Formation of Grain Boundary a in b Ti Alloys

内蒙古自治区科技引导计划项目（20071911） 作者简介：刘宗昌，（1940～），男，汉族，河北玉田人，内蒙古科技大学教授。

从事相变理论和热处理技术研究。

发表论文260余篇，出版专著和高等院校教材14部。

E －mail ：lzchang75@复徐祖耀《评刘宗昌等“贝氏体……”一文》刘宗昌，计云萍，任慧平，袁长军，段宝玉（内蒙古科技大学 材料与冶金学院，内蒙古 包头 014010）摘要：对徐祖耀院士在《评刘宗昌等“贝氏体铁素体的形核”一文》中提出的问题进行了阐述和回复。

指出：贝氏体铁素体在晶界形核的新观察验证了形核的一般规律。

依据试验观察，理论计算得贝氏体临界晶核尺寸和形核功为：*a =16.7nm ；*b =25nm ，*G ∆=270J ·mol-1，此值合理。

奥氏体中贫碳区的存在是普遍事实，试验也测得贝氏体相变孕育期内形成了贫碳区；不能将Spinodal Decomposition 与奥氏体中形成贫碳区和富碳区混为一谈。

涨落是相变的契机，在孕育期内奥氏体中必由于涨落而形成贫碳区。

阐述了非协同热激活跃迁形核机制。

大量TTT 图分析和实测均表明贝氏体铁素体形核-长大不可能以扩散方式进行。

在这些问题上徐祖耀院士的观点，我们不能苟同。

关键词：贝氏体铁素体；晶界形核；扩散；切变；热激活跃迁Reply to the paper 《Comment on the paper …... authored by LIUZong-chang 》authored by XU Zu-yaoLIU Zong-chang, JI Yun-ping, REN Hui-ping, YUAN Chang-jun, DUAN Bao-yu（Material and Metallurgy School, Inner Mongolia University of Science and Technology, Baotou 014010, Inner Mongolia ，China ）Abstract: The questions posed by academician XU Zu-yao in the paper “ Comment on the paper 《Study on the nucleation of bainite ferrite 》authored by LIU Zong-chang et. al ” were expounded and replied. It is pointed out that the new experimental observation of the bainite ferrite nucleation at the grain boundary validates the general rule of nucleation. According to the experimental observation, the calculated values of the critical crystal nucleus dimension and the critical nucleus nucleation energy o f the bainite ferrite, which are as follows, a* =16.7 nm, b=25 nm and 270 J•mol -1, are reasonable. The existence of carbon depleted region in austenite is a common fact. Furthermore, the formation of the carbon depleted region in the incubation period of bainite transformation has been measured. Spinodal decomposition and the formation of rich and poor carbon areas in austenite cannot be confused with each other. The incoordinate heat activation transition mechanism of bainite transformation is set forth. The analysis of lots of TTT diagrams and the actual measured results show that the nucleation and growth of bainite ferrite cannot be by means of diffusion. We cannot agree with academician XU Zu-yao’s viewpoints about above issues.Key words: bainite ferrite; grain boundary nucleation; diffusion; shear; heat activation transition关于贝氏体相变的形核-长大机制一直是切变学派和扩散学派论争的核心问题。

第 3 期第 100-108 页材料工程Vol.52Mar. 2024Journal of Materials EngineeringNo.3pp.100-108第 52 卷2024 年 3 月球磨时间对Ti -13Nb -5Sn 牙科合金耐蚀与耐磨性能的影响Effect of ball milling time on corrosion and wear resistance of Ti -13Nb -5Sn dental alloys颉芳霞1，2*，陆东兴1，黄家兵1，张文成1，孙琪超1，何雪明1，2（1 江南大学 机械工程学院，江苏 无锡 214122；2 江苏省食品先进制造装备技术重点实验室，江苏 无锡 214122）XIE Fangxia 1，2*，LU Dongxing 1，HUANG Jiabing 1，ZHANG Wencheng 1，SUN Qichao 1，HE Xueming 1，2（1 School of Mechanical Engineering ，Jiangnan University ，Wuxi 214122， Jiangsu ，China ；2 Jiangsu Key Laboratory of Advanced Food ManufacturingEquipment and Technology ，Wuxi 214122，Jiangsu ，China ）摘要：采用粉末冶金法制备了Ti -13Nb -5Sn 牙科合金，研究了不同球磨时间（3，12，24，48 h ）对粉末特性、材料微观结构、电化学腐蚀和摩擦学行为的影响规律。

结果表明：随着球磨时间从3 h 增加至48 h ，粉末形貌由大块状逐渐变成细小颗粒，部分Nb 和Sn 原子扩散到Ti 晶格中，形成了一定体积的Ti （Nb ）和Ti （NbSn ）固溶体；等轴α-Ti 减少转变为柱状的晶界α-Ti ，网篮组织转变为魏氏组织；动电位极化曲线显示，合金在人工唾液（AS ）和模拟体液（SBF ）中的腐蚀电位（E corr ）和极化电阻（R p ）呈上升趋势，腐蚀电流密度（I corr ）呈下降趋势，α-Ti 减少，β-Ti 增多，使得合金耐腐蚀性能提升；合金的硬度升高，而摩擦因数、磨痕深度和磨损率逐渐降低，细化粉末在烧结中会产生更多的晶界，使得合金的耐磨性能提升。

