ECAP-processed alloy.

    Fig.7.The variation of normalized shear stress (τm/G) with the reciprocal of temperature at different constant shear strain rates obtained from the SPT results for the ECAP-processed alloy in the superplastic forming temperature range.

    Fig.8.The IPF maps and the KAM maps of the extruded (a and c) and ECAP-processed (b and d) taken from the shear deformation zone after SPT at the temperature of T=623 K and shear strain rate of ˙γ=3.3 × 10-2 s-1,and the corresponding KAM distribution diagrams obtained from the EBSD results shown in (e) and (f) for the extruded and ECAP-processed alloys,respectively.

    Fig.9.The IPF maps and the KAM maps of the extruded (a and c) and ECAP-processed (b and d) taken from the shear deformation zone after SPT at the temperature of T=673 K and shear strain rate of ˙γ=3.3 × 10-2 s-1,and the corresponding KAM distribution diagrams obtained from the EBSD results shown in (e) and (f) for the extruded and ECAP-processed alloys,respectively.

    Similarly,Fig.9a and b display the IPF maps after SPT,this time at 673 K,with the same shear strain rate of 3.3 × 10-2s-1,for the extruded and ECAPed alloys,along with their KAM maps in Fig.9c and d and their corresponding KAM angle distribution diagrams in Fig.9e and f.The extruded alloy still contains large,heavily deformed,grains with some DRXed grains at the boundaries,larger than the ones observed at 623 K in Fig.8a.However,according to the IPF map of Fig.9b,the most drastic evolution has occurred for the ECAP-processed alloy,where a significant grain coarsening has taken place at 673 K,resulting in the average grain size of 6.8 μm.Grains are still equiaxed and no preferential directionality is observed for the ECAP-processed alloy,whereas the extruded alloy still exhibits elongated grains in the shear zone of SPT (Fig.9a).The extruded alloy again exhibits a high level of KAM value,indicative of a heavily deformed microstructure,with afREXof 29% (Fig.9c and e).On the other hand,in the case of the ECAP-processed alloy,the microstructure keeps a much higherfREXof 76%,with overall lower KAM values in the map of Fig.9d,and in the histogram of Fig.9f.

    4.Discussion

    The formation of equiaxed grains within a fully recrystallized microstructure withfREX=95% in the as-extruded alloy,shown in Fig.2a,stems from the intrinsic tendency of the tested alloy for refinement after hot extrusion at the high temperature of 673 K.After ECAP,the microstructure experiences even more refinement (Fig.2b),in such a way that a homogeneous grain structure consisting of fine DRXed grains is obtained.This can be also inferred from its narrow grain size distribution in Fig.2d.This microstructural uniformity can be attributed to the significant activity of DRX in the material after experiencing high levels of imposed strains,by 6 passes of ECAP,and also the incorporation of working route Bc that increases the homogeneity of the strain distribution throughout the specimen.

    According to the (0001) pole figures of the extruded alloy shown in Fig.2a,the typical fiber texture has not formed.Instead,it can be perceived that the majority of the basal planes are inclined relative to the ED with a split in the basal poles.This unusual arrangement of the basal plane has been reported for other extruded Mg-Gd-Y alloys before[28,39,40],and was attributed to the effect of rare earth (RE)elements on postponing the occurrence of DRX,and also activation of non-basal slip systems during hot extrusion.On the other hand,in the case of the ECAP-processed alloy,there is one concentrated basal pole with no splitting,indicative of the arrangement of the majority of basal planes inclined about~45° relative to ED.This configuration of the basal planes is the typical shear component usually occurring in Mg alloys after being processed by ECAP using route Bc,which has also been reported in previous studies [22,41–43].

    The most important feature of the TEM micrographs in Fig.3,besides the development of fine grains,is the formation of the spherical Mg5Gd-type nano-particles mostly at the boundaries of the newly formed fine DRXed grains after ECAP.These particles are formed during straining in ECAP through dynamic precipitation,which is a strain-induced phenomenon depending on the development of dislocations and new grain boundaries.The formation of the Mg5Gd-type compounds in the form of nano-sized particles with a similar globular morphology through dynamic precipitation has been reported in several previous works for different Mg-Gd-Y alloys processed by various thermo-mechanical treatments[19,44–47],and also in our previous works [48,49] for an alloy similar to that in the present study after ECAP and SSE at the same processing temperature of 553 K.The possible role of these Mg5Gd-type particles on the superplastic behavior of the ECAP-processed alloy will be discussed later.

