Spatial Compactification and Decay-Rate Behavior
群论第8章

能级简并(时间反演的结果). 实表示:Cn 的特征标为+1( A 表示),-1( B 表示)。 反演对称操作i 的特征标为 1(偶宇称,下标用 g ),-1(奇宇称,下标用u ).
除Ci ,有 10 个点群具有反演操作i 对称,它们均可以表示为Ci 群与另一正 则转动群的直积:
对 n = 2,4,6 ,它包含一个反演操作 I (≡ C2σ h )。
Sn 群:有一个 n 度转动反演轴( n = 4,6 ); 对 n = 2,3的 S2 和 S3 ,一般用 Ci 和 C3h 符号;
Dn 群:有一个 n 度转动轴及 n 个与之垂直的二度轴( n = 2,3,4,6 ); Dnd 群: Dn 群加 4 n 个垂直对交镜面( n = 2,3)镜面将二度轴角度平分。 Dnh 群: Dn 群加一个水平镜面( n = 2,3,4,6 ). n = 2,4,6 时, Dnh 包含反演操作。 除以上 27 个群外,还有Oh , O ,Td ,Th 和T 群。
群 论 讲 稿----吴 长 勤
第八章 点群和空间群 (Point Groups and Space Groups)
§1 点群 (Point Groups)
点群:使系统(如分子)不变的对称操作的集合构成的群。(某点固定,空 间任何两点距离不变的有限群)
一般,几何对称操作有:
E : 恒等操作;
Cn :转角 2π / n 的操作,转动轴称 n 度轴;
{ } C3v : {E}, C3,C32 , {σ1,σ 2 ,σ 3}; 三个共轭类。 { } { } C'3v : {E},{E}, C3,C32 , EC3, EC32 ,{σ1,σ 2 ,σ 3},{Eσ1, Eσ 2 , Eσ 3};
1汉英力学名词(1993)

BZ反应||Belousov-Zhabotinski reaction, BZ reactionFPU问题||Fermi-Pasta-Ulam problem, FPU problemKBM方法||KBM method, Krylov-Bogoliubov-Mitropolskii method KS[动态]熵||Kolmogorov-Sinai entropy, KS entropyKdV 方程||KdV equationU形管||U-tubeWKB方法||WKB method, Wentzel-Kramers-Brillouin method[彻]体力||body force[单]元||element[第二类]拉格朗日方程||Lagrange equation [of the second kind] [叠栅]云纹||moiré fringe; 物理学称“叠栅条纹”。
[叠栅]云纹法||moiré method[抗]剪切角||angle of shear resistance[可]变形体||deformable body[钱]币状裂纹||penny-shape crack[映]象||image[圆]筒||cylinder[圆]柱壳||cylindrical shell[转]轴||shaft[转动]瞬心||instantaneous center [of rotation][转动]瞬轴||instantaneous axis [of rotation][状]态变量||state variable[状]态空间||state space[自]适应网格||[self-]adaptive meshC0连续问题||C0-continuous problemC1连续问题||C1-continuous problemCFL条件||Courant-Friedrichs-Lewy condition, CFL condition HRR场||Hutchinson-Rice-Rosengren fieldJ积分||J-integralJ阻力曲线||J-resistance curveKAM定理||Kolgomorov-Arnol'd-Moser theorem, KAM theoremKAM环面||KAM torush收敛||h-convergencep收敛||p-convergenceπ定理||Buckingham theorem, pi theorem阿尔曼西应变||Almansis strain阿尔文波||Alfven wave阿基米德原理||Archimedes principle阿诺德舌[头]||Arnol'd tongue阿佩尔方程||Appel equation阿特伍德机||Atwood machine埃克曼边界层||Ekman boundary layer埃克曼流||Ekman flow埃克曼数||Ekman number埃克特数||Eckert number埃农吸引子||Henon attractor艾里应力函数||Airy stress function鞍点||saddle [point]鞍结分岔||saddle-node bifurcation安定[性]理论||shake-down theory安全寿命||safe life安全系数||safety factor安全裕度||safety margin暗条纹||dark fringe奥尔-索末菲方程||Orr-Sommerfeld equation奥辛流||Oseen flow奥伊洛特模型||Oldroyd model八面体剪应变||octohedral shear strain八面体剪应力||octohedral shear stress八面体剪应力理论||octohedral shear stress theory巴塞特力||Basset force白光散斑法||white-light speckle method摆||pendulum摆振||shimmy板||plate板块法||panel method板元||plate element半导体应变计||semiconductor strain gage半峰宽度||half-peak width半解析法||semi-analytical method半逆解法||semi-inverse method半频进动||half frequency precession半向同性张量||hemitropic tensor半隐格式||semi-implicit scheme薄壁杆||thin-walled bar薄壁梁||thin-walled beam薄壁筒||thin-walled cylinder薄膜比拟||membrane analogy薄翼理论||thin-airfoil theory保单调差分格式||monotonicity preserving difference scheme 保守力||conservative force保守系||conservative system爆发||blow up爆高||height of burst爆轰||detonation; 又称“爆震”。
4H 和 6H-SiC的介电常数

II. BULK 4H AND 6H SiC
A. Samples
The 4H and 6H SiC samples studied here were obtained commercially from Cree Research. For spectroscopic ellipsometry, we used single-side polished ͑Si-terminated͒ wafers, 35 mm in diameter, and 0.42 mm thick. The miscut, i.e., the angle between the surface normal and the hexagonal axis, was about 8°, confirmed by x-ray diffraction. The wafers were not intentionally doped, but nitrogen impurities resulted in electron concentrations near 6 – 8ϫ1018 cmϪ3 in 4H SiC and 1ϫ1018 cmϪ3 in 6H SiC, determined by secondary ion mass spectrometry, Fourier-transform infrared ellipsometry, and electrical measurements by the supplier. The samples were measured as received. No surface preparation was performed. Therefore, we expect that the wafers are covered with a thin native oxide (SiO2). Samples used for transmission intensity measurements were similar, but two-side polished.
磁性测量中ZFC和FC数据的获得与解释

1957年,χ-T低温极大值(CuMn,AgMn)
J. Owen & M. E. Browne, V. Arp & A. F. Kip, J. Phys. Chem. Solids, 2 (1957) 85
统一理论
?, ?, ? (?) ?