LJournal of Alloys and Compounds 253–254(1997)87–89Nanocrystalline hydrogen storage alloys for rechargeable batteriesH.Kronberger¨Institut f urTechnische Elektrochemie ,Getreidemarkt 9,A -1060Wien ,Austria AbstractAB -type intermetallic compounds were prepared by the melt spinning method.Structure analysis was carried out by X-ray5diffractometry,SEM and high resolution electron microscopy.The hydrogen storage capacity was determined by isothermic mass controlled absorption of hydrogen and by electrochemical charge/discharge cycles.A variation of the preparation parameters showed that a nanocrystalline structure was achieved at high cooling rates.Nanocrystalline AB -compounds show improved electrochemical 5properties.Keywords :Nanocrystalline;Hydride;Electrodes;Batteries;Cells1.Introductiondiameter was used.The influence of the protective gas atmosphere was studied and the cooling rate was changed The enhancement of grain boundary diffusion of hydro-by a stepwise variation of the gas pressure and the gen in polycrystalline AB -compounds by the formation of rotational speed (Table 1)5additional phases was found to accelerate the limiting transport processes [1].From this point of view the 2.2.Electrode preparationproperties of materials in an amorphous or nanocrystalline state also are of special interest.Although thin layers of The materials were obtained as short ribbons or flakes,amorphous LaNi prepared by r.f.sputtering were investi-immersed in a copper solution as used for electroless 5gated by some authors,we were looking for a suitable deposition and finely ground in a mortar.The resulting method for the production of substantial amounts of powders were supplied with a protective copper layer by amorphous or nanocrystalline material from AB -com-chemical reduction.Electrodes were formed by attaching 5pounds for the preparation of electrodes.Several papers the material to a nickel net using a fluoro–organic binder.have been published concerning the electrochemical be-A more detailed description of the melt spinning process haviour of microcrystalline AB -compounds produced by and the electrode preparation was given in Ref.[1].5rapid solidification [2]in a melt spinning device,but apparently the cooling rates that are usually achieved with Table 1this method are too low to produce amorphous materials.Preparation conditions Moreover,the influence of preparation parameters on the Basic comp Gas Gas pressure /bar Rotational speed/r.p.m.properties of these electrode materials,in particular con-I Ar 1.100/1.0001500cerning kinetic aspects,still remain unclear.I He 1.100/1.0002000II Ar 1.100/1.0002000II He 1.000/0.9201500III Ar 1.100/1.00020002.ExperimentalIII He 0.990/0.9102000I He 0.650/0.55020002.1.Preparation and rapid solidificationII He 0.660/0.5802000III He 0.640/0.5602000Electrode materials were prepared from I He 0.350/0.3001500I He 0.160/0.1001100RENi Co Mn Al (RE 5La or Mischmetall)by melt 3.50.80.40.3II He 0.160/0.0902000spinning.IIIHe0.160/0.1002500A melt spinning device with a copper wheel of 30cm0925-8388/97/$17.00©1997Elsevier Science S.A.All rights reserved PII S0925-8388(96)02921-088H.Kronberger/Journal of Alloys and Compounds253–254(1997)87–89Basic compounds:I5LaNi Co Mn Al;II5phase with a CaCu-structure could be detected both in3.50.80.40.35MmNi Co Mn Al,30%La in Mm;III5samples prepared by induction melting and melt spinning.3.50.80.40.3MmNi Co Mn Al,50%La in Mm;gas pressure5Apart from a slight line broadening no change of com-3.50.80.40.3gas reservoir/meltspinning chamber.position or crystal structure was observed in rapidlysolidified samples.2.3.Structure analysis SEM pictures of samples produced in helium atmos-phere at pressures below550mbar showed a needlelike Structure analysis was carried out by X-ray diffrac-(1–3m m diameter)texture vertical to the surface of the tometry(Siemens D500)and the Debye–Scherrer method.ribbons orflakes respectively.The average grain size and the influence of lattice distor-A calculation of the grain size by evaluation of the XRD tions were estimated by evaluation of the diffraction line peak broadening yielded values ranging from25to60nm broadening.Additional investigations were done by scan-indicating that the average grain size is lower than the ning electron microscopy and transmission electron micro-average diameter of the texture profiles by at least one scopy.order of magnitude.Additional examinations using a high resolving TEM 2.4.Storage capacity revealed that a major part of the material remained in ananocrystalline state with a grain size significantly below The hydrogen storage capacity was determined by mass10nm.The TEM pictures also showed some isolated controlled isothermic absorption of hydrogen at808C.grains with a diameter between10–300nm embedded in amatrix of nanocrystalline material(Fig.1).2.5.Electrochemical characterization Samples prepared in Ar atmosphere at a lower coolingrate exhibited a microcrystalline hexagonal structure with a Electrochemical measurements were carried out in6M grain size between0.5and3m m.KOH using a saturated mercurosulphate reference elec-A more detailed examination of the XRD patterns trode.The storage capacity was measured by constant additionally revealed significant differences of the intensity current charge/discharge cycles at different current den-distribution.Fig.2shows the XRD patterns ofNi Co Mn Al prepared by induction melting(A)3.50.80.40.3and by melt spinning with a lower(B)and a higher(C)cooling rate.Obviously the002peak of material(B)is 3.Results and discussion significantly increased.Material(A)shows an intensitydistribution similar to the values calculated for LaNi and5 3.1.Melt spinning parameters and cooling rate(C)shows a less distinct deviation like(B).As the samples(B)and(C)consisted of short ribbons orflakes they were The efficiency of rapid solidification by melt spinning is not randomly attached to the carrier like a powder(A).The determined by different parameters and a nanocrystalline intensity increase of the002peak of(B)is apparently due or amorphous state can be achieved only by sufficient to a predominant orientation of the c-axis of the hexagonal cooling rates.crystals vertical to the surface of the ribbons.A further Although the rotational speed and the heat transport increase of the cooling rate causes a more random orienta-inside the copper wheel plays a dominant role,the coolingrate is also influenced by the intensity and time of thecontact between the liquid metal and the surface of thecopper wheel.The protective gas atmosphere can enhancethe contact time and contributes to the cooling process bymeans of its specific heat and specific thermal conduc-tivity,its viscosity and pressure.The cooling rate was notmeasured directly but structural changes of samples pre-pared in helium atmosphere at reduced pressures indicate,that a maximum is obtained at pressures below300mbar.3.2.Structural changes by melt spinningMmNi Co Mn Al like other LaNi-related inter-3.50.80.40.35metallic compounds crystallize in the hexagonal CaCu-5structure.Previous experiments had shown,that LaNi and5related compounds are difficult to get in an amorphousstate.From Debye–Scherrerfilms a uniform crystalline Fig.1.TEM picture of material(C).H.Kronberger/Journal of Alloys and Compounds253–254(1997)87–8989to well established diffusion paths for hydrogen atomsalong the numerous grain boundaries.A comparisonbetween the discharge capacities and the correspondingcapacity values calculated from isothermic hydrogen de-sorption experiments showed only negligible differencesbetween the materials as supplied and nanocrystallinematerials.In contrast to that,melt-spun micro-crystalline sampleswith oriented crystallization(B)showed very poor kineticproperties probably indicating an anisotropy of hydrogendiffusion inside the single crystals.4.ConclusionNanocrystalline materials can be prepared from AB-5type intermetallic compounds by optimization of the meltspinning process.Electrodes prepared from these materialsshow excellent activation behaviour and improved electro-chemical properties.Microcrystalline material with ori-ented crystallization prepared at a lower cooling rateexhibits poor kinetic properties.Fig. 2.XRD-patterns of polycrystalline samples before(A)and aftermeltspinning(B,C)at different cooling rates.AcknowledgmentsThe investigations were carried out in cooperation with tion of the grains.Thisfinding is in good agreement with¨the Institut fur Experimentalphysik der Technischen Uni-the results of high resolution TEM.¨versitat Wien.The TEM pictures were supplied by the Isothermic hydrogen absorption experiments showed¨Institut fur Angewandte und Technische Physik.The only negligible differences in the storage capacities be-author thanks Prof.H.Kirchmayr,Prof.Ch.Fabjan and tween the materials as supplied and nanocrystalline materi-Doz.P.Pongratz for their encouragement.als.3.3.Electrochemical behaviourReferencesNanocrystalline materials(C)generally showed im-proved discharge characteristics with distinct potential[1]H.Kronberger,GDCh Monographie,2,Elektrochemie und Werk-stoffe,GDCh,Frankfurt,1995,pp.411–425.plateaux after a very few activation cycles in comparison[2]R.Mishima,H.Miyamura,T.Sakai,N.Kuriyama,H.Ishikawa and to the materials as supplied(A).The improvement ofI.Uehara,J.Alloys Comp.,192(1993)176–178.activation behaviour and kinetic properties is probably due。

退火温度对Pb(Mg1/3Nb2/3)O3-PbTiO3薄膜结构和性能的影响赵媛媛，胡广达（济南大学材料科学与工程学院，山东济南250022）摘要：采用溶胶-凝胶法在LaNiO3/Si(100)衬底上制备Pb(Mg1/3Nb2/3)O3-PbTiO3薄膜，退火温度在500℃~650℃之间，主要研究了退火温度对薄膜结构和性能的影响。

结果表明：提高退火温度可以有效地抑制焦绿石相，改善薄膜的电学性能。

值得注意是我们得到纯钙钛矿相结构薄膜的退火温度降低至600℃，650℃下退火薄膜在10μm×10μm测试区域内的平均压电响应高达~180pm/V。

关键词：溶胶-凝胶法；Pb(Mg1/3Nb2/3)O3-PbTiO3薄膜；退火温度；压电响应Effect of The Annealing Temperature on The Structure and Properties ofPb(Mg1/3Nb2/3)O3-PbTiO3Thin FilmZHAO Yuanyuan,HU Guangda(School of Materials Science and Engineering,University of Jinan,Jinan250022,China) Abstract:The Pb(Mg1/3Nb2/3)O3-PbTiO3thin films were deposited on LaNiO3/Si(100)substrates annealed at the temperature ranging from500℃to650℃by a sol-gel method.The effect of annealing temperature on the structure and properties of Pb(Mg1/3Nb2/3)O3-PbTiO3thin film was investigated.The experimental results show that the pyrochlore phase can be effectively suppressed by increasing annealing temperature.At the same time,the electric properties of films were improved.The annealing temperature required to obtain the film with a pure perovskite phase can be lowered to600℃.It was noteworthy that the average piezoelectric coefficient of the film annealed at650℃in the10μm×10μm detected areas was as high as180pm/V.Key word:Sol-gel method;Pb(Mg1/3Nb2/3)O3-PbTiO3thin film;annealing temperature;piezoresponsePb(Mg1/3Nb2/3)O3-PbTiO3(PMN-PT)是一种典型的弛豫铁电体材料，它在准同型相界处具有大的压电响应和大的机电耦合系数，因此使其在微机电系统(MEMS)中有很大的应用前景[1]。