    According to the high-temperature SPT curves,shown in Fig.4,it can be observed that after an initial linear elastic behavior,the material undergoes a short hardening stage until a peak shear stress is reached.These peak stresses will be used to obtain the SRS indices at different temperatures.With further straining,the shear flow stress drops due to the prevalence of softening effects.The raise in the flow stress by increasing the shear strain rate at a constant temperature for both extruded and ECAP-processed alloys (Fig.4a and b)is indicative of a positive SRS,attributed to the increase of the dislocation multiplication rate.

    Considering the SRS measurements,illustrated in Fig.5 and 6,the significant differences in the obtainedm-values of the extruded and ECAPed alloys must be interpreted in terms of their microstructural features.The largest SRS indices of 0.41 and 0.52 measured at the temperatures of 598 and 623 K are close to the theoretical SRS index ofm=0.5 [5,50],indicating the occurrence of superplastic flow at these temperatures for the fine-grained alloy processed by ECAP.However,in the case of the extruded alloy,the highestm-value reached 0.24 at 673 K,which does not indicate a superplastic behavior.One of the most important features of the (τm/G) vs.(˙γ T/G) plots for the ECAP-processed alloys shown in Fig.5b,is the development of a sigmoidal behavior at the temperatures of 598 and 623 K,where the superplastic flow took place.This type of behavior implies that superplasticity occurs in a certain range of strain rate,which is known as region II [6,7].Therefore,for the lower and higher strain rates outside this specific range (i.e.,respective regions of I and III [6,7]) at the temperature of superplastic forming,the dependency of flow stress to the strain rate decreases noticeably,leading to reduced SRS and deterioration of GBS.The observed superplastic flow in the ECAP-processed alloy is attributed to the fine-grained structure developed through the progress of DRX after experiencing high levels of straining.As the emergence of GBS during superplastic flow is basically assisted by diffusion of atoms through the grain boundaries,finer grain structures would enhance the contribution of GBS during deformation at high temperatures,due to the higher density of HAGBs.Consequently,the difference in the grain size would best explain the discrepancy in the type of flow behavior between the extruded and ECAP-processed alloys.

    The average activation energy of 118 kJ mol-1achieved for the superplastic flow of the ECAP-processed alloy(Fig.7),is slightly greater than the activation energy of grain boundary diffusion for Mg (92 kJ mol-1[22]).This could be ascribed to the presence of the large RE elements Gd and Y having low diffusion rates in the Mg matrix [51].Moreover,the formation of the globular Mg5Gd-type nano-particles through dynamic precipitation,shown by the TEM studies,could also make a contribution to increasing the required activation energy of GBS during superplastic flow.It was shown via TEM studies that the Mg5Gd-type nano-particles are mostly formed at boundary sites of the newly formed DRXed grains.Therefore,the presence of these particles during superplastic flow could cause disturbance,as they might act as obstacles to easy grain boundary sliding,leading to deterioration of superplastic capability.As a result,greater activation energy of superplastic flow might be required in order to make the GBS process able to overcome the aforementioned barrier.The calculated activation energy of 118 kJ mol-1for the superplastic flow is greater than the ideal value of 92 kJ mol-1for the grain boundary diffusion of Mg.In addition to the probable role of RE elements as mentioned earlier,the observed difference in the obtained activation energy with the ideal value of 92 kJ mol-1could be attributed to the presence and formation of Mg5Gd-type nano-particles at the boundary sites of fine DRXed grains,leading to a more difficult GBS.

    To sum up,by consideringm-values close to 0.5 at the temperatures of 598 and 623 K and also the calculated average activation energy of 118 kJ mol-1near to the one for grain boundary diffusion in Mg,a deformation mechanism of GBS assisted by grain boundary diffusion is proposed for the superplastic flow in the fine-grained alloy processed by ECAP.