EA
Ising、Heisenberg、XY、 Bethe Lattice、Mattis、SK、 Random Bond…
单个Fe、Mn原子的各向异性
Science, 315 (2007.08.31) 1199-1203
三、Fe原子(团)更分叉
混磁性、自旋玻璃(SG)
非线性磁化率的实验 1979年~1980年,(Y. Miyako, et al) J. Phys. Soc. Japan, 46 (1979) 1951 J. Phys. Soc. Japan, 47 (1979) 335 J. Phys. Soc. Japan, 48 (1980) 329 综述: K. Binder & A. P. Young, Rev. Mod. Phys., 58 (1986) 801 Magnetic Susceptibility of Superconductor and Other Spin Systems Eds. R. A. Hein, T. L. Francavilla & D. H. Liebenberd, 1991, New York
三、Fe原子(团)更分叉
临界浓度、交换相互作用
近藤效应:稀释磁性合金电阻率-温度曲线极小值 1964年,始作俑者不是Jun Kondo(近藤 淳) J. Kondo, Prog. Theor. Phys., 32 (1964) 37 1931年,AuFe(J. W. Shih) Phys. Rev., 38 (1931) 2051 1951年,R-T低温极大值(AgMn)
测绘学名词

测绘学名词本文共7页当前为第1页01.总类02.大地测量学02.001 大地测量 geodetic surveying02.002 几何大地测量学geometric geodesy02.003 椭球面大地测量学ellipsoidal geodesy02.004 大地天文学geodetic astronomy02.005 物理大地测量学(又称“大地重力学”) physical geodesy 02.006 空间大地测量学space geodesy02.007 卫星大地测量学satellite geodesy02.008 动力大地测量学dynamic geodesy02.009 海洋大地测量学marine geodesy02.010 月面测量学lunar geodesy,selenodesy02.011 行星测量学planetary geodesy02.012 天文大地网(又称“国家大地网”)astro--geodetic network 02.013 参考椭球reference ellipsoid02.014 贝塞尔椭球Bessel ellipsoid02.015 海福德椭球Hayford ellipsoid02.016 克拉索夫斯基椭球Krasovsky ellipsoid02.017 参考椭球定位orientation of reference ellipsoid02.018 大地基准geodetic datum02.019 大地坐标系geodetic coordinate system02.020 弧度测量arc measurement02.021 拉普拉斯方位角Laplace azimuth02.022 拉普拉斯点Laplace point02.023 三角测量triangulation02.024 三角点triangulation point02.025 三角锁triangulation chain02.026 三角网triangulation network02.027 图形权倒数weight reciprocal of figure02.028 菲列罗公式Ferreros formula02.029 施赖伯全组合测角法Schreiber method in all combinations02.030 方向观测法method of direction observation,method by series02.031 测回observation set02.032 归心元素elements of centring02.033 归心改正correction for centring02.034 水平折光差(又称“旁折光差”) horizontal refraction error02.035 基线测量base measurement02.036 基线baseline02.037 基线网base network02.038 精密导线测量precise traversing02.039 三角高程测量trigonometric leveling02.040 三角高程网trigonometric leveling network 02.041 铅垂线plumb line02.042 天顶距zenith distance02.043 高度角elevation angle, altitude angle02.044 垂直折光差vertical refraction error02.045 垂直折光系数vertical refraction coefficient 02.046 国家水准网national leveling network02.047 精密水准测量Precise leveling02.048 水准面level surface02.049 高程height02.050 正高orthometric height02.051 正常高normal height02.052 力高 dynamic height02.053 地球位数geopotential number02.054 水准点benchmark02.055 水准路线leveling line02.056 跨河水准测量river-crossing leveling02.057 椭球长半径major radius of ellipsoid02.058 椭球扁率flattening of ellipsoid02.059 椭球偏心率eccentricity of ellipsoid02.060 子午面meridian plane02.061 子午圈meridian02.062 卯酉圈prime vertical02.063 平行圈parallel circle02.064 法截面normal section02.065 子午圈曲率半径radius of curvature in meridian02.066 卯酉圈曲率半径radius of curvature in prime vertical 02.067 平均曲率半径mean radius of curvature02.068 大地线geodesic02.069 大地线微分方程differential equation of geodesic 02.070 大地坐标geodetic coordinate02.071 大地经度geodetic longitude02.072 大地纬度geodetic latitude02.073 大地高geodetic height,ellipsoidal height02.074 大地方位角geodetic azimuth02.075天文大地垂线偏差astro—geodetic deflection of the vertical02.076 垂线偏差改正correction for deflection of the vertical02.077 标高差改正correction for skew normals02.078 截面差改正correction from normal section to geodetic02.079 大地主题正解direct solution of geodetic problem02.080 大地主题反解 inverse solution of geodetic problem02.081 高斯中纬度公式Gauss mid—latitude formula02.082 贝塞尔大地主题解算公式Bessel formula for solution of geodetic problem02.083 高斯一克吕格投影Gauss-Kruger projection又称“高斯投影”。
黎曼曲面讲义

3.5 Abel-Jacobi 定理 . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 107
第四章 曲面与上同调
121
4.1 全纯线丛的定义 . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 121
f 的实部和虚部分别为 u, v, 则 f 为全纯函数的充分必要条件是 u, v 满足如下的
Cauchy-Riemann 方程:
$ & ux “ vy,
% uy “ ´vx.
全纯函数的定义还有许多其他的等价形式.
平均值公式:
若函数
f
在圆盘
tz
P
C
ˇ ˇ
|z
´ a|
ă
Ru
内全纯并连续到边界,
则
f paq “
本书主要内容如下:第一章基本上是关于复变函数的简单复习,我们给出了 单值化定理的简单情形,即 Riemann 映照定理的证明。这一章也得到了调和函数 的梯度估计以及 Harnack 原理,这里采用的方法可以推广到一般的黎曼流形上。 第二章引入了抽象黎曼曲面的定义,并给出了单连通黎曼曲面的分类(单值化定 理),其中,黎曼环面作为一类重要的紧致黎曼曲面也加以了分类。证明单值化定 理的方法是通过调和函数(可能带有奇点)来构造特殊的全纯映射。而调和函数 的存在性是通过经典的 Perron 方法获得的。第三章是本书核心内容之一,我们给 出了 Riemann-Roch 公式的证明,并选择了若干有意思的应用加以介绍。我们选 择的 Riemann-Roch 公式的这个证明也是经典的,它也涉及某些给定奇性的亚纯 微分的存在性,这种亚纯微分的存在性是通过 Hodge 定理获得的,为了尽快的介 绍 Riemann-Roch 公式的应用,我们把重要的 Hodge 定理的证明放在本书第二个 附录中了。通过 Riemann-Roch 公式我们知道了紧致黎曼曲面上亚纯函数的丰富 性,我们也证明了亚纯函数域是一个一元代数函数域,并且它惟一地决定了黎曼曲 面本身。作为例子我们简单介绍了黎曼环面上的亚纯函数,它们就是经典的椭圆 函数。通过适当地挑选亚纯函数,我们把黎曼曲面全纯地嵌入到了复投影空间中, 因此可以从代数曲线的角度来研究它们。我们还介绍了计算总分歧数的 RiemannHurwitz 公式,并利用它简单研究了超椭圆型的黎曼曲面。接下来我们介绍了曲面 上的 Weierstrass 点,得到了 Weierstrass 点的个数估计。这些结果又被应用于曲面 的全纯自同构群,特别地,我们证明了亏格大于 1 的紧致黎曼曲面全纯自同构群 的阶的估计。作为第二章的结束,我们还介绍了重要的双线性关系、Jacobi 簇,证
rapid solidification
Spinodally decomposed patterns in rapidly quenched Co–Cu meltsE.Davidoffa ,b ,P.K.Galenko c ,⇑,D.M.Herlach a ,M.Kolbe a ,N.Wanderka daInstitut fu ¨r Materialphysik im Weltraum,Deutsches Zentrum fu ¨r Luft-und Raumfahrt (DLR),51170Ko ¨ln,GermanybInstitut fu ¨r Festko ¨rperphysik,Ruhr-Universita ¨t Bochum,44780Bochum,GermanycFriedrich-Schiller-Universita ¨t Jena,Physikalisch-Astronomische Fakulta ¨t,D-07737Jena,GermanydInstitute of Applied Materials,Helmholtz-Zentrum Berlin fu ¨r Materialien und Energie GmbH,Glienicker Str.100,14109Berlin,GermanyReceived 10September 2012;accepted 9October 2012Available online 19November 2012AbstractThe Co–Cu system is analyzed in the region of the metastable miscibility gap with separation of the undercooled melt into the Co-rich and Cu-rich liquids.Phase separation of undercooled and quenched samples of the Co 50Cu 50melt are investigated experimentally using an electromagnetic levitation technique,quenching on a Pb-solder-coated copper chill substrate and splat-quenching methods.It is found that quenching of the liquid samples with cooling rate J 106K s À1leads to a freezing of splats having the microstructure of spinodally decomposed liquids.The composition of the Co-rich phase measured by transmission electron microscopy is Co 71.7Cu 28.3and that of the Cu-rich phase is Co 26.8Cu 73.2.These compositions are inside the spinodal region and close to the calculated spinodal boundary in the phase diagram of the Co–Cu system at temperatures below T %1450K.Experimental results are compared with predictions of compu-tational modeling using a model of fast spinodal decomposition.Ó2012Acta Materialia Inc.Published by Elsevier Ltd.All rights reserved.Keywords:Undercooling;Phase separation;Spinodal;Binodal1.IntroductionCu–Co is a well-known peritectic system [1,2],which has attracted considerable interest,mainly because of its mag-netic properties (giant magnetoresistance [3])and its use as catalyst in the synthesis of higher alcohols [4].A special feature of the Cu–Co system is the metastable miscibility gap in the range of the undercooled melt.If the homoge-neous melt is undercooled about 120K below the liquidus temperature,it reaches a binodal and separates into a Co-rich phase (so-called “L1-phase ”)and a Cu-rich phase (so-called “L2-phase ”).Both phases are liquid and upon further cooling they follow the concentration given by the binodal which is shown as solid circles in Fig.1.As a result of phase separation and cooling,the microstructure is subjected to further modifications as the liquid L1-andL2-phases solidify.This makes a detailed analysis of the initial metastable states difficult.Sufficient undercooling can be achieved by various tech-niques,such as electromagnetic levitation [5–8],drop tube processing [9,10],splat cooling [5],electron beam surface melting [6]and melt flux embedding [11].The latter approach has been used to measure the metastable misci-bility gap with high precision by differential thermal analy-sis (DTA)and differential scanning calorimetry [8,12,13].Many attempts have been