Materials Science and Engineering A302(2001)141–150Grain boundary and triple junction migrationL.S.Shvindlerman a,b,*,G.Gottstein ba Institute of Solid State Physics,Russian Academy of Sciences,Chernogolo6ka,Moscow District142432,Russiab Institut fu¨r Metallkunde und Metallphysik,RWTH Aachen,Kopernikusstr.14,D-52074Aachen,GermanyAbstractThe current status and latest achievements of grain boundary(GB)and triple junction(TJ)migration in metals are reviewed. The migration of90° 112 planar tilt symmetrical and asymmetrical GB in specially grown Bi-bicrystals driven by magnetic force and the dependence of GB mobility on temperature,driving force and the direction of motion are addressed.The motion of low-and high angle planar tilt 112 and 111 GBs moved by shear stresses and the peculiarities of such a motion are considered. In particular,the sharp transition from low-to high-angle boundaries was observed.In practice the motion of a straight GB is the exception rather than the rule.The shape of a moving GB is a source of new and usefulfindings concerning GB migration. The experimentally derived shape of a GB in Al-bicrystals was compared with theoretical calculations in the Lu¨cke–Detert approximation.The experimental and theoretical results of a motion of grain boundary systems with triple junctions are presented.Their impact on the kinetics of microstructure evolution and,in particular,on Von Neumann–Mullins relation is outlined.©2001Elsevier Science B.V.All rights reserved./locate/msea1.Magnetically driven grain boundary motionA grain boundary(GB)migration occurs when the boundary displacement leads to the reduction of a total energy of the system.There are two ways by which this may be accomplished.Thefirst uses free energy of the GB itself,the other utilizes a free energy difference of the adjacent grains.The most frequently used method is the displacement of a curved GB[1–4].However,the obtained mobilities can,therefore,not be related to a specific GB structure,while by using the second type of driving force a plane boundary can be forced to move.A bicrystal with grains that have some orientation dependent property like elastic constants or magnetic susceptibility can be utilized in this case.This driving force does not depend on boundary properties.Such conditions,in particular,can be obtained by the action of a magneticfield on a bicrystal of a material with anisotropic magnetic susceptibility[3,4].The origin of the driving force for grain boundary migration in a magnetically anisotropic material was considered by Mullins[5].The expression for the driv-ing force,as applied to bismuth,reads P=v0D2H2(cos2[1−cos2[2)(1)where H is the magneticfield strength,D is the differ-ence of the susceptibilities parallel and perpendicular to the trigonal axis,[1and[2are the angles between the magneticfield and the trigonal axes in both grains of the Bi-bicrystal.Three efforts were made in the past to utilize a magneticfield for the study of GB kinetics in Bi by Goetz,Mullins and Fraser[6,7],however,no specific boundary motion was investigated.Our experiments were carried out on bicrystals of high purity(99.999%)bismuth[8,9].Symmetrical and asymmetrical( =45°)pure tilt boundaries with90° 112 misorientation were examined(Fig.1,the devia-tion of asymmetrical GB from symmetrical position equals ).The experiments were carried out using the high magneticfield facilities of the National High Magnetic Field Laboratory in Tallahassee,FL,USA.A resistive, steady-state20-T bitter magnet with50-mm bore di-ameter was used,and afield strength between0.80×107and1.59×107A m−1was applied.The magnetic field was imposed on the samples at different tempera-tures ranging from210to260°C.*Corresponding author.Tel.:+7-95-9132324;fax:+7-64-412654.E-mail address:shvind@issp.ac.ru(L.S.Shvindlerman).0921-5093/01/$-see front matter©2001Elsevier Science B.V.All rights reserved. PII:S0921-5093(00)01366-6L .S .Sh 6indlerman ,G .Gottstein /Materials Science and Engineering A 302(2001)141–150142Fig.1.Geometry of investigated bicrystals with 90° 112 tilt,(a)symmetrical;and (b)asymmetrical boundaries.The possibility to change the magnitude of the driv-ing force for boundary migration by exposing the sam-ples to magnetic fields of different strength yields the unique opportunity to change the driving force on a specific grain boundary and thus,to obtain the driving force dependence of grain boundary velocity (Fig.2).The experiments unambiguously confirmed that grain boundaries in Bi-bicrystals actually move under the action of a magnetic driving force.The observed linear dependence of boundary displacement on annealing time proves the free character of its motion.To prove that boundary motion was caused exclu-sively by the magnetic driving force,the experiment was carried out in two different ways.First,a specimen was mounted in a holder such that the c -axis ( 111 )of crystal 1was directed parallel to the field (Fig.3a).The 111 axis in crystal 2in this case was perpendicular to the field,and the grain boundary moved in the direc-tion of the latter crystal due to its higher magnetic free energy.Second,a specimen was mounted in a position where the axis 111 in crystal 2was close to the field direction,and the corresponding axis in crystal 1was perpendicular to the field.The direction of boundary motion in this case was opposite,from crystal 2toward crystal 1(Fig.3b).This result provides unambiguous evidence that the grain boundaries in the bicrystals were forced to move by the magnetic driving force only.In addition,some bicrystals were annealed in a magnetic field in both positions,and boundary motion in opposite direction was observed in the same specimen dependent on its position with regard to the magnetic field.In the current experiments,we investigated the mi-gration of two differently inclined 90° 112 tilt grain boundaries,namely a symmetrical and an asymmetrical boundary (Fig.1).In contrast to the symmetric tilt boundary,for the asymmetric tilt boundary the measured boundary mo-bilities were found to be distinctly different for motion in opposite directions (Fig.4).There are several poten-tial reasons for this anisotropy.First,there is an essen-tial difference in the distance between the crystallographic planes on each side of the boundary.An estimation shows that this factor may change the velocity of grain boundary motion;however,this factor is unlikely to change the velocity of grain boundarymotion by more than 20%,which is distinctly less than the observed effect.Second,because grain boundary motion in Bi-bicrystals may be influenced by impurity drag,the difference in the diffusivity of impurities in two opposite directions in the anisotropic structure of Bi should be taken into consideration.In this respect it is interesting that the symmetric tilt boundary exhibited a much higher mobility than the asymmetric tilt boundary and did not show a dependence of boundary mobility on the sense of motion (Fig.4).In any event,if this asymmetry of grain boundary mobility holds also for other metals,it would have a serious impact on our understanding of grain boundaryFig.2.Dependence of the velocity of a 90° 112 symmetrical tilt boundary on the magnetic driving force.Fig.3.Geometry of investigated bicrystals and sense of driving force P with regard to direction of the magnetic field H .L.S.Sh6indlerman,G.Gottstein/Materials Science and Engineering A302(2001)141–150143 Fig.4.(a)Normalized displacement of a grain boundary vs.annealing time for the same grain boundary moving in opposite directions;(b) temperature dependence of mobility of90° 112 symmetrical( )and asymmetrical( , )boundaries in Bi-bicrysytals: –trigonal axis in the growing grain is parallel to the growth direction; –trigonal axis in the growing grain is perpendicular to the growth direction.motion,since the mobility of a grain boundary iscommonly conceived as not dependent on its directionof motion.2.Influence of external shear stresses on grainboundary migrationA method to activate and investigate the migration ofplanar,symmetrical tilt boundaries in aluminum bicrys-tals under the influence of an external shear stress wasintroduced.It was shown that low-as well as high-an-gle boundaries could be moved by this shear stress.From the activation parameters for grain boundarymigration,the transition from low-to high-angleboundaries can be determined.The migration kineticswere compared with results on curved boundaries,andit was shown that the kinetics of stress induced motionwere different from the migration kinetics of curvaturedriven boundaries.In1952,Washburn,Parker et al.