    The microstructural observations after SPT at 623 K are shown in Fig.8.The formation of elongated deformed grains and shear bands in the microstructure of the extruded alloy after SPT depicted in Fig.8a justifies the lowestm-value of 0.11 at 623 K.In contrast,the preserved equiaxed structure of the fine DRXed grains in the ECAP-processed alloy even after straining via SPT (Fig.8b) corroborates them-value of 0.52 achieved at 623 K.In other words,superplastic flow is able to retain an equiaxed grain structure with no preferred directionality and also absence of grain growth,due to the thermal stability of the microstructure.In addition,the fact that even after SPT at 623 K there is still a remarkably high fraction of recrystallized grains (fREX=86%) confirms the occurrence of GBS as the dominant mechanism of deformation,i.e.without significant dislocation slip.This can be well observed through the KAM results of the ECAP-processed alloy after SPT at 623 K in Fig.8d and f.The nano-sized Mg5Gd-type particles are likely to play a role in the thermal stability of the microstructure through imposing a drag pressure on the boundaries of the DRXed grains via Zenner effect,impeding the dynamic grain growth during superplastic flow at 598 and 623 K for the ECAP-processed alloy.Moreover,according to the HAADF and its corresponding elemental distribution maps of Fig.3 obtained during TEM studies,it is shown that Ag element is preferentially segregated on the sites of the Mg5Gd-type nano-particles.The presence of Ag element might encourage the formation of second phase particles through absorption and co-segregation with Gd and Y due to their noticeable atomic size difference [52].Therefore,the indirect role of Ag element on superplasticity could be associated with favoring the formation of the Mg5Gd-type nano-particles and their effect on deterring the grain growth during the occurrence of GBS and superplastic flow.

    The significant grain growth occurring after SPT at 673 K for the ECAP-processed alloy (Fig.9b) would justify the drastic drop of SRS index from the highest value of 0.52 obtained at 623 K to the lower value of 0.27 at 673 K.However,the microstructure has remained equiaxed,with a highfREX=76% compared to its extruded counterpart (29%).It may therefore be assumed that GBS remains non negligible,at least in the first stages,when the microstructure is still fine enough.

    5.Conclusions

    Superplasticity of an Mg-6Gd-3Y-1.5Ag (wt%) alloy after extrusion and ECAP was investigated by measuring the strain rate sensitivity indices through shear punch testing(SPT),and the following conclusions were drawn:

    (1) EBSD maps showed a fully recrystallized microstructure for the extruded alloy with a mean grains size of 8.6 μm,while the ECAP-processed alloy exhibited a uniform finegrained structure with an average size of 1.3 μm for the newly formed fine dynamically recrystallized (DRXed)grains and a high fraction of high angle grain boundaries(HAGBs),caused by extensive DRX.

    (2) Transmission electron microscopy (TEM) of the ECAPprocessed alloy showed that globular Mg5Gd-type nanosized particles were formed through dynamic precipitation,mostly at new boundaries of the DRXed grains.

    (3) SPT results showed higher values of strain rate sensitivity(m-value) for the ECAP-processed alloy,reaching 0.41 and 0.52 at 598 and 623 K,indicating a superplastic flow controlled by grain boundary sliding (GBS).The average activation energy of 118 kJ mol-1calculated for the ECAPprocessed alloy along with them-values close to 0.5 suggested GBS assisted by grain boundary diffusion as the dominant deformation mechanism during superplastic flow at 598 and 623 K.

    (4) The EBSD studies after SPT at 623 K revealed an equiaxed microstructure without any grain growth for the finegrained alloy processed by ECAP,whereas the microstructure of the extruded alloy at the same temperature was comprised of deformed grains elongated along the loading axis of SPT.The microstructural feature of the ECAPprocessed alloy was responsible for the observed superplasticity at 623 K,with GBS as the controlling deformation mechanism.

    Declaration of competing interest

    The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.

    CRediT authorship contribution statement

    A.Rezaei:Conceptualization,Investigation,Methodology,Writing–original draft.R.Mahmudi:Conceptualization,Supervision,Validation,Writing– review &editing.R.E.Logé:Writing– review &editing.

    Data availability statement

    Data will be made available on request.

    Funding

    This research did not receive any specific grant from funding agencies in the public,commercial,or not-for-profit sectors.

    Acknowledgements

    The authors would like to thank Dr.Cyril Cayron at Laboratory of Thermomechanical Metallurgy (LMTM),école Polytechnique Fédérale de Lausanne (EPFL),Switzerland for his assistance in the EBSD and TEM experiments.R.Logé acknowledges the generous financial support of PX Group to their laboratory.