made to understand the for-mation of the solidified microstructure in terms of the for-mation of Co-rich and Cu-rich phases.For example,a quantitative description of L1-droplet growth in rapidly solidified Cu 84Co 16has been given taking into account nucleation and chemical diffusion growth in the liquid under rapid cooling conditions [14,15].Therefore,quench-ing at off-critical concentrations,i.e.off-critical quench into the metastable region of phase separation,has been inves-tigated in detail by various experimental techniques [16].However,only a few investigations have been carried out1359-6454/$36.00Ó2012Acta Materialia Inc.Published by Elsevier Ltd.All rights reserved./10.1016/j.actamat.2012.10.010⇑Corresponding author.E-mail address:peter.galenko@uni-jena.de (P.K.Galenko)./locate/actamatAvailable online atActa Materialia 61(2013)1078–1092for the Co–Cu alloy in the region around the critical con-centration,namely for phase separation around the com-position Co50Cu50.In particular,after investigations of ribbons produced by the melt spinning process,it was assumed that alloy Co50Cu50solidifiesfirst polymorphi-cally as a solid solution,and then decomposes spinodally in the solid state during further cooling and aging[17]. Therefore,around the composition Co50Cu50,phase sepa-ration at a critical quench can be observed in the binodal region with“metastable!stable”phase formation or even in the spinodal region with“unstable!metastable”phase formation.Experimentally,one can expect very fast separation in the unstable region of the phase diagram,though this has not yet been observed for the high-temperature liquid–liquid phase separation of metallic melts.Such investiga-tion is of fundamental interest from the theoretical point of view.In particular,deeply quenching metallic liquids into the unstable region of the phase diagram should result in characteristic features of non-equilibrium phase separa-tion which can be analyzed within the concept of fast phase transitions[18,19].Hence,we consider the Co–Cu binary melt,undercooled or rapidly quenched at its critical con-centration by modern experimental techniques,as an excel-lent system with which it is possible to verify recent theoretical models of phase separation.The present paper is devoted to the investigation of undercooled and quenched liquid samples with subsequent freezing of microstructure in the Co50Cu50system.We focus on the attempt to preserve the initial microstructure of melts after solidification by liquid metal cooling and to deduce details of the liquid–liquid demixing process from its traces in the solidified microstructure.In particular, the spatial and time characteristics of the experimentally determined microstructure in splat quenching at the highest cooling rates of106–107K sÀ1are interpreted in terms of models of fast phase separation.2.Experimental set-upSpecimens with a nominal composition Co50Cu50at.% were alloyed from high-purity Co(99.995%)and Cu (99.999%)by arc melting under an Ar atmosphere at 980mbar.The oxygen concentration was reduced with the help of a Ti-getter inside the chamber of the arc fur-nace.The sample composition was controlled by weight balancing prior to and after arc melting.The deviation from the nominal concentration was less than0.1at.%.Co50Cu50drops of about1g mass,which correspond to spheres of about6mm diameter,were processed under container-free,high-purity conditions by electromagnetic levitation(EML)with optional splat cooling(see mono-graph[20]and references therein).Using EML,the melts can be undercooled and rapidly solidified either by sponta-neous nucleation or by splat cooling.The vacuum chamber of the EML apparatus was evacuated to10À7mbar and refilled with He up to900mbar.The levitated samples were cyclically melted and overheated by approximately200K in the He atmosphere to evaporate oxygen from the sam-ple,and then undercooled by thermal conduction of He gas,which provided cooling rates of10–20K sÀ1in this particular case.The temperature of the levitated samples was measured with a digital one-color pyrometer with ±10K accuracy.Alternatively,Co50Cu50melts were only slightly under-cooled to temperatures below the critical point and quenched by contacting them with a Pb-coated copper sub-strate.For the production of rapidly quenched samples a splat-cooling device[21]has been installed below the levita-tion-coil system inside the EML chamber.This splat-cooling device allows us to reach quenching rates of the order of106–107K sÀ1[22].Levitated samples were over-heated above the liquidus temperature by200–300K and then quenched by splat cooling.Droplets solidified in the EML chamber with gas cool-ing only were cut and polished.Splats also processed and produced in the EML chamber were only polished.Subse-quently,polished samples were examined by scanning elec-tron microscopy(SEM)using LEO1530VP and a Zeiss 1540EsB CrossBeam workstation equipped with an energy-dispersive X-ray spectrometry(EDS)system.Co-rich and Cu-rich phases were imaged using a detector for backscattered electrons(BSE),showing the Co-rich phase dark and the Cu-rich phase bright.Selected parts of the splat-cooled samples were cut and then subjected to ion beam thinning.The primary micro-structure of splat-cooled samples was analyzed by trans-mission electron microscopy(TEM)using a Philips CM30operating at300kV with an attached EDS system. The beam size for the EDS measurements was about 20nm.E.Davidoffet al./Acta Materialia61(2013)1078–109210793.Experimental resultsThe alloy system Co–Cu exhibits a metastable miscibil-ity gap in the region of the undercooled melt[1,2,8].Tem-peratures for the binodal line in liquid-liquid phase separation were precisely measured by DTA(see solid cir-cles in Fig.1)in the composition range of16–89.3at.%Cu as described by Cao et al.[11].The metastable miscibility gap is symmetrical with respect to the critical point(T c,c c)having the temperature T c=1547K and concentration c c=52.7at.%Cu.Note that the miscibility gap is nearlyflat in the range of45–60at.%Cu(see Fig.1).Using the DTA results for the mis-cibility gap of the Co–Cu system extracted from Ref.[11], the spinodal line has been calculated by Landau’s theory and the standard thermodynamic method,as described in Refs.Appendix A.1and Appendix A.2.3.1.Non-quenched samplesSignificant undercooling(P120K)of the homogeneous melt below the binodal leads to separation of the melt into a Co-rich L1-phase and a Cu-rich L2-phase.Such underco-oling is easily achieved by containerless processing in the EML apparatus.The large undercooling required to enter the metastable miscibility gap produces a large driving force for rapid solidification.The Co50Cu50samples have been undercooled systemat-ically into the range of the metastable miscibility gap and then rapidly solidified.This composition is close to the crit-ical concentration c c,i.e.to the critical point consistent into the metastable Co-rich(dark)and Cu-rich(bright) phases.The morphology of the Co-rich and Cu-rich phases is distorted due to electromagnetic stirring of the melt which additionally stimulates coagulation of the phases [16].The average composition of these phases measured by EDS is Co84Cu16for the Co-rich phase and Co4Cu96 for the Cu-rich phase.The Co-rich phase follows the com-positions of the binodal line at the respective nucleation temperature,as previously reported by Cao et al.