[10,11]investigatedplanar low-angle boundaries in Zn under the influenceof an external shear stress and observed the motionwith polarized light in an optical microscope.Thecurrent study was aimed at probing the effect of amechanical,shear stressfield on planar low-and high-angle boundaries[12].For the investigations bicrystals of different purities(1and7.7ppm impurity content)with 112 and 111 tilt grain boundaries with misorientation angles in a range from4to32°were grown.The grainboundary motion was measured in situ with an X-rayinterface continuous tracking device(XICTD).Symmetrical low angle tilt boundaries consist of peri-odic arrangements of a single sets of edge dislocations.An external shear stress perpendicular to the boundaryplane will cause a force on each dislocation and insummary a driving force on the boundary.The sampleswere exposed to a shear stress ranging from10−1to 10−3MPa.In aluminum(purity99.999%)the yield stress is15–20MPa,hence the applied shear stress is definitely in the elastic range.High angle symmetrical tilt boundaries also can be formally described as an arrangement of a single set of edge dislocations except that the dislocation cores over-lap and the identity of the dislocations gets lost in the relaxed boundary structure.First of all we want to show that irrespective of the magnitude of the angle of rotation,grain boundaries can be moved under the action of the applied shear stress.Fig.1shows the dependence of the grain boundary velocity on the applied mechanical shear stress for two different 112 -tilt boundaries.From Fig.5we can see that obviously,both the low-and the high-angle grain boundary move under the influence of the shear stress and the grain boundary velocity changes in proportion to the stress in both cases. Fig.6shows the dependence of the activation en-thalpy on misorientation angle for different tilt axes and impurity content.For low angle grain boundaries wefind a constant activation enthalpy of D H=1.28eV and for high angle grain boundaries D H=0.85eV.The transition from low-to high-angle grain boundaries is Fig.5.Dependency of the grain boundary velocity on the external shear stress for two symmetrical 112 tilt boundaries.L .S .Sh 6indlerman ,G .Gottstein /Materials Science and Engineering A 302(2001)141–150144Fig.6.Activation enthalpy vs.misorientation angle for 112 and 111 tilt boundaries with different impurity content.see a strong dependency of the activation enthalpy on the misorientation angle,i.e.on the grain boundary structure.There is also a clear difference between the activation enthalpies for the stress induced motion of the planar high angle grain boundaries and the curva-ture driven migration of the curved high angle grain boundaries.Obviously,a dislocation in a high angle grain boundary does not relax completely its strain field and correspondingly,a biased elastic energy density induced by an applied shear stress will induce a force on all dislocations that comprise the grain boundary.The results prove that grain boundaries can be driven by an applied shear stress irrespective whether low-or high-angle boundaries.Obviously,the motion of the grain boundary is caused by the movement of the dislocations,which compose the grain boundary.The activation enthalpy for the low angle grain boundaries amounts to D H =1.28eV and is comparable with the activation enthalpy of bulk self-diffusion in aluminum.For the high angle grain boundaries we found an activation enthalpy of D H =0.85eV,which is compara-ble to the activation enthalpy for grain boundary diffu-sion in aluminum.The motion of an edge dislocation in a fcc crystal in reaction to an applied shear stress ought to be purely mechanical and not thermally activated.Obviously,the observed grain boundary motion is a thermally acti-vated process controlled by diffusion.To understand this,one has to recognize first that grain boundary motion is a drift motion since it experiences a driving force that is smaller compared with thermal energy.Moreover,real boundaries are never perfect symmetri-cal tilt boundaries but always contain structural dislo-cations of other Burgers vectors.These dislocations have to be displaced by nonconservative motion to make the entire boundary migrate.The climb process requires diffusion,which can only be volume diffusion for low angle grain boundaries but grain boundary diffusion for high angle grain boundaries according to the observed activation enthalpies.The different behavior of curvature driven grain boundaries is not due to the curvature of the boundaries rather than due to a different effect of the respective driving force.While an applied shear stress couples with the dislocation content of the boundary in a curved grain boundary each individual atom experi-ences a drift pressure to move in order to reduce curvature.3.Shape of the moving grain boundariesThe principal parameter which controls the motion of a grain boundary is the grain boundary mobility.In practically all relevant cases the motion of a straightFig.7.Dependency of the activation enthalpy on misorientation angle for curvature driven and planar 111 grain boundaries,and planar 112 grain boundaries (open symbols [14];filled [12]).revealed by a conspicuous step of the activation en-thalpy at a misorientation angle of 13.6°.There exists no evidence,that the deviations from the activation enthalpy levels for low-and high-angle boundaries show a dependence of the activation en-thalpy on grain boundary structure.From Fig.6we conclude that 112 -and 111 -tilt boundaries move with the same activation enthalpies when exposed to a mechanical stress.This holds for low angle as well as for high angle symmetrical tilt boundaries.Previous experiments on curvature driven 111 tilt boundaries in aluminum bicrystals showed a strong misorientation dependence of the activation enthalpies [13].For comparison,we conducted curvature driven boundary migration experiments on 111 tilt boundaries.The driving force was a constant capillary force,p =|/a where a is the width of the shrinking grain (quarter-loop technique).The typical values of a driving force in both types of our experiments are nearly the same,p 103J m −3.In Fig.7the dependence of the activation enthalpy on the misorientation angle for the curved and the planar grain boundaries is shown.For the curvature driven grain boundaries our results are in good agree-ment with previous experimental data [14]and one canL .S .Sh 6indlerman ,G .Gottstein /Materials Science and Engineering A 302(2001)141–150145grain boundary is the exception rather than the rule.That is why the shape of a moving grain boundary is of interest and it will be shown that the grain boundary shape is a source of new interesting and useful findings of grain boundary motion,for the interaction of a moving grain boundary with mobile particles,in partic-ular.The experimentally derived shape of grain boundary ‘quarter-loop’[15]in Al-bicrystals of differ-ent purity was compared with theoretical calculations in the Lu ¨cke–Detert approximation.The shape of a moving GB quarter-loop was deter-mined analytically under the assumption of uniform GB properties and quasi-two-dimensionality [15]:y (x )=ÁÃÍÃÄ−(b F −b L )arc cos sin [e x*/b F+a2−b L y 2+b F arc cos(e b F ln(sin [)−x /b F )05x 5x*a 2−b Ly2+b L arc cos(e b L ln(sin [)−x*((b L /b F )−1)−x /b L)x ]x*(2)where b L is:b L =b F (arc cos(sin [/e x*/b F +[−(y /2)−a /2))arc cos(sin [/e x*/b F )−(y /2)(3)The parameters in Eq.(2)are the width of the shrinking grain a /2,the angle [of the grain boundary with the free surfaces in the triple junction,the critical point x *,and b F and b L :b L =m L |/V ;b F =m F |/V ,where m L and m F are the GB mobilities for ‘loaded’and ‘free’GB,respectively,|is GB surface tension,V is a velocity of a quarter-loop.The first two parameters can be measured directly in the experiment.The latter two have to be chosen in an approximate way to fit the experimentally derived grain boundary shape.The point x *is the point of intersection ‘free’and ‘loaded’segments of the GB.The value m L /m F is a measure for how drastic the change between the ‘free’and the ‘loaded’part in the point of intersection will be.Corresponding experi-ments were carried out on aluminum bicrystals with a 40.5° 111 tilt boundary.The samples differed by the amount of dissolved impurities.Bicrystals with a total impurity content of 0.4,1.0,3.6,4.9and 7.7ppm were studied.The investigation proves that the influence of the impurity atoms on grain boundary properties and behavior is rather strong even in very pure materials.The experimentally measured shape of a moving grain boundary (Al with 1.0ppm impurities)and the shape calculated according to equation which does not take into consideration impurity drag,are compared in Fig.8.The large discrepancy is obvious and apparently due to the neglect of boundary–impurity interactions.How-ever,with m L and m F determined as explained above the measured boundary shape can be successfully fitted by Eq.(2))using only x *as a free fit parameter (Fig.9).The same holds for the reversed-capillary technique.Any attempt to fit the shape by assuming a freely moving boundary fails,but good agreement between experiment and theory can be observed when impurity drag and thus,different mobilities are taken into ac-count (Fig.10)[16].As mentioned above,the shape of a moving grain boundary is a new source of information on grain boundary migration.One example is given in Fig.11,where the value of the critical distance x *,normalized by the driving force (in terms of the quarter-loop width a )is plotted versus the impurity content.In accordance with the Lu ¨cke–Detert theory the critical velocity 6*(and rigidly bound to it the position of the critical pointparison between experimental data (solid line)and calcu-lated shape (dotted line)disregarding segregation.Fig.9.Experimentally observed (solid line)and calculated (Eq.