    青春草国产在线视频 | 91在线精品国自产拍蜜月| 99热只有精品国产| 亚洲精品日韩av片在线观看| 亚洲激情五月婷婷啪啪| 伦理电影大哥的女人| 久久久久免费精品人妻一区二区| 午夜精品一区二区三区免费看| 亚洲美女搞黄在线观看| 美女高潮的动态| 麻豆国产av国片精品| 午夜老司机福利剧场| a级毛片免费高清观看在线播放| 久久精品国产亚洲av香蕉五月| 国产精品一区二区性色av| 国产午夜精品一二区理论片| 99久国产av精品| 给我免费播放毛片高清在线观看| 国产黄色小视频在线观看| 亚洲精品成人久久久久久| 91午夜精品亚洲一区二区三区| 婷婷精品国产亚洲av| 国产av麻豆久久久久久久| 九九爱精品视频在线观看| 国产精品美女特级片免费视频播放器| 一个人观看的视频www高清免费观看| 亚洲欧洲日产国产| 国产成年人精品一区二区| 日本免费一区二区三区高清不卡| 国产探花极品一区二区| 午夜视频国产福利| 欧洲精品卡2卡3卡4卡5卡区| 国产人妻一区二区三区在| 一本久久精品| 国模一区二区三区四区视频| 国产一区二区三区在线臀色熟女| 精品一区二区免费观看| 少妇被粗大猛烈的视频| 黄片无遮挡物在线观看| 免费看a级黄色片| 亚洲激情五月婷婷啪啪| 色哟哟哟哟哟哟| 免费av不卡在线播放| 18+在线观看网站| 欧美一级a爱片免费观看看| 级片在线观看| 精品久久久久久成人av| 国产91av在线免费观看| 麻豆乱淫一区二区| 国产老妇伦熟女老妇高清| 日日撸夜夜添| 日本黄色视频三级网站网址| 91精品一卡2卡3卡4卡| 啦啦啦韩国在线观看视频| 国产又黄又爽又无遮挡在线| 最近最新中文字幕大全电影3| 亚洲精品乱码久久久v下载方式| 久久精品夜色国产| 久久久国产成人免费| 夜夜爽天天搞| 国产黄色小视频在线观看| 舔av片在线| 岛国在线免费视频观看| 一区二区三区四区激情视频 | 在线播放国产精品三级| 久久久久久久久久久丰满| 亚洲久久久久久中文字幕| 国产v大片淫在线免费观看| 热99re8久久精品国产| 中文字幕精品亚洲无线码一区| 免费观看的影片在线观看| 一区二区三区免费毛片| 欧美zozozo另类| 丰满乱子伦码专区| 欧美精品国产亚洲| 国产成人精品婷婷| 国产高清视频在线观看网站| 1000部很黄的大片| 亚洲最大成人中文| 日韩在线高清观看一区二区三区| 啦啦啦韩国在线观看视频| 最近最新中文字幕大全电影3| 国产高清三级在线| 久久久a久久爽久久v久久| 欧美高清性xxxxhd video| 性欧美人与动物交配| 亚洲人与动物交配视频| 亚洲av免费高清在线观看| 久久久色成人| 日本一二三区视频观看| 最近手机中文字幕大全| 精品欧美国产一区二区三| 男人的好看免费观看在线视频| 99久国产av精品国产电影| 1024手机看黄色片| 简卡轻食公司| 久久精品夜色国产| 久久人人爽人人片av| 国产美女午夜福利| a级毛色黄片| 亚洲欧美精品综合久久99| 精品99又大又爽又粗少妇毛片| 亚洲成a人片在线一区二区| 桃色一区二区三区在线观看| 午夜精品国产一区二区电影 | 99九九线精品视频在线观看视频| 成人漫画全彩无遮挡| 日日干狠狠操夜夜爽| 卡戴珊不雅视频在线播放| 最近手机中文字幕大全| 麻豆国产av国片精品| 久久精品国产亚洲网站| 久久99热6这里只有精品| 免费在线观看成人毛片| 日本撒尿小便嘘嘘汇集6| 国产精品蜜桃在线观看 | 免费黄网站久久成人精品| 老司机福利观看| 别揉我奶头 嗯啊视频| av在线老鸭窝| 国产精品野战在线观看| 