[10,11].The SEM image in Fig.2a shows the microstructure of the whole droplet in cross-section.The substructure of the interface between the Cu-rich and the Co-rich phases is shown in Fig.2b.The secondary a-dendrites of Co solidi-fied after the Co-rich phase solidification in the Cu-rich phase at lower temperatures.It seems that the dendrites were triggered by Co-rich phase as the dendrites grow at the Co–Cu interface.The oval shape morphology of the Co-rich phase with the thinfilm of Cu-rich phase in between is typical of a deeply undercooled sample(see Fig.2a).The microstructure described above appears to be the result of the liquid–liquid phase separation by the binodal mechanism as discussed elsewhere[6,11,14].3.2.Quenched samples with a cooling rate of104K sÀ1To investigate the initial stages of liquid-phase separa-tion in the Co50Cu50system,we used EML together with quenching of samples.The melt drops,undercooled to a temperature below the critical point,were quenched by coming into contact with a Pb-solder-coated Cu substrate before the crystal nucleation starts inside the levitatedwith the microstructure of the Co50Cu50sample undercooled on D T%250>T LÀT B using the EML technique liquidus temperature and binodal temperature,respectively).The cross-section of the whole droplet(a)and Co-rich phases(b)are shown as a result of the liquid-phase separation.The Co-rich phase appears1080 E.Davidoffet al./Acta Materialia61(2013)1078–1092compared with the microstructure of solidified samples processed without quenching.The Co 50Cu 50melt quenched on a solder-coated Cu sub-strate at D T =220K undercooling also decomposed into Co-and Cu-rich phases as demonstrated in Fig.3.However,the observed microstructure was different from those obtained by EML without quenching and shown in Fig.2.Inside the large Co-rich coagulated phase encased in the Cu-rich phase,Cu-rich droplets 15–300l m in diameter were found (Fig.3a).No Co-rich dendrites solidified inside Cu-rich droplets as usually found in gas-cooled samples without quenching (see Fig.2b).Note that the top region of the sam-ple has a larger amount of these Cu-rich droplets than the bottom region which was in close contact with the cooling substrate.This fact shows that the upper region of the sam-ple had a much longer time for phase separation than the lower contact part of the sample.This tendency is explained by non-uniform cooling of the bulk sample during quench-ing with the given rate of the order of 104K s À1.It should also be noted that the structure of the quenched droplets exhibits inhomogeneity.In particular,in parts of the droplets which are close to the substrate,small Co-rich dots with an average diameter of 0.55l m were found inside Cu-rich oval phases (droplets)about 100l m in size (see Fig.3b).In these quenched samples,the size of the dots is much smaller compared to the gas-cooled samples.A rather similar microstructure with Co-rich dots dispersed in Cu-rich droplets upon phase sep-aration in a Co 16Cu 84melt has been previously reported for samples processed by a drop-tube technique [14].The aver-age composition of the large Co-rich phase is Co 82Cu 18and the composition of the Cu-rich phase without Co-rich pre-cipitates is Co 9Cu 91.The Cu-rich droplets with Co-rich precipitates have the average composition of Co 12Cu 88.The composition of the Co-rich phase has nearly the same composition as the Co-rich droplets of the gas-cooled positions of Co-rich and Cu-rich phases (mea-sured by SEM-EDS)also indicate the composition and temperature corresponding to the binodal line (shown by solid circles in Fig.1).3.3.Quenched samples with cooling rates of 106–107K s À1Co 50Cu 50melts were also rapidly quenched by splat cooling which provides cooling rates of the order of 106–107K s À1.The surfaces of frozen solid splats were polished and then analyzed by SEM,X-ray diffraction (XRD)using Cu K a radiation,and TEM.3.3.1.Microstructure under “low magnification ”It is well known that the chemical composition of a binodally decomposed sample has spatial inhomogeneity on the mesoscopic and microscopic length scales.Indeed,samples solidified under low and intermediate cooling rates exhibit macro-and microstructures with chemical inhomo-geneity upon phase separation (see Figs.2and 3).Con-versely,samples frozen under the highest cooling rates P 106K s À1show a mesoscopically homogeneous struc-ture.As shown in Fig.4a,a microstructure with the initial (nominal)chemical composition of the alloy has been detected over an area of 30Â20l m 2.Therefore,one can conclude that a structureless crystal pattern is observed under “low magnification ”(see Fig.4a).The crystallographic characteristics of this mesoscopi-cally structureless crystal pattern are as follows.Bragg reflexes of two phases with face-centered cubic (fcc)lattice have been detected from the XRD pattern of the Co 50Cu 50splat shown in Fig.4b.The experimental pattern has been compared with that calculated using Powder Cell software [24].The strong Bragg reflexes with the angles of 2H =43.33°(111),50.52°(200)and 74.17°(220)have been clearly identified as the fcc crystal structure of the Cu-rich phase (higher-angle reflections marked as x sym-bols in Fig.4b).A lattice parameter of a =0.3615nm has been calculated for the Cu-rich phase.The XRD pattern and lattice parameter of this Cu-rich crystalline phase cor-respond to the fcc lattice of pure Cu as well.It can be con-cluded that the Cu-rich phase is the stable one.The second phase with Bragg reflexes with angles of 2H =44.06°,51.35°and 75.58°has been determined as Co-rich fcc crystal structure (Fig.4b)[24].A latticeparam-showing the microstructure of Co 50Cu 50undercooled sample quenched into Pb substrate inside liquid–liquid phase separation.The Co-rich phase appears dark,the Cu-rich phase appears bright.The white substrate.(b)Substructure of Cu-rich droplet from the bottom layer of as-quenched sample displays Co-richeter of a =0.3559nm has been calculated for the Co-rich phase.However,the Bragg reflexes of this phase are shifted to smaller 2H angles due to the small difference between the lattice parameters of the pure high-temperature fcc crystal structure of Co (a =0.3544nm)and the lattice parameters of the Co-rich solution in Co 50Cu 50splat.Obviously,Cu atoms replace the Co atoms at some nodes of the crystal lattice.The lattice parameters of the Co-rich and Cu-rich phases are in accordance with the results reported for the rapidly solidified Co 50Cu 50samples [13,25].The lattice con-stant of 0.36118±0.00002nm for the Cu-rich solution and 0.35599±0.00002nm for the Co-rich solution were obtained by Rietveld analysis of XRD patterns of the chilled side of Co 50Cu 50ribbons [13].3.3.2.Microstructure under “high magnification ”Details of the splat from Fig.4a are shown at higher magnification in Fig.4c and d imaged with backscattered electrons.In some regions of the splat,small Co-rich initial dendritic structures 2–4l m in size exist in Cu-rich matrix as observed in Fig.4c.As a rule,worm-like structures which are typically observed in spinodal decomposition were found on other parts of the splat (Fig.4d).These worm-like structures are nearly oval in cross-section with a diameter of about 0.29l m.The periodicity as a mean dis-tance between two neighboring structures is about 0.4l m.The microstructure of the splat in Fig.4e also exhibits spinodal patterns when analyzed by SEM using an InLens detector (secondary electrons).The Co-rich phase is imaged bright and the Cu-rich phase is dark.Theshowing an overview of the microstructure of Co 50Cu 50samples after splat cooling.(b)X-ray diffractogram correspond to calculated Cu-rich phase (Â)with fcc lattice having the lattice parameter 0.3615nm.Dotted (+)with fcc lattice having the lattice parameter 0.3559nm.(c)A part of a splat with dendritic structure.structures.(e)Overview of the splat microstructure analyzed by SEM using an InLens detector.