(3),dotted line)grain boundary shape for Al with an impurity content of (a)1.0;(b)3.6ppm (quarter-loop technique).L.S.Sh6indlerman,G.Gottstein/Materials Science and Engineering A302(2001)141–150146Fig.10.Experimentally observed and calculated shape accounting for drag effect,(shaded area);neglecting the drag effect(dashed line)(Fe–3% Si,reversed-capillary technique).Fig.11.Dependence of critical point x*/a on(a)impurity content;(b)reciprocal impurity content.x*on the quarter-loop)is determined by the balance between the maximum force of interaction of the impu-rity atoms with the boundary and the force,which is imposed by the energy dissipation caused by boundary motion across the matrix.The difference of the impu-rity drag for grain boundaries in samples with different amount of impurities is caused by the adsorption of impurities at the grain boundary.According to theory, the velocity should decrease proportionally to the in-verse of the concentration of adsorbed atoms.There-fore x*should increase with decreasing impurity content,as observed qualitatively(Fig.11)[15].How-ever,a linear relation between the inverse of the impu-rity concentration and6*,i.e.x*,is not observed over the whole concentration range,which indicates a more complicated interaction of adsorbed atoms with the grain boundary.In such a case,x*/a should increase more strongly with decreasing impurity content than it does linearly.This tendency is indeed observed (Fig.11).4.Dragging effect of triple junction on grain boundary motionIn spite of the fact that a line(or column)of intersec-tion of three boundaries constitutes a system with spe-cific thermodynamic properties was realized more than 100years ago(by Gibbs),the kinetic properties of this subject,in particular the mobility of triple junctions, and their influence on grain growth and relevant pro-cesses were ignored up to now.Although the number of triple junctions in polycrystals is comparable in magni-tude with the number of boundaries,all peculiarities in the behavior of polycrystals during grain growth were solely attributed to the motion of grain boundaries so far.It was tacitly assumed in theoretical approaches,L.S.Sh6indlerman,G.Gottstein/Materials Science and Engineering A302(2001)141–150147 computer simulations and interpretation of experimen-tal results that triple junctions do not disturb grainboundary motion and that their role in grain growth isreduced to preserve the thermodynamically prescribedequilibrium angles at the lines(or the points for2-Dsystems)where boundaries meet.The most prominentexample of how this assumption determines the funda-mental concepts of grain structure evolution gives theVon Neumann–Mullins relation[17,18].No doubt this relation forms the basis for practicallyall theoretical and experimental investigations as well ascomputer simulations of microstructure evolution in2-D polycrystals in the course of grain growth.Thisrelation is based on three essential assumptions,namely,(i)all grain boundaries possess equal mobilitiesand surface tensions,irrespective of their misorientationand crystallographic orientation of the boundaries;(ii)the mobility of a grain boundary is independent of itsvelocity;(iii)the third assumption relates directly to thetriple junctions,namely,they do not affect grainboundary motion;therefore,the contact angles at triplejunctions are in equilibrium and,due to thefirst as-sumption,are equal to120°.As it was shown in[17,18],for2-D grain,the rate ofchange of the grain area S can be expressed byd S d t =−A b7d (4)where A b=m b|;m b being the grain boundary mobility, |is the grain boundary surface tension.If the grain were bordered by a smooth line,the integral in Eq.(4)would equal2y.However,owing to the discontinuous angular change at every triple junc-tion,the angular interval D =y/3is subtracted from the total value of2y for each triple junction. Consequently,d S d t =−A b2y−n y3=A b y3(n−6)(5)where n is the number of triple junctions for each respective grain,i.e.the topological class of the grain. Thus,the rate of area change is independent of the shape of the boundaries and determined by the topo-logical class n only.Grains with n\6will grow and those with n B6will disappear[18].The existence of triple junctions drastically affects the kinetics of grain growth.To discuss this problem quan-titatively the mobility of a triple junction should be measured.However,the steady-state motion of a grain boundary system with a triple junction is only possible in a very narrow class of geometrical configurations. Two of these special boundary systems were investi-gated in[19–21]under three main assumptions.Two of them comply with the assumptions(1)and(2)of the Von Neumann–Mullins consideration,while the third one is determined by Eq.(2):the normal GB displace-ment rate6is proportional to the GB curvature K. As shown in[19],the model grain boundary system (Fig.12)can move steadily,and the analysis of its motion permits us to understand the influence of the finite mobility of a triple junction on the migration of GBs.The considered grain boundary system(Fig.12)con-sists of three grain boundaries,two of them are curved with a common triple junction.During steady-state motion of the system the velocity V parallel to the x-axis(Fig.12)is related to the rate of normal displace-ment6:6=V cos =V y%[1+(y%)2]1/2(6)where y(x)is the shape of the positive part(upper part in Fig.12)of the curved boundary.Due to the mirror symmetry of the problem relative to the x-axis,the shape of the lower part boundary is the negative equivalent.Then the equation for the steady-state shape of the moving grain boundaryy¦=−Vm by%(1+(y%)2)(7)Eq.(7),restricted by three boundary conditions,per-mits us tofind the desired shape y(x)and the velocity V of the moving grain boundary(Fig.12)y(0)=0y( )=a2y%(0)=tan[(8) The meaning of the length a and the angle[is clear from Fig.12.A driving force|(2cos[−1)acts on the triple junction from the curved boundaries.Introducing the mobility of the triple junction m Tj,its velocity reads V Tj=m Tj|(2cos[−1)(9) Due to the fact that the driving force acting on the grain boundary is a pressure and the driving force onFig.12.Configuration of grain boundaries at a triple junction during steady-state motion for n B6.L .S .Sh 6indlerman ,G .Gottstein /Materials Science and Engineering A 302(2001)141–150148Fig.13.Angle [as a function of \,(a)for n B 6(Eq.(12));(b)for n \6(Eq.(18)).x =a 2[c 1=ln(sin [)c 2=−y2−[(10)The velocity V of steady-state motion of the system is V =2[m b |a(11)The steady-state value for the angle [can be found from the equation.2[2cos [−1=m Tj am b =\(12)If a triple junction is mobile and does not drag grain boundary motion,the criterion \ and [ y /3,i.e.the equilibrium angular value at a triple junction in the uniform grain boundary model.In contrast,how-ever,when the mobility of the triple junction is rela-tively low (strictly speaking,when m Tj a m b )then [ 0(Fig.13).It should be stressed that the angle [is strictly defined by the dimensionless criterion \,which,in turn,is a function of not only the ratio of triple junction and grain boundary mobility,but of the grain size as well.Experimental investigations [20]were based on the considered grain boundary system (Fig.12).It was shown that triple junctions do possess a finite mobility.It was found that the vertex angle [at the triple junction could deviate distinctly from the equilibrium value,when a low mobility of the triple junction hin-ders the motion of the grain boundaries.In fact,a transition from triple junction kinetics to grain boundary kinetics was observed (Figs.14and 15).For grains with topological class greater than six let us consider the steady-state motion of a grain boundary system shown in Fig.16with the same set of assump-tions applied to the previous boundary system,namely,uniform grain boundary properties and quasi-two-di-mensionality [21,22].The steady-state motion of this system is determined by the system of Eqs.(7)and (8)only with different boundary and initial conditions y %(0)= y %(x 0)=tan [y (0)=0(13)The velocity of the triple junction motion can be expressed as (Fig.3)V Tj =m Tj |(1−2cos [)(14)Like in the previous case,Eqs.(5)and (13)define the considered problem completely.Fig.14.The angles in the tip of the tricrystal half-loop at differenttemperatures.(Zn tricrystal,misorientation angles of the tilt grain boundaries are 46° 1011 ,43° 1011 and 3°).Fig.15.The temperature dependence of the criterion \of the investigated Zn tricrystal.the triple junction is a force,the dimensions of grain boundary and triple junction mobility are different,so that their ratio m b /m Tj has the dimension of a length.For the configuration in Fig.12,Eqs.(7)and (8)define the problem completely.The solution can be expressed as [19]:y (x )=x arc cos(e−x /x +c 1)+c 2。