欧美变态另类bdsm刘玥| 日韩成人伦理影院| 天天一区二区日本电影三级| 久久久久国产网址| 黄色日韩在线| 寂寞人妻少妇视频99o| 不卡一级毛片| 精品熟女少妇av免费看| 91久久精品电影网| 亚洲精品久久久久久婷婷小说 | av在线老鸭窝| 久久久久久久亚洲中文字幕| 亚洲丝袜综合中文字幕| 久久久久免费精品人妻一区二区| 精品少妇黑人巨大在线播放 | 国产欧美日韩精品一区二区| 欧美人与善性xxx| av福利片在线观看| 久久久久久九九精品二区国产| 蜜臀久久99精品久久宅男| 久久婷婷人人爽人人干人人爱| 长腿黑丝高跟| 免费大片18禁| 精品久久久久久久末码| 精品欧美国产一区二区三| 亚洲成a人片在线一区二区| 老司机福利观看| 男女那种视频在线观看| 国产激情偷乱视频一区二区| 国产激情偷乱视频一区二区| 寂寞人妻少妇视频99o| 蜜臀久久99精品久久宅男| 亚洲精品亚洲一区二区| 精品久久久久久久久亚洲| 91麻豆精品激情在线观看国产| 国产男人的电影天堂91| 最近视频中文字幕2019在线8| 欧美zozozo另类| av女优亚洲男人天堂| 亚洲成a人片在线一区二区| 别揉我奶头 嗯啊视频| 久久久精品大字幕| 欧美变态另类bdsm刘玥| 黄色一级大片看看| 在线观看免费视频日本深夜| 日本-黄色视频高清免费观看| 男的添女的下面高潮视频| 精华霜和精华液先用哪个| 国产精品一及| 国产成人福利小说| 欧美日韩乱码在线| 最后的刺客免费高清国语| 能在线免费观看的黄片| 国产精品伦人一区二区| 成年av动漫网址| 99久久精品一区二区三区| 午夜免费男女啪啪视频观看| 免费无遮挡裸体视频| 一区二区三区高清视频在线| 日本色播在线视频| 免费不卡的大黄色大毛片视频在线观看 | 国产高清激情床上av| 精品久久久久久久久av| 亚洲av一区综合| 久久久久网色| 亚洲av不卡在线观看| 啦啦啦观看免费观看视频高清| 中文资源天堂在线| 人体艺术视频欧美日本| 不卡一级毛片| 18禁黄网站禁片免费观看直播| 99热网站在线观看| 亚洲欧洲日产国产| 欧美zozozo另类| 美女 人体艺术 gogo| 国产精品永久免费网站| 真实男女啪啪啪动态图| 18+在线观看网站| 天堂中文最新版在线下载 | 欧美高清性xxxxhd video| 乱码一卡2卡4卡精品| 日日摸夜夜添夜夜添av毛片| 成人亚洲欧美一区二区av| 亚洲中文字幕一区二区三区有码在线看| 黄片无遮挡物在线观看| 色吧在线观看| 亚洲av一区综合| 一本一本综合久久| 国产亚洲欧美98| 国产精品永久免费网站| 天堂网av新在线| 国产精品国产高清国产av| 欧美一区二区精品小视频在线| 男人舔女人下体高潮全视频| АⅤ资源中文在线天堂| 国产高清有码在线观看视频| 久久久久网色| 如何舔出高潮| 亚洲人成网站高清观看| 国产成人freesex在线| 国产免费一级a男人的天堂| 日韩中字成人| 精品午夜福利在线看| 偷拍熟女少妇极品色| 国产精品久久久久久精品电影小说 | 啦啦啦韩国在线观看视频| 色综合色国产| 亚洲精品久久久久久婷婷小说 | 欧美三级亚洲精品| 久久精品国产亚洲av香蕉五月| 一级二级三级毛片免费看| 亚洲欧美日韩高清专用| 最近最新中文字幕大全电影3| 婷婷精品国产亚洲av| 男女啪啪激烈高潮av片| 国产精品一区二区三区四区久久| 性插视频无遮挡在线免费观看| 成人二区视频| 国产精品人妻久久久久久| 亚洲第一区二区三区不卡| 久久99热这里只有精品18| 一级毛片电影观看 | 久久久午夜欧美精品| 欧美性猛交黑人性爽| 