(f)Spinodal magnification.The microstructure in (c)and (d)has been imaged by backscattered electrons and inmicrostructure details are shown in Fig.4f at a higher mag-nification.The average next-neighbor distance of144nm between Co-rich structures was measured in Fig.4f.The Co-rich”worm”structures are about87nm in diameter.Fig.5presents details of the spinodal microstructure observed in Fig.4e and f in a typical bright-field(BF) TEM micrograph of the Co50Cu50splat.The Co-rich and Cu-rich phases are difficult to distinguish because of the similar mass contrast.In Fig.5,the Co-rich crystals are vis-ible as dark-grey band-like structures(Co)and the Cu-rich are bright structures in between the Co-rich phase.The Co-rich band-like morphology is nearly oval in cross-section. The Co-rich“bands”are approximately100nm in diame-ter.The periodicity,i.e.the mean distance between neigh-boring spinodally decomposed patterns,ranges from120 and170nm.The average atomic composition of the Co-rich phase of Co71.7Cu28.3was measured by TEM-EDS. The Cu-rich phase has the average composition of Co26.8Cu73.2.The measured compositions of Co-rich and Cu-rich phases are indicated in the phase diagram of the Co–Cu alloy system(see Fig.1).Obviously,the measured composition of the Co-rich phase is close to the calculated spinodal miscibility gap based on using the Landau approach.The measured composition of the Cu-rich phase is slightly offthe calculated spinodal at the peritectic temper-ature;however,it lies inside the unstable miscibility gap (represented by the spinodal region of the phase diagram).4.Discussion4.1.Microstructure identificationSpinodal and binodal structures exhibit significantly dif-ferent patterns which are shown as time sequences of snap-shots in Fig.6a and b,respectively.One of the important reasons for this difference can be seen in mechanisms of their appearance,growth and coarsening in spinodally or binodally decomposed liquids.As shown in sequence(b)of Fig.6,binodal decomposi-tion is realized through the nucleation stage.When applied to the Co–Cu alloy system,separation of the homogeneous melt into Co-rich and Cu-rich phases starts from a large number nuclei in sufficiently undercooled melts(usually, in the region of the off-critical quench in a phase diagram). This separation leads to formation of droplet dispersions during the binodal liquid–liquid separation(Fig.2). Regarding our Co–Cu system,using quenching methods in particular,we found that Co-rich dots distributed in Cu-rich droplets are close to the Cu substrate layer of quenched Co50Cu50melt(Fig.3).The average composition of both Co-rich and Cu-rich phases measured by SEM-EDS is defined by the concentration of the binodal at the nucleation temperature.In comparison with gas-cooled samples,only the average composition of Co-rich phase conforms to the binodal.This shows that the liquid Cu-rich droplets close to the Cu substrate were undercooled deeper by coming into contact with the Pb substrate.This means that the Cu-rich droplets were frozen at some stage of bin-odal phase separation.Contrary to the binodal decomposition mechanism, spinodal decomposition is realized through spontaneous growth offluctuations.This process of phase separation leads to worm-like stochastically orientated patterns(e.g. compare patterns from Fig.4with sequence(a)of patterns from Fig.6).Therefore,one can conclude from the mor-phological identity of the patterns shown in Figs.4d–f and5and the patterns shown in sequence(a)of patterns in Fig.6,the splat cooling method with high-rate quench-ing gives metastable phases of spinodally decomposed liquid–liquid separation.We note in particular that the worm-like patterns shown in Figs.4d–f and5are directly related to the liquid–liquid phase separation and not to some form of aging process in the solid crystalline state.To support this,it should be noted that the rapid cooling process led to a drastic decrease in the temperature of the splats down the room temperature,which led to a sluggish atomic diffusion in the solid state with no possibility of causing phase separa-tion by the spinodal mechanism in the solid state.This argument confirms that the spinodal mechanism is able to quench high-temperature liquid–liquid phase separation. To the best of the authors’knowledge,patterns of spinodal decomposition in high-temperature metallic liquids(partic-ularly,in Co–Cu alloy melt)have not previously been observed and described in the literature.Therefore,in the following subsections,quantitative estimations also con-firm the above idea about spinodal decomposition in the Co–Cu melt.The preferential Gibbs free energy difference on phase decomposition by the spinodal mechanism is compared with the Gibbs free energy difference on primary solidification(Sections4.2.3and Appendix A.3).The spinodal phase separation shown here has been experimentally foundfirst in this work by SEM analysis5.Bright-field TEM image exhibits the spinodally decomposed structure of Co50Cu50sample shown in Fig.4e.The Co-rich phase imaged as dark and the Cu-rich phase as bright.The composition of phase is Co71.7Cu28.3and the composition of the Cu phase26.8Cu73.2.61(2013)1078–10921083of the microstructure of rapidly quenched metallic under-cooled Co–Cu liquids.The dark Co-rich worm-like phase in Fig.4d has an average diameter of 0.29l m and the next-neighbor distance is about 0.4l m.The Co-rich band structures found by TEM and shown in Fig.5have a smal-ler characteristic size of about 0.1l m and a periodicity of 0.1–0.2l m compared with the spinodal patterns investi-gated by SEM.The specimens analyzed by SEM and TEM were produced from different splats,which have prob-ably been quenched by different quenching rates.The quenching and cooling rates are known to determine the thermal history of the sample.A common factor was also revealed for two types of structures (dendritic and spinodal)in different parts of the same sample shown in Fig.4c and d.Dendrites need more time to grow than spinodal structures,which are frozen in a very short time.Therefore,the den-dritic part of the splat is thicker than the spinodal ing the Landau theory of phase transitions (see Ref.Appendix A.1)and the standard thermodynamic method (see Ref.Appendix A.2),spinodal lines in the phase dia-gram of the Co–Cu system were calculated.The results of computation and the chemical compositions of phases on high-rate quenching are shown in Fig.1.Note that the measured chemical composition is indicated in Fig.1by h-symbols for various temperatures.It has been assumed that the composition has been the same since the beginning of the splat quenching process.However,it can be seen from Fig.1that these compositions are inside the spinodal region and close to the calculated spinodal boundary using the Landau theory (as described in Ref.Appendix A.1)at the temperature below T %1450K.This argument on mea-sured chemical composition,together with the described morphological feature of patterns (see first three para-graphs of this subsection),serve as proof of the identity of the experimentally obtained patterns as these patternsappear during spinodal decomposition in the Co–Cu alloy melt.4.2.Time of phase separation in spinodal decomposition and time for freezing the sampleIn Section 4.1the origin of microstructure observed has been discussed.However,a question about the actual stage at which the system has been frozen always arises for experimental quenching of metastable states and phases.Identification of the concrete stage of phase separation in the present investigation is a complicated task,for the fol-lowing two reasons at least.First,when investigating the spinodal decomposition in the metallic melt,we are dealing with a very fast transition from a highly unstable to a meta-stable state.Second,our liquid,freezing and frozen Co–Cu samples are non-transparent systems,making an experi-mental reconstruction of the detailed picture of the evolu-tion of phase separation quite difficult.Evaluation of the spinodal decomposition is possible using model calcula-tions and the final frozen microstructure.Therefore,we give several numerical estimations of characteristic time scales and spatial lengths appearing in spinodal decompo-sition and compare these with experimentally obtained common microstructural characteristics.In evaluating a spinodally decomposing Co 50Cu 50alloy melt we use two models.The first one is the Cahn–Hilliard model [26]which is described by a partial differential equa-tion of a parabolic type describing a so-called “parabolic evolution ”of a spinodally decomposing system under a long-wave (short-frequency)regime.The second model is a hyperbolic model described by a partial differential equa-tion of a hyperbolic type which assumes relaxation of the diffusion flux to its steady state (see,for details,Ref.