无机非金属材料专业英语单词abrasive [ ə'breisiv ]n. 磨料a. 磨蚀的，磨损的agate [ 'æɡət ]n. 玛瑙alite [ 'eilait ]n. 硅酸三钙石（C3A）alkali resistance [ 'ælkəlai ri'zistəns]耐碱性，抗碱能力alumina [ ə'lju:minə ]n. 氧化铝amorphous phase [ ə'mɔ:fəs feiz]无定形相，非晶相ampoule [ 'æmpju:l ]n. 小玻璃瓶，筒，安瓿anhydrite [ æn'haidrait ]n. 硬（无水）石膏，CaSO4 anion [ 'ænaiən ]n. 阴离子anisotropic [ æn,aisəu'trɔpik ] a. 各向异性的，非均质的anneal [ ə'ni:l ]n. & v. 退火anomaly [ ə'nɔməli ]n. 反常现象，不规则anorthite [ æ'nɔ:θait ]n. 钙长石CaO·Al2O3·2SiO2 apatite [ 'æpətait ]n. 磷灰石apparent porosity [ ə'pærənt pɔ:'rɔsiti]显气孔率asbestos [ æz'bestɔs ]n. 石棉asphalt [ 'æsfælt ]n. 沥青basicity [ bə'sisəti ]n. 碱度，碱性batch bin [ bætʃ bin]配合料料仓batch feeder [ bætʃ 'fi:də]投料机，加料器bauxite [ 'bɔ:ksait ]n. 矾土，铝矾土belite [ 'bi:lait ]n. 二钙硅酸盐（水泥）binder [ 'baində ]n. 粘胶剂，粘结剂biocompatibility [ 'baiəukəm,pætə'biləti ]n. 生物相容性biological [ ,baiəu'lɔdʒik,-kəl ] a. 生物学的，用生物（如病菌等）对付敌人的bisque firing [ bisk 'faiəriŋ]素烧（初次焙烧）body [ 'bɔdi ]n. 坯体body-centered lattice[ 'bɔdi 'sentəd 'lætis]体心格子borate [ 'bɔ:reit ]n. 硼酸盐borax [ 'bɔ:ræks ]n. 硼砂Na2B4O7·10H2Ocalcine [ 'kælsain ]v. & n. 烧结，烧成calcite [ 'kælsait ]n. 方解石calcium [ 'kælsiəm ]n. 钙capillary [ kə'piləri, 'kæpi- ] a. 细作用（的）n. 毛细管catalyst [ 'kætəlist ]n. 催化剂cation [ 'kætaiən ]n. 阳离子cellular [ 'seljulə ] a. 细胞的，由细胞组成的，多孔的cellulose [ 'seljuləus ]n. & a. 纤维素，含纤维素的ceramic [ si'ræmik ] a. 陶瓷、陶器checker [ 'tʃekə ]n. 格子砖checker chamber [ 'tʃekə 'tʃeimbə]蓄热室chemical durability [ 'kemikəl ,djuərə'biləti]化学稳定性chemical vapour deposition (CVD) [ 'kemikəl 'veipə ,depə'ziʃən]化学气相沉积cleavage [ 'kli:vidʒ ]n. 解理clinker[ 'kliŋkə ]n. 熟料、熔块coagulation[ kəuæɡju'leiʃən ]n. 凝结、凝固作用，聚集、角凝coating [ 'kəutiŋ ]n. 涂层，涂料，涂盖层collagen [ 'kɔlə,dʒen ]n. 骨胶原combustion flue [ kəm'bʌstʃən flu:]烟道complex [ 'kɔmpleks ]n. & a. 复合物，络合物；复杂的configuration [ kən,fiɡju'reiʃən ]n. 构形；（电子）排布constituent [ kən'stitjuənt ]n. 成分，组分contamination [ kən,tæmi'neiʃən ]n. 污染，杂质convection [ kən'vekʃən ]n. 对流，传递coordination numbers [ kəu,ɔ:di'neiʃən 'nʌmbəs]配位数coordination polyhedron [ kəu,ɔ:di'neiʃən ,pɔli'hi:drən]配位多面体cord [ kɔ:d ]n. 条纹，条痕（玻璃缺陷）cordierite [ 'kɔ:diərait ]n. 堇青石2MgO·2Al2O3·5SiO2 corrosion-resistant [ kə'rəuʒən ri'zistənt] a. 抗腐蚀的corundum [ kə'rʌndəm ]n. 刚玉α-Al2O3covalent [kəuˈveilənt] a. 共价的crazing[ 'kreiziŋ ]n. 细裂，龟裂，碎纹裂creep [ kri:p ]n. 蠕变cristobalite [ kris'təu,bəlait ]n. 方石英critical value [ 'kritikəl 'vælju:]临界值cross-fired glass melting furnace [ krɔ:s 'faiəd ɡlɑ:s'meltiŋ 'fə:nis]横火焰池窑crown [ kraun ]n. 炉顶，窑拱crown flint glass [ kraun flint ɡlɑ:s]冕火石玻璃crucible [ 'kru:sibl ]n. 坩埚crystallinity [kristəˈlinəti]n. 结晶度，结晶性crystallization [ ,kristəlai'zeiʃən ]n. 结晶（作用），晶化cubic [ 'kju:bik ] a. 立方晶系的cubic body-centered [ 'kju:bik 'bɔdi 'sentəd]体心立方（晶格）cubic face-centered[ 'kju:bik feis 'sentəd]面心立方（晶格）cullet [ 'kʌlit ]n. 碎玻璃，废玻璃（料）curing [ 'kjuəriŋ ]n. 固化，熟化，养护damper [ 'dæmpə ]n. 挡板，烟道闸板deflocculant [ di'flɔkjulənt ]n. 反絮凝剂，解凝剂deformation [ ,di:fɔ:'meiʃən ]n. 变形degrade [ 'di'ɡreid ]v. 降（裂，分）解，降低，衰变dendrite [ 'dendrait ]n. 树枝石，树枝状结晶densification [ ,densifi'keiʃən ]n. 密实化desiccator [ 'desikeitə ]n. 干燥器（皿）deteriorate [ di'tiəriəreit ]v. 1、（使）变坏，（使）恶化；2、损坏，消耗devitrify [ di:'vitrifai ]vt. 析晶devitrite [di:ˈvitrait]n. 失透石dielectric constant [ ,daii'lektrik 'kɔnstənt]介电常数differential thermal analysis (DTA) [ ,difə'renʃəl 'θə:məl ə'næləsis]差热分析diffraction [ di'frækʃən ]n. 衍射diffusion [ di'fju:ʒən ]n. 扩散dilatation [ ,dailə'teiʃən, dilə- ]n. 膨胀，扩展dilatometer [ ,dilə'tɔmitə ]n. 膨胀仪diode [ 'daiəud ]n. 二极管dipole moment [ 'daipəul 'məumənt]偶极矩dislocation [ ,disləu'keiʃən ]n. 位错，位移dispersion [ dis'pə:ʃən ]n. 色散，分散displacement [ dis'pleismənt ]n. 位移，易位，取代distortion [ dis'tɔ:ʃən ]n. 扭曲，变形dolomite [ 'dɔləmait ]n. 白云石MgCO3·CaCO3 domain [ dəu'mein ]n. 畴，域，范围，铁电体的均一极化区donor level [ 'dəunə 'levəl]施主能级dopant [ 'dəupənt ]n. 掺杂剂dotted line [ 'dɔtid lain]虚线drawability [ ,drɔ:ə'biləti ]n. 可纺性（玻璃纤维），可拉伸性ductile [ 'dʌktail, -til ] a. 可延展的，易变形的earthenware [ 'ə:θənwεə ]n. 陶（瓦）器eddy [ 'edi ]n. 涡流，漩涡，螺旋efflorescence [ ,eflɔ:'resəns ]n. 粉化、风化elastic modulus [ i'læstik 'mɔdjuləs]弹性模量electronegativity [ i'lektrəu,neɡə'tivəti ]n. 电负性electrophoretic [ i,lektrəfə'retik ] a. 电泳的electrostatic [ i,lektrə'stætik ] a. 静电的，静电学的embossing [ im'bɔsiŋ ]n. 浮雕，压花，压纹emulsifier [ i'mʌlsifaiə ]n. 乳化剂enamel [ i'næməl ]n. 搪瓷endothermic [ ,endəu'θə:mik,-məl ] a. 吸热的end-port furnace [ end pɔ:t 'fə:nis] (或horseshoe-fired furnace) 马蹄焰窑enstatite [ 'enstətait ]n. 顽火辉石enzyme [ 'enzaim ]n. 酶epitaxy [ 'epitæksi ]n. 外延，（晶体）取向生长epoxy [ ep'ɔksi ] a. 环氧的n. 环氧树脂erode [ i'rəud ]v. 腐蚀，受侵蚀ethylene[ 'eθili:n ]n. 乙烯eucryptite [ju:ˈkripˌtait]n. 锂霞石eutectic [ ju:'tektik ] a. 低共熔的，共晶的exothermic [ ,eksəu'θə:mik,-'θə:məl ] a. 放热的extrude [ ek'stru:d ]v. 挤压extrusion [ ek'stru:ʒən ]n. 挤出，挤压feldspar [ 'feldspɑ: ]n. 