欧美色视频一区免费| 男女那种视频在线观看| 三级经典国产精品| 亚洲成人中文字幕在线播放| 99九九线精品视频在线观看视频| 乱系列少妇在线播放| 青春草视频在线免费观看| 高清午夜精品一区二区三区 | 啦啦啦啦在线视频资源| 国产成人一区二区在线| 成人毛片a级毛片在线播放| 国产高清激情床上av| 91久久精品国产一区二区三区| 51国产日韩欧美| av在线老鸭窝| 日本黄色视频三级网站网址| 婷婷六月久久综合丁香| 岛国在线免费视频观看| 婷婷色av中文字幕| 亚洲国产日韩欧美精品在线观看| 天天躁夜夜躁狠狠久久av| 亚洲熟妇中文字幕五十中出| 午夜福利视频1000在线观看| 亚洲图色成人| 欧美激情久久久久久爽电影| 人人妻人人澡欧美一区二区| 国产一区二区激情短视频| 最近手机中文字幕大全| 99热这里只有精品一区| 天天一区二区日本电影三级| 亚洲精品日韩av片在线观看| 国产精品女同一区二区软件| 午夜激情欧美在线| 日韩大尺度精品在线看网址| 国产老妇女一区| 久久婷婷人人爽人人干人人爱| 国产成人a∨麻豆精品| 日本黄色片子视频| 欧美性感艳星| 国产成人aa在线观看| 免费人成在线观看视频色| 成年女人看的毛片在线观看| 国产私拍福利视频在线观看| 午夜亚洲福利在线播放| 色视频www国产| 麻豆成人av视频| 国产极品天堂在线| 国产一区二区亚洲精品在线观看| 高清毛片免费观看视频网站| 日韩欧美国产在线观看| 熟女电影av网| 亚洲av男天堂| 国产成人影院久久av| 中文在线观看免费www的网站| 夫妻性生交免费视频一级片| 国产成人91sexporn| 国产精品久久视频播放| 99久久成人亚洲精品观看| 三级男女做爰猛烈吃奶摸视频| 婷婷六月久久综合丁香| 毛片一级片免费看久久久久| 啦啦啦啦在线视频资源| 中国美白少妇内射xxxbb| av天堂在线播放| 日本爱情动作片www.在线观看| 久久精品国产99精品国产亚洲性色| 国产精品99久久久久久久久| 亚洲精品成人久久久久久| av视频在线观看入口| 免费看日本二区| 久久久久久久久久成人| 精品人妻视频免费看| 18禁在线播放成人免费| 免费看av在线观看网站| 内射极品少妇av片p| 日本色播在线视频| 我要搜黄色片| 在线免费十八禁| 成人性生交大片免费视频hd| 亚洲成人精品中文字幕电影| 国产成人影院久久av| av黄色大香蕉| videossex国产| 午夜爱爱视频在线播放| 亚洲人成网站高清观看| 精品熟女少妇av免费看| 久久久久久久久久黄片| 国产精华一区二区三区| 成人美女网站在线观看视频| 亚洲欧美精品自产自拍| 长腿黑丝高跟| 国产黄色视频一区二区在线观看 | 真实男女啪啪啪动态图| 国产免费一级a男人的天堂| 国产成年人精品一区二区| 亚洲国产色片| 成人午夜精彩视频在线观看| 国产亚洲5aaaaa淫片| 综合色丁香网| 高清毛片免费看| 国产精品久久久久久久电影| 亚洲国产欧美在线一区| 久99久视频精品免费| 成人欧美大片| 男女啪啪激烈高潮av片| 深爱激情五月婷婷| 女人被狂操c到高潮| 伊人久久精品亚洲午夜| 婷婷色综合大香蕉| 好男人视频免费观看在线| 午夜久久久久精精品| 不卡一级毛片| 亚洲欧洲日产国产| 夜夜夜夜夜久久久久| 国产毛片a区久久久久| 亚洲一级一片aⅴ在线观看| 国产老妇伦熟女老妇高清| 青春草视频在线免费观看| 2021天堂中文幕一二区在线观| 日韩成人av中文字幕在线观看| 午夜精品国产一区二区电影 | 午夜精品一区二区三区免费看| 亚洲精品亚洲一区二区| 日本爱情动作片www.