[19]and references therein).This gives a so-called “hyperbolicResults of two-dimensional computational modeling for typical spatial patterns in binary systems [28].(a)Evolution (from left decomposed patterns developed by the fluctuation mechanism.(b)Evolution (from left to right)of patterns developed decomposition through the nucleation process.。
Temporal scaling for neutrons中子的时间尺度
Objectives
To develop, within a uniform framework: (1) Geological-mathematical models to quantitatively describe the accumulation of cosmogenic nuclides in evolving landforms, and to invert field and isotopic data to obtain landform ages and rates and frequencies of geological processes that act on these landforms. (2) Databases of basic and applied knowledge and data useful in the evaluation of cosmogenic data, drawn from all fields relevant to cosmogenic nuclide geochemistry: nuclear physics and cosmic-ray physics, chemistry and geochemistry, various fields of geology, atmospheric sciences, magnetism and paleomagnetism, statistics and mathematics.
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Software for all occasions
Software will satisfy computation and information needs in six areas:
patran错误日志及解决方法
2. USER WARNING MESSAGE 4124 (IFS3P)
THE SPCADD OR MPCADD UNION CONSISTS OF A SINGLE SET 在图中用了 RB3 的 MPC,其中 dependent node (ux,uy,uz), independent(ux,uy,uz,rx,ry,rz),有可 能是这里的问题。不过这个倒不影响计算结果。
^^^ RUN TERMINATED DUE TO EXCESSIVE PIVOT RATIOS IN MATRIX KLL. ^^^ USER ACTION: CONSTRAIN MECHANISMS WITH SPCI OR SUPORTI ENTRIES OR SPECIFY PARAM,BAILOUT,-1 TO CONTINUE THE RUN WITH MECHANISMS. 以前也遇到这种情况,这次遇到后,又在一节点加载了位移约束,就解决了。看来这 种错误主要是由于约束不够,线性方程组无解造成的。 还有可能是没有 equivalence,This should solve your problem or reduce the number of failed ratios.有一次就遇到此情况。
7. 常用材料定义对比表
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isotropic anisotropic(2) orthotropic(3) orthotropic(2) anisotropic(3) • Use a FORCE entry if you want to define a static, concentrated force at a grid point by 一个点的力 specifying a vector. • Use a FORCE1 entry if the direction is determined by a vector connecting two grid points. 两个点的力 • Use a FORCE2 entry if the direction is specified by the cross product of two such vectors. 以上的乘积
Radioactivedecay...
Radioactive decay lines from asymmetric supernova explosionsA.HungerfordLos Alamos National Laboratory,P.O.Box 1663,Los Alamos,NM 87545,USASteward Observatory,University of Arizona,USAAbstractHigh energy emission from supernovae provide a direct window into the quantity and distribution of radioactive elements produced in these bining supernova explosion calculations with 3D Monte Carlo c -ray transport,I have studied the effect mixing and asymmetries have on the hard X-ray and c -ray spectra.With sufficient spectral resolution,the emission line profiles from nickel decay have enough information to distinguish between spherical and mildly asymmetric supernova explosions.Ó2003Elsevier B.V.All rights reserved.PACS:95.85.Pw;97.60.BwKeywords:c -rays ;Supernovae;Asymmetries1.IntroductionThe past decade has brought great strides in observational and theoretical studies of core-col-lapse supernovae,with interest stimulated by the wealth of data (and surprises)obtained from SN 1987A.For theoretical work in particular,the early emergence of hard X-and c -ray emission from SN 1987A (X-rays:e.g.Dotani et al.,1987;c -rays:e.g.Cook et al.,1988;Mahoney et al.,1988;Matz et al.,1988)signaled a departure from the spherically symmetric geometry that had been as-sumed in models of core-collapse explosions to that point.The appearance of this high energy emission,nearly 6months earlier than theorists had predicted,was most readily explained by theoutward mixing of the nickel synthesized in the inner layers of the explosion (e.g.Pinto and Woosley,1988a;Arnett et al.,1989a,b and refer-ences therein).In addition,line profiles from iron (the daughter product of nickel decay)were broadened to roughly 3500km/s (Spyromilio et al.,1990),further evidence that nickel had been mixed to large radii in the homologous supernova ejecta.This qualitative explanation for the observations motivated several groups to investigate,at a de-tailed level,the multidimensional instabilities which give rise to such mixing within the context of massive star explosions (Arnett et al.,1989a,b;Hachisu et al.,1990;Herant and Benz,1992;Kifonidis et al.,2000).The hydrodynamical sim-ulations carried out by these groups resulted in extended spatial distributions of the nickel,but not sufficiently extended to match the line profiles of the iron emission from SN 1987A.E-mail address:**************(A.Hungerford).1387-6473/$-see front matter Ó2003Elsevier B.V.All rights reserved.doi:10.1016/j.newar.2003.11.001New Astronomy Reviews 48(2004)19–24/locate/newastrevA number of ways to enhance the mixing in theoretical calculations,thus bringing them into agreement with observations,were proposed by Herant and Benz(1992):(1)the decay of56Ni could inject enough energy to force additional mixing,(2)convection in the pre-collapse core could seed more vigorous mixing and(3)global asymmetries in the explosion mechanism itself could enhance mixing along a particular direction in the explosion.This third possibility has been invoked to explain several other observational puzzles regarding core-collapse events.Nagataki et al.(1998)found that not only could slight asymmetries in the supernova explosion produce the required mixing to explain1987A,but they could also explain anomalies in the nucleosyn-thetic yields produced by several supernovae. Furthermore,the most straightforward explana-tion of the large polarization seen in core-collapse supernovae(see Leonard and Filippenko,2001 and references therein)is that the explosion driv-ing these supernovae is inherently asymmetric (H€oflich,1991).In addition,the high observed velocities of pulsars and the formation scenarios of neutron star binaries both suggest that neutron stars are given strong kicks at birth.These kicks are most easily explained by some asymmetry in the supernova explosion where the neutron star is born(see Fryer et al.,1996for a review).In this proceeding,we present theoretical c-ray spectra calculated using asymmetric supernova models as input to a Monte Carlo c-ray transport code.The asymmetry of the input model is moti-vated by the strong asymmetries that stellar rota-tion has been shown to produce in the supernova explosion(M€o nchmeyer and M€u ller,1989;Janka and M€o nchmeyer,1989;Fryer and Heger,2000; Khokhlov et al.,1999).The nature of these asymmetries depends upon the angular momen-tum profile of the collapsing star and,although most calculations predict jet-like explosions along the rotation axis,some calculations imply that an