长石ferrite [ 'ferait ]n. 铁氧体ferroelectric [ ,ferəui'liktrik ] a. & n. 铁电体（性，的）filament [ 'filəmənt ]n. 细丝，灯丝filter press [ filtə pres]压滤机fineness [ 'fainnis ]n. 细度、精度、纯度fireclay [ 'faiəklei ]n. 耐火（粘）土，（耐）火泥firing [ 'faiəriŋ ]n. 烧成flaw [ flɔ: ]n. 裂纹，裂痕，瑕疵flexural strength [ˈflekʃərəl streŋθ]抗弯强度flexible [ 'fleksibl ] a. 挠性的，易柔曲的，韧性的float glass [ fləut ɡlɑ:s]浮法（平板）玻璃fluorescence [ fluə'resns ]n. 荧光，荧光性fluoride [ 'flu（:）əraid ]n. 氟化物fluorspar [ 'fluəspɑ: ]n. 萤石，氟石CaF2 fracture toughness [ 'fræktʃəˈtʌfnis]n. 断裂韧性frit [ frit ]n. 熔块、釉料garnet [ 'ɡɑ:nit ]n. 石榴石，石榴红色gel [ dʒel ]n. 凝胶germanium [ dʒə:'meiniəm ]n. 锗（Ge）glass fiber reinforced plastics[ɡlɑ:s'faibə,ri:in'fɔ:sd 'plæstiks ]玻璃纤维增强塑料（GFRP）glaze [ ɡleiz ]v. 上釉glost [ ɡlɔst ]n. 釉grain boundary [ ɡrein 'baundəri]n. 颗粒界面，晶界granulate [ 'ɡrænjuleit ]v. 粒化，成粒graphite [ 'ɡræfait ]n. 石墨green body [ ɡri:n 'bɔdi]n. 生坯，未烧坯grinding [ 'ɡraindiŋ ]n. 研磨，磨碎grit [ ɡrit ]n. 磨料gypsum [ 'dʒipsəm ]n. 石膏halide [ 'hælaid ] a. 卤化物（的），卤族的heterogeneous [ ,hetərəu'dʒi:njəs ] a. 异种的，非均质的hexagonal [ hek'sæɡənəl ] a. 六方的，六方晶系的host [ həust ]n. 基质，晶核homogeneity [ ,hɔməudʒe'ni:əti, ,həu- ]n. 均匀性，均一（性）homogeneous [ ,hɔmə'dʒi:niəs, ,həu- ] a. 均匀的，均一的humidity [ hju:'midəti ]n. 湿气，湿度hydrolysis [ hai'drɔlisis ]n. 水解（作用），加水分解immiscibility [ i,misə'biləti ]n. 不混溶性impediment [ im'pedimənt ]n. 妨碍，阻碍，障碍物impermeable [ im'pə:miəbl ] a. 不可渗透的，不透水的impurity [ im'pjuərəti ]n. 杂质，不纯物inclusion [ in'klu:ʒən ]n. 夹杂（物），掺杂index of refraction [ 'indeks ɔv ri'frækʃən]折射率inertness[iˈnə:tnis]n. 惰性infra-red spectrum [ 'inflə red 'spektrəm]红外光谱ingot[ 'iŋɡət ]n. 块料interferometer [ ,intəfə'rɔmitə ]n. 干涉仪interphase [ 'intəfeiz ]n. 界面，中间相a. 相间的interstitial [ ,intə'stiʃəl ] a. 间隙的intrinsic(al) [ in'trinsik,-kəl ] a. 内在的，固有的，本质的intrude [ in'tru:d ]v. 渗入isomorphic [ ,aisəu'mɔ:fik ] a. 同晶型的isostatic pressing [ ,aisəu'stætik 'presiŋ]n. 等静压成型isotherm [ 'aisəuθə:m ]n. 等温isotropic [ ,aisəu'trɔpik ] a. 各向同性的，均质的jiggering [ 'dʒiɡəriŋ ]n. 旋坯kaolinite [ 'keiəlinait ]n. 高岭土kiln [ kiln, kil ]n. 窑，炉lime [ laim ]n. 石灰，氧化钙limestone [ 'laimstəun ]n. 石灰石lithium [ 'liθiəm ]n. 锂lubrication [ ,lu:bri'keiʃən ]n. 润滑作用luster [ 'lʌstə ]n. 光泽v. 发光，使有光泽，给……上釉magnesium [ mæɡ'ni:ziəm, -ʃi- ]n. 镁magnesite [ 'mæɡnəsait ]n. 菱镁矿manganese[ 'mæŋɡə,ni:s]n. 锰（Mn）marls [ mɑ:l s ]n. 石灰泥matrix [ 'meitriks ]n. 基体，基质metallurgical [ ,melə'lə:dʒik,-kəl ] a. 冶金学的，冶金术的metastable [ ,metə'steibl ] a. 亚稳的，介稳的methane[ 'mi:θein ]n. 甲烷mica [ 'maikə ]n. 云母microcrack [ 'maikrəukræk ]n. 微裂纹microprobe [ 'maikrəuprəub ]n. 显微探针microstructure [ 'maikrəu,strʌktʃə ]n. 显微结构migrate [ mai'ɡreit, 'maiɡ- ]vi. 迁移mineralogy [ ,minə'rælədʒi ]n. 矿物学mineralizer [ 'minərəlaizə ]n. 矿化剂miscible [ 'misəbl ] a. 可混（合）的，可混（溶）的mixer [ 'miksə ]n. 混合机，混料机modification [ ,mɔdifi'keiʃən ]n. 更改，修改，变体modifier [ 'mɔdifaiə ]n. 调整体modulus [ 'mɔdjuləs, -dʒu- ]n. 模数，模量moldable [ˈməuldəbl] a. 可塑的，可模制的monoclinic [ ,mɔnəu'klinik ] a. 单斜的monolithic [ ,mɔnəu'liθik ]n. 单片（块）a. 整体的，单块的mortar [ 'mɔ:tə ]n. 砂（灰、泥）浆mullite [ 'mʌlait ]n. 莫来石multicomponent[ˌmʌltikəmˈpəunənt] a. 多成分的，多元的multiplicity [ ,mʌlti'plisəti ]n. 多样（性），多重性，大量mutrual orientation [ 'mju:tʃuəl ,ɔ:rien'teiʃən]相互取向needle-like [ 'ni:dl laik]针状neutralisation [ ,nju:trəlai'zeiʃən ]n. 中和（作用，法）nitridation [ ,naitri'deiʃən ]n. 氮化notch [ nɔtʃ ]n. 凹口，槽口observable [ əb'zə:vəbl ] a. 可观察到的，可以察觉的octahedral [ ,ɔktə'hedrəl, -'hi:- ] a. 八面体的octahedron [ ,ɔktə'hedrən, -'hi:- ]n. 八面体olivine [ ,ɔli'vi:n, 'ɔlivi:n ]n. 橄榄石opacity [ əu'pæsiti ]n. 乳浊，不透光性，浑浊度，不透明度opaque [ əu'peik ] a. 不透明的，模糊的optical flint [ 'ɔptikəl flint]火石光学玻璃optical crown [ 'ɔptikəl kraun]冕牌光学玻璃optics [ 'ɔptiks ]n. 光学optimum [ 'ɔptiməm ]n. 最佳条件orbital hybridation [ 'ɔ:bitəl haibriˈdeiʃən]轨道杂化organosilane [ 'ɔ:ɡənəu'silein]n. 有机硅烷orient [ 'ɔ:riənt, 'əu-, 'ɔ:rient ]n. 东方vt. 定……的方位orthorhombic [ ,ɔ:θə'rɔmbik ] a. 正交（晶）的，斜方（晶）的orthosilicate [ˌɔ:θəˈsiləkeit]n. 正（原）硅酸盐oscillate [ 'ɔsileit ]v. 振荡，振动overlap [ ,əuvə'læp, 'əuvəlæp ]vt. 与……重叠，与……部分一致overview [ 'əuvəvju: ]n. 综述，概述，概观oxalate [ 'ɔksəleit ]n. 草酸盐pelletization [ ,pelitai'zeiʃən ]n. 造球，球粒化作用particle size distribution [ 'pɑ:tikl saiz ,distri'bju:ʃən]粒径分布particulate [ pə'tikjulit ]n. & a. 粒子，细粒（的）peel [ pi:l ]v. 剥，削，剥落pellet [ 'pelit ]n. 片，粒化（料），丸permeation[ˌpə:miˈeiʃən]n. 渗入，透过permissible [ pə'misibl ] a. 容许的，许可的perpendicular [ ,pə:pən'dikjulə ] a. 垂直的petrochemical [ ,petrəu'kemikəl ] a. & n. 化工的，化工产品phase transition [ feiz træn'siʒən]相变phosphate [ 'fɔsfeit ]n. 磷酸盐photonic [ fəu-'tɔnik ] a. 光子的，光电子的piezoceramic [ pi:'eizəu si'ræmik ]n. 压电陶瓷pigment [ 'piɡmənt ]n. 颜（色）料pitch [ pitʃ ]n. 沥青placement [ 'pleismənt ]n. 放置，布局plasma [ 'plæzmə ]n. 等离子体，等离子区platinum [ 'plætinəm ]n. 铂plotter [ 'plɔtə ]n. 绘图器，测绘仪；制图员plunger [ 'plʌndʒə ]n. 活塞，园柱，插棒polarization [ ,pəulərai'zeiʃən, -ri'z- ]n. 