在线观看| 国产精品一二三区在线看| 一本精品99久久精品77| 寂寞人妻少妇视频99o| 亚洲欧美日韩无卡精品| 亚洲最大成人av| 国产69精品久久久久777片| 亚洲色图av天堂| 爱豆传媒免费全集在线观看| 能在线免费观看的黄片| 岛国毛片在线播放| 欧美日韩精品成人综合77777| 性色avwww在线观看| 亚洲天堂国产精品一区在线| 国产精品1区2区在线观看.| 久久中文看片网| 乱系列少妇在线播放| 亚洲在久久综合| 久久精品国产亚洲av香蕉五月| 欧美色视频一区免费| 中文资源天堂在线| 国产伦精品一区二区三区视频9| 午夜精品在线福利| 日韩一区二区视频免费看| 亚洲欧美日韩无卡精品| 18禁在线无遮挡免费观看视频| 亚洲人成网站高清观看| av天堂在线播放| 男女视频在线观看网站免费| 日韩视频在线欧美| 久久99蜜桃精品久久| 免费搜索国产男女视频| 欧美一级a爱片免费观看看| 12—13女人毛片做爰片一| 少妇裸体淫交视频免费看高清| 欧美成人免费av一区二区三区| 国产熟女欧美一区二区| 天堂√8在线中文| 国产一级毛片在线| 边亲边吃奶的免费视频| 一级二级三级毛片免费看| 亚洲第一电影网av| 22中文网久久字幕| 乱人视频在线观看| 国产精品一区二区在线观看99 | 国产精品女同一区二区软件| 欧美成人免费av一区二区三区| 精品熟女少妇av免费看| 欧美性感艳星| 亚洲天堂国产精品一区在线| 亚洲真实伦在线观看| 精品久久久久久久末码| 国产av麻豆久久久久久久| 2021天堂中文幕一二区在线观| 最后的刺客免费高清国语| 日韩视频在线欧美| 国产精品福利在线免费观看| 午夜老司机福利剧场| 97超碰精品成人国产| 久久婷婷人人爽人人干人人爱| 午夜精品在线福利| 国产精品99久久久久久久久| 高清日韩中文字幕在线| 三级毛片av免费| 亚洲最大成人中文| 亚洲一级一片aⅴ在线观看| 美女 人体艺术 gogo| 在线a可以看的网站| 青春草亚洲视频在线观看| av黄色大香蕉| 此物有八面人人有两片| 欧美成人一区二区免费高清观看| 99久久精品一区二区三区| 久久精品夜夜夜夜夜久久蜜豆| 边亲边吃奶的免费视频| 97人妻精品一区二区三区麻豆| 欧美在线一区亚洲| 小蜜桃在线观看免费完整版高清| 26uuu在线亚洲综合色| 久久精品夜色国产| 看十八女毛片水多多多| 欧美性猛交╳xxx乱大交人| 老女人水多毛片| 亚洲国产精品sss在线观看| 久久国内精品自在自线图片| 麻豆成人av视频| av又黄又爽大尺度在线免费看 | 成年女人永久免费观看视频| 中文字幕免费在线视频6| 国产一级毛片七仙女欲春2| 舔av片在线| 久久久久久久久久久丰满| 最好的美女福利视频网| 久久午夜亚洲精品久久| 精品少妇黑人巨大在线播放 | 床上黄色一级片| 亚洲国产精品国产精品| 久久欧美精品欧美久久欧美| 国产精品久久久久久av不卡| 欧美高清成人免费视频www| 男女做爰动态图高潮gif福利片| 午夜激情福利司机影院| 在线a可以看的网站| 深爱激情五月婷婷| 国产探花在线观看一区二区| 色噜噜av男人的天堂激情| 狂野欧美白嫩少妇大欣赏| 在线观看66精品国产| 最近视频中文字幕2019在线8| 亚洲三级黄色毛片| 久久99热这里只有精品18| 成年免费大片在线观看| 精品一区二区三区人妻视频| 超碰av人人做人人爽久久| 日韩大尺度精品在线看网址| 热99在线观看视频| 女人被狂操c到高潮| 22中文网久久字幕| 午夜免费激情av| 黄色配什么色好看| 国产视频首页在线观看| 