equatorial explosion could occur(M€o nchmeyer and M€u ller,1989).Our spectral calculations were carried out for both a jet-like explosion with axis ratio of2:1(motivated by Fryer and Heger(2000); we refer to this explosion model as Jet2)and a symmetric explosion model(Symmetric).Our analysis of these model spectra concentrates on the differences in total luminosity and line profile shape with the introduction of realistic explosion asymmetries.Since the progenitor star used as in-put to our simulations was a15M red supergiant, we are unable to directly compare our calculated spectra with the observed high energy spectra of SN1987A.However,we discuss how our models compare to various spectral trends observed from SN1987A.2.c-ray line profilesThe high energy spectra were calculated using a Monte Carlo technique,similar to that described in Ambwani and Sutherland(1988),for modeling c-ray transport in three-dimensions.Input models of the supernova ejecta(element abundances, density and velocities)were taken from3D SPH explosion simulations(Hungerford et al.,2003; models Jet2and Symmetric)and mapped onto a 140Â140Â140Cartesian grid.Escaping photons were tallied into250coarse energy bins,withfiner binning at the decay line energies to provide line profile information.The emergent photons were also tallied into11angular bins(D h¼10°)along the polar axis(the models investigated in this work are essentially axisymmetric,alleviating the need to tally in azimuthal angle as well.)A detailed look at the c-ray line profile shapes and strengths,for the1.238and0.847MeV56Co lines,reveals clear trends with viewing angle.Fig.1 shows line profiles of the0.847MeV56Co line for both the Symmetric and Jet2explosion models. We have placed this object at the distance of the Large Magellanic Cloud(60kpc)for easy com-parison withflux data from SN1987A observa-tions.The broadening of the line is caused by Doppler velocity shifts resulting from the spatial distribution of radioactive nickel in the homolo-gously expanding ejecta.The four panels are shown for days200,250,300and365after ex-plosion.The three lines in the Jet2spectra repre-sent different viewing angles through the ejecta (along the pole,the equator and an intermediate angle$45°.)For the Symmetric spectra,we have plotted these same viewing angles.20 A.Hungerford/New Astronomy Reviews48(2004)19–24As we can see from the abovefigure,both ex-plosion scenarios(Symmetric and Jet2)show blue-shifted line profiles,though to varying degree. These differences can be best understood by examining the physical effects which dictate the formation of the line profile edges.The blue edge to the lines is set by the maximum observed line of sight velocity of the56Co in the ejecta.Since the expansion is basically homologous after100days, the line of sight velocity of afluid element in the ejecta is proportional to its distance above the mid-plane of the explosion.Each spectral energy bin in the line profile can be mapped to a unique line of sight velocity in the ejecta,which can in turn be mapped to a specific height above the mid-plane.For example,defining the line of sight to be along the z-axis,the line profile shape should be proportional to the total mass of cobalt summed in x and y as a function of z height in the ejecta. Therefore,the bluest edge of the line will arise from material that was mixed furthest out along the line of sight direction.Fig.2shows a contour plot of density(outer contour)and56Co number density(inner contour) for the Jet2and Symmetric models at t¼150days. Decay of56Co is the major source of c-ray pho-tons,so the inner contour essentially traces the surface of the emission region.The horizontal and vertical lines in Fig.2represent lines of sight from the ejecta surface to the emission source and are labeled with the optical depth along that line-of-sight.The dominant opacity for the hard X-and c-rays is Compton scattering offelectrons and,since the density contours remainroughly A.Hungerford/New Astronomy Reviews48(2004)19–2421spherical in both models,the optical depth from a given point to the ejecta surface is roughly constant.It is clear from Fig.2that the nickel was mixed further out in the polar direction (z -axis of Fig.2)of the asymmetric explosion.Following the arguments above,it is not surprising that the c -ray line profiles viewed along the polar direction are much more blue-shifted for the Jet2model than the Symmetric model.Fig.2does not show a very large difference in the extent of mixing along the equatorial direc-tion between the two models.Correspondingly,the blue edge of the Symmetric lines and the equator view of the Jet2lines are comparable.The red edge of the lines is determined by the escaping emission from 56Co with the smallest line of sight velocity in the ejecta.In a Symmetric model,this should be an indication of how deep into the ejecta we can see along a given viewing angle.However,there is a more pronounced effect at play in the asymmetric explosion models.Much of the c -ray emission for the equatorial view arises from the ‘‘tips’’of the elongated 56Co distribution.This material has a very low line of sight velocity for an equatorial observer,since it is being ejected predominantly in the polar direction.This allows for a significantly lower velocity red edge of the equator view lines,even though the optical depth profiles do not vary much between polar and equator viewing angles.It is interesting to note that the c -ray line pro-files from SN 1987A were in fact red-shifted,a trend that is not obtained with these simulations.Although the c -ray data uncertainties were quite high,this red-shift was also observed in the far infrared forbidden lines of FeII,providing verifi-cation for the c -ray line centroid measurements.As was discussed above,the spectral line shape is directly correlated with the total cobalt mass at a given z -coordinate along the line-of-sight.With this in mind,the observed red-shifted line profiles towards SN 1987A imply,not only a break in spherical symmetry,but also a break in axisym-metry of the ly,there should be more nickel/cobalt mass on the far side of SN 1987A Õs ejecta as seen from our viewing angle.Pulsar ve-locity distributions also support the need for some non-axisymmetry in core-collapse supernova ex-plosions.An interesting study,which will be ad-dressed in a future paper,is to link the magnitude of velocity kick imparted to a neutron star with the compositional asymmetry implied by the red-shif-ted line profiles of SN 1987A.3.Hard X-ray and c -ray spectrumFig.3is a logarithmic plot of the calculated photon flux (c /s/MeV/cm 2)across the entireenergyFig.2.Contour plots in the xz -plane of the Symmetric and Jet2explosion models at t ¼150days.Inner contour is for 56Co number density which traces the surface of the c -ray emitting region.Outer contour is for the mass density which follows electron density and thus traces the dominant opacity source (Compton scattering).The lines represent lines-of-sight through the ejecta for which the optical depth from emission region to ejecta surface has been calculated.Regardless of viewing angle,the optical depth of the 56Co ejected along the poles in the Jet2explosion remains quite low.Hence,it is this material that dominates the observed emission for all viewing angles in the aspherical explosion.22 A.Hungerford /New Astronomy Reviews 48(2004)19–24range investigated with these simulations(0.3keV to4MeV).Thefive panels are spectra from the different time slices;in each panel,we plot the spectrum for the Symmetric model,along with polar and equatorial views of the Jet2model.The effects of mixing are present in both these simula-tions,though at differing levels due to the differ-ences