极化，偏振polycrystalline [ ,pɔli'kristəlain, -lin ] a. 多晶的polyhedron [ ,pɔli'hi:drən, -he- ]n. 多面体polymorphic [ ,pɔli'mɔ:fik ] a. 多形的，多态的，多晶的porosity [ pɔ:'rɔsiti, pəu- ]n. 气孔率，多孔性postulate [ 'pɔstjuleit, -tʃə- ]n. 假定，假设potash [ 'pɔtæʃ ]n. 碳酸钾pottery [ 'pɔtəri ]n. 陶器厂，陶器（制造术）precursor [ pri:'kə:sə, pri- ]n. 前驱物premise [ pri'maiz, 'premis ]n. 前提vt. 预述（条件），提出……为前提prism [ 'prizm ]n. 棱镜prismatic [ priz'mætik ] a. 斜方晶系的probe [ prəub ]v. & n. 探针，探测器，（以探针等）探察，查明progressively [ prəu'ɡresiv li ]ad. 日益增多地，逐渐projection [ prəu'dʒekʃən ]n. 喷射prolong [ prə'lɔŋ, 'lɔ:ŋ ]vt. 拉长，延长prospective [ prəu'spektiv ] a. 预期的，有希望的prototype [ 'prəutətaip ]n. 原型，样品pseudomorph [ 'psju:dəumɔ:f ]n. 假象，假晶quarry [ 'kwɔri ]n. 采石场quartzite [ 'kwɔ:tsait ]n. 石英岩，硅岩quench [ kwentʃ ]vt. 1、把……淬火；2、熄灭ram [ ræm ]v. 猛击，填塞，撞reagent [ ri:'eidʒənt ]n. 试剂rearrangement [ 'ri:ə'reindʒmənt ]n. 重排reciprocal [ ri'siprəkəl ]n. 倒数reciprocate [ ri'siprəkeit ]v. 往复运动，上下移动，来回recycle [ ,ri:'saikl ]v. & n. 再循环，反复利用refining[riˈfainiŋ]n. （玻璃液）澄清reflectivity [ ,ri:flek'tiviti ]n. 反射性，反射系数refraction [ ri'frækʃən ]n. 折射refractive index [ ri'fræktiv 'indeks]n. 折射率refractoriness[ ri'fræktərinis]n. 耐火度refractory [ ri'fræktəri ]n. & a. 耐火材料，耐熔的，难熔的rigorous [ 'riɡərəs ] a. 严厉的，严酷的replica [ 'replikə ]n. 复制品，拷贝resonator [ 'rezəneitə ]n. 谐振器，共振器retract [ ri'trækt ]vt. 缩进，收缩retrieve [ ri'tri:v ]vt. 1、取回，恢复；2、补偿，弥补retrogression [ ,retrəu'ɡreʃən ]n. 逆反应rheology [ ri:'ɔlədʒi, ri- ]n. 流变性rhombohedral [ˌrɔmbəuˈhi:drəl] a. 菱形的，菱面体的ruby [ 'ru:bi ]n. 红宝石rupture [ 'rʌptʃə ]n. 断裂rutile [ 'ru:tail, -ti:l ]n. 金红石sagger [ 'sæɡə ]n. 闸体sanitaryware[ˈsænitəriwɛə]n. 卫生洁具schematically[ski:ˈmætikəli]ad. 用示意图，示意地，大略地scrap [ skræp ]n. 碎片，废料screw dislocation [ skru: ,disləu'keiʃən]螺旋位错cullet [ 'kʌlit ]n. 碎玻璃seam [ si:m ]n. 缝，接缝segregation [ ,seɡri'ɡeiʃən ]n. 分层sensor [ 'sensə, -sɔ: ]n. 传感器setting time[ 'setiŋ taim]硬化时间setup [ 'setʌp ]n. 1、组织，构造；2、装置，装配，创立shear [ ʃiə ]n. 剪切shrinkage [ 'ʃriŋkidʒ ]n. 收缩（性，量，率）shutdown [ 'ʃʌtdaun ]n. 关闭，熄灭sieve [ siv ]vt. & n. 筛分silicate [ 'silikit, -keit ]n. 硅酸盐silo [ 'sailəu ]n. 料仓，简仓sintering [ 'sintəriŋ ]n. 烧结skid [ skid ]n. 1、滑动，打滑；2、滑橇，划板slab [ slæb ]n. 板皮，石板岩，厚平板，厚片slag [ slæɡ ]n. （炉）渣slip casting [ slip 'kɑ:stiŋ]n. 注浆成型，泥浆浇注slurry [ 'slə:ri, 'slʌ- ]n. 稀泥浆，水泥浆soda ash [ 'səudə æʃ]苏打灰Na2CO3sodium [ 'səudiəm ]n. 纳（Na）solder [ 'sɔldə ]n. & vt. 焊料，焊接spall [ 'spɔ:l ]v. 研碎，散裂spark plug [ spɑ:k plʌɡ]n. 火花塞spatial orientations [ 'speiʃəl ,ɔ:rien'teiʃəns]空间取向spherically [ 'sferikəli]ad. 球地，球形地spindle [ 'spindl ]n. 1、轴，心轴；2、锭子，纺锤spine [ spain ]n. 脊柱spinel [ spi'nel, 'spinəl ]n. 尖晶石spodumene [ 'spɔdjumi:n ]n. 锂辉石Li2O·Al2O3·4SiO2 spray-drying[ sprei 'draiiŋ]n. 喷雾干燥sputter deposition [ 'spʌtə ,depə'ziʃən]溅射沉积stochastic [ stɔ'kæstik, stəu- ] a. 随机的，机遇的，推测的stoichiometric [ ,stɔikiə'metrik ] a. 化学计量的stoneware [ 'stəunwεə ]n. 石制品，粗陶瓷（器）stress-strain curve [ stres strein kə:v]应力-应变曲线subjective [ səb'dʒektiv ] a. 主观的submicrometer [ sʌb 'maikrəu mi:tə ]n. 亚微米suffice [ sə'fais ]v. 足够，使满足superconductor [ ,sju:pəkən'dʌktə ]n. 超导体superfine [ ,sju:pə'fain ] a. 特级的supersaturation [ 'sju:pə,sætʃə'reiʃən ]n. 过饱和（现象）surfactant [ sə:'fæktənt ]n. 表面活化剂suspension [ sə'spenʃən ]n. 悬浮液symmetry [ 'simitri ]n. 对称，匀称symposium [ sim'pəuziəm ]n. 1、专题讨论会；2、专题论文集talc [ tælk ]n. & vt. 滑石，用滑石处理tantalum [ 'tæntələm ]n. 钽tar [ tɑ: ]n. 焦油temporal [ 'tempərəl ] a. 1、暂时的，转瞬间的；2、时间的tensile strength [ 'tensail streŋθ]抗张强度ternary [ 'tə:nəri ] a. & n. 三元（的），三重（的）tetragonal [ te'træɡənəl ] a. 四方晶系的tetrahedron [ ,tetrə'hi:drət, -'he- ]n. 四面体tetravalent [ ,tetrə'veilənt, te'trævə- ] a. 四价的texture [ 'tekstʃə ]n. 织构，质地，结构thermalcouple [ 'θə:məl 'kʌpl]n. 热电偶thermal expansion coefficient[ 'θə:məl ik'spænʃən ,kəui'fiʃənt ]热膨胀系数thermal shock resistance[ 'θə:məl ʃɔk ri'zistəns ]抗热震（性）thermoplastic[ ,θə:məu'plæstik ] a. 热塑性的throwing[ 'θrəuiŋ ]n. 手工拉坯titania [ tai'teiniə, ti- ]n. 二氧化钛titanate [ 'taitəneit ]n. 钛酸盐tolerance [ 'tɔlərəns ]n. 公差，容许限度toughness[ tʌfnis ] n. 韧性toxicity [ tɔk'sisəti ]n. 毒性translucent [ trænz'lju:sənt, træns-, trɑ:n- ]n. 半透明的tridymite [ 'tridimait ]n. 磷石英trigonal [ 'triɡənəl, trai'ɡəunəl ] a. 三方的valency [ 'veilənsi ]n. 化合价，价，原子价varistor [ və'ristə ]n. 压敏电阻，可变电阻versatile [ 'və:sətail ] a. 1、通用的，万能的；2、活动的，万向的vertebra [ 'və:tibrə ]n. 椎骨，脊椎（pl. vertebrae）vinylalcohol [ 'vainil 'ælkəhɔl]n. 乙烯醇vitreous [ 'vitriəs ] a. 玻璃质的，玻璃态的vitrification [ ,vitrifi'keiʃən ]n. 玻璃化vitrify [ 'vitrifai ]v. 玻璃化，（使）成玻璃volatilization [ vɔ,lætilai'zeiʃən ]n. 挥发wetting[ 'wetiŋ ]n. （变、润、浸）湿whisker [ 'hwiskə ]n. 晶须whiteware [ 'hwaitwεə ]n. 白色（卫生）陶瓷wollastonite [ 'wuləstənait ]n. 硅灰石workability [ ,wə:kə'biləti ]n. 成型性zeolite [ 'zi:əlait ]n. 沸石zinc[ ziŋk ]n. 锌zirconia [ 'zə:kɔniə]n. 氧化锆zircon [ 'zə:kɔn ]n. 锆石，锆英石。