久久人妻av系列| avwww免费| 日本撒尿小便嘘嘘汇集6| 悠悠久久av| 国产成人影院久久av| 老熟妇乱子伦视频在线观看| 免费看美女性在线毛片视频| 国产精品野战在线观看| 97超视频在线观看视频| 校园春色视频在线观看| 日日啪夜夜撸| 99久国产av精品国产电影| av天堂中文字幕网| 亚洲七黄色美女视频| 国产精品人妻久久久久久| 国产av不卡久久| 国产亚洲av片在线观看秒播厂 | 美女xxoo啪啪120秒动态图| 日韩欧美国产在线观看| 色噜噜av男人的天堂激情| a级毛色黄片| 边亲边吃奶的免费视频| 一本久久精品| 国产伦在线观看视频一区| АⅤ资源中文在线天堂| 别揉我奶头 嗯啊视频| 国产 一区精品| 麻豆国产av国片精品| 日本成人三级电影网站| 丝袜美腿在线中文| 伊人久久精品亚洲午夜| 淫秽高清视频在线观看| 国产高清三级在线| 国产私拍福利视频在线观看| 亚洲美女搞黄在线观看| 亚洲欧美日韩无卡精品| av视频在线观看入口| 赤兔流量卡办理| 国产精品人妻久久久影院| 99久久成人亚洲精品观看| 国产不卡一卡二| 一级av片app| 亚洲av中文av极速乱| 国产精品久久久久久精品电影小说 | 国产成人91sexporn| 成年av动漫网址| av免费观看日本| 如何舔出高潮| 久久国产乱子免费精品| 国产视频内射| 欧美+亚洲+日韩+国产| 亚洲欧美中文字幕日韩二区| 国产极品精品免费视频能看的| 一级毛片我不卡| 夜夜看夜夜爽夜夜摸| 一区二区三区免费毛片| 国产探花极品一区二区| 成人漫画全彩无遮挡| 18+在线观看网站| 亚洲自偷自拍三级| 亚洲av成人精品一区久久| 国产私拍福利视频在线观看| 99久久人妻综合| 久久这里只有精品中国| 午夜精品国产一区二区电影 | 国产成人一区二区在线| 最近视频中文字幕2019在线8| 午夜视频国产福利| 哪里可以看免费的av片| 久久久久久久亚洲中文字幕| 日韩三级伦理在线观看| 亚洲在线观看片| av又黄又爽大尺度在线免费看 | 欧美色视频一区免费| 三级国产精品欧美在线观看| 老司机影院成人| 欧美精品一区二区大全| 三级毛片av免费| 日韩精品青青久久久久久| 国产麻豆成人av免费视频| 天天躁夜夜躁狠狠久久av| 亚洲成人久久爱视频| 亚洲精品自拍成人| 久久精品国产亚洲网站| 蜜臀久久99精品久久宅男| 日本撒尿小便嘘嘘汇集6| 国产亚洲5aaaaa淫片| 日本撒尿小便嘘嘘汇集6| 日本与韩国留学比较| 啦啦啦啦在线视频资源| 少妇人妻一区二区三区视频| 午夜福利成人在线免费观看| 成人国产麻豆网| 亚洲图色成人| 丰满人妻一区二区三区视频av| 又爽又黄a免费视频| 日韩欧美三级三区| 亚洲欧美日韩高清在线视频| 亚洲18禁久久av| 免费人成在线观看视频色| 久久精品综合一区二区三区| 久久久欧美国产精品| 一级二级三级毛片免费看| 亚洲欧美成人精品一区二区| 日本av手机在线免费观看| 岛国毛片在线播放| 国产精品久久久久久av不卡| 变态另类成人亚洲欧美熟女| 午夜福利视频1000在线观看| 三级国产精品欧美在线观看| 日韩 亚洲 欧美在线| 欧美又色又爽又黄视频| 麻豆乱淫一区二区| 国产真实伦视频高清在线观看| 中文字幕制服av| 高清日韩中文字幕在线| 国产精品麻豆人妻色哟哟久久 | 欧美一级a爱片免费观看看| 99在线人妻在线中文字幕| 国产激情偷乱视频一区二区| 九九热线精品视视频播放| 国产午夜精品论理片| 少妇猛男粗大的猛烈进出视频 | 小说图片视频综合网站| 亚洲高清免费不卡视频| 全区人妻精品视频|