in explosion asymmetry.It can be seen immediately that the hard X-rays emerge earlier from the ejecta with a global explosion asymmetry (Jet2model).This holds regardless of viewing an-gle(pole versus equator)towards the explosion.As discussed in Section1,the observed high energy spectrum of SN1987A differed from the predictions of theoretical onion-skin models in two fundamental ways.Both the broad lines of nickel and the early emergence of the hard X-rays could be explained qualitatively by invoking a mixing argument.From a theoretical standpoint,including a1D prescription for that mixing makes the as-sumption that both data points can befit with one free parameter.However,the simulations in this work suggest that the addition of a global asym-metry will change the direct correlation between the emergence time and the degree of line broadening. That is to say,for a given hard X-rayflux,the Symmetric model will correspond to a single line profile,regardless of viewing angle.The Jet2model, however,produces similar hard X-ray continua for different viewing angles,but the line profile varies significantly with viewing angle.In fact,the data for SN1987A(the c-line profiles and hard X-ray continuum)were notfit well by1D models.In particular,the model10HMM(Pinto and Woos-ley,1988a),which was mixed sufficiently to account for theflux in the hard X-ray continuum observa-tions,resulted in c-line centroids that were shifted too far to the blue(Tueller et al.,1990).Although the uncertainties in these data were relatively large, this trend may be in the right direction to suggest a global asymmetry(i.e.,an asymmetric explosion scenario for SN1987A could produce thesame A.Hungerford/New Astronomy Reviews48(2004)19–2423hard X-rayflux level,but with a redder line profile than the symmetric explosion scenario). 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Matz,S.M.,Share,G.H.,Leising,M.D.,Chupp, E.L., Vestrand,W.T.,1988.Nature331,416.M€o nchmeyer,R.,M€u ller,E.,1989.In:€Ogelman,H.,van den Heuvel,E.P.J.(Eds.),NATO ASI Series,Timing Neutron Stars.ASI,New York.Nagataki,S.,Shimizu,T.M.,Sato,K.,1998.ApJ495,413. Pinto,P.A.,Woosley,S.E.,1988a.ApJ329,820. Spyromilio,J.,Meikle,W.P.S.,Allen,D.A.,1990.MNRAS 242,669.Tueller,J.,Barthelmy,S.,Gehrels,N.,Teegarden, B.J., Leventhal,M.,MacCallum,C.J.,1990.ApJ351,L41.24 A.Hungerford/New Astronomy Reviews48(2004)19–24。
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τ and T are Euclidean time and temperature. This means we have two distinct periodic boundary conditions in this case, which makes the mechanism of the sphaleron transition to be very complicate. In this letter we will explore this issue by introducing a simple (1+1)dimensional scalar field model and show the type of sphaleron transition is dependent on the circumference of the spatial coordinate. Now, let us start with Euclidean action SE = 1 dτ dx 2
arXiv:hep-th/9906002v2 18 Aug 1ysics, Korea Advanced Institute of Science and Technology, Taejon, 305-701, Korea. (February 1, 2008)
where k is modulus of elliptic function and √ 2 k κ= , 1+k 1+k β (k ) = µ √ . 1 + k2 (4)
Since Jacobian Elliptic function dn[y, κ] has period 2K (κ), where K is complete elliptic function [17], the circumference L is defined 3
KNTP-99-03
Spatial Compactification and Decay-Rate Behaviour
D. K. Parka , Soo-Young Leea , Hungsoo Kimb
a
Department of Physics, Kyungnam University, Masan, 631-701, Korea.
Ln =
2n K (κ), β (k )
(5)
where n is some integer. Using φs (x) the classical action for sphaleron solution is straightforwardly computed:
Ln /2 S1 1 ∂φs Sn dx + U (φ s ) = n , ≡ P 2 ∂x P −Ln /2 2 2 2 2 S1 (1 − k ) a µ (1 + k ) 4E (κ) − = K (κ) , 2 P 3 β (k ) 1 + k 1 + k2
∂φ ∂τ
2
1 + 2
∂φ ∂x
2
where U (φ) is usual inverted double well potential U (φ ) = −
+ U (φ ) ,
(1)
µ2 2 µ2 4 2 2 ( φ − a ) + a. 2a2 2a2
(2)
It is very easy to show that sphaleron transition for the model (1) with usual noncompactified spatial coordinate is smooth second order if non-linear perturbation [12] or number of negative modes approach [13] are employed. Both approaches yield an identical sufficient condition for the first-order sphaleron transition and are very useful for the discussion of the effect of the arbitrary wall thickness in the bubble nucleation [14]. Fig. 1 describes action-vs-temperature diagram in this simple model, which shows the type of the sphaleron transition to be second order. Now, let us consider action (1) with a compactified spatial coordinate. In this case as mentioned before sphaleron solution φs (x) must satisfy a periodic boundary condition φs (x) = φs (x + L). The explicit expression of φs (x) is [15,16] φs (x) = a β (k )dn[β (k )x, κ], µ (3)
(6)
where P is period of sphaleron solution, i.e., 1/T and E is another complete elliptic function. Since S/P is interpreted as a barrier height of energy, the barrier height with L = Ln is n-times higher than that with L = L1 , and hence decay-rate is negligible for large n. In this letter, therefore, we will confine ourselves to only L = L1 case. Now we apply the result of non-linear perturbation presented in Ref. [12] in this model. For this we expand φ(x, τ ) around sphaleron φs (x); φ(x, τ ) = φs (x) + η (x, τ ), where η (x, τ ) is small fluctuation field. Inserting it into the equation of motion ∂2φ ∂2φ + = U ′ (φ ), ∂τ 2 ∂x2 one can get ˆ ˆ + G2 [η ] + G3 [η ], lη = hη where ∂2 ˆ l = 2, ∂τ 2 ˆ = − ∂ + U ′′ (φs ), h ∂x2 1 G2 [η ] = U ′′′ (φs )η 2 , 2 1 ′′′′ G3 [η ] = U (φs )η 3 . 6 ˆ is standard Lam´ It is well-known [16] that the eigenvalue equation of h e equation: 4 (10) (9) (8) (7)
Abstract
The transition from instanton-dominated quantum tunneling regime to sphaleron-dominated classical crossover regime is explored in (1+1)dimensional scalar field theory when spatial coordinate is compactified. It is shown that the type of sphaleron transition is critically dependent on the circumference of the spatial coordinate.
1
Recently, much attention is paid to the winding number transition from instanton [1]dominated quantum tunneling regime to the sphaleron [2,3]-dominated classical crossover regime in SU (2)-Higgs model [4–7], which is believed to describe electroweak phase transition in early universe. The active research in this field is mainly for the hope to understand baryon number violating process, which is very important consequence of electroweak chiral anomaly [8]. Since, unfortunately, the sphaleron transition in SU (2)-Higgs model or real electroweak theories is too complicated to treat and it needs lot a numerical calculation, it is very hard to understand the real mechanism of the electroweak phase transition by investigating these models directly. Hence a decade ago Mottola and Wipf(MW) [9] adopted a non-linear O (3) model with a soft symmetry breaking term as a toy model for the study of baryon number violating process. This model has an advantage that analytical expression of the sphaleron solution can be derived by paralleling Manton’s original argument. Recently, the sphaleron transition in this model with and without Skyrme term is examined [10,11]. Comparing, however, the result of Ref. [11] with that of Ref. [5], one can obviously conclude that MW model in itself cannot play a key role of toy model for electroweak theory when MH > 6.665MW , where MH and MW are masses of Higgs and W particles, respectively. In this region SU (2)-Higgs theory exhibits a smooth second-order sphaleron transition, while MW model exhibits a first-order sphaleron transition in the full range of its parameter space. Hence it may be helpful in understanding the real nature of the electroweak phase transition if one can find a simple toy model which exhibits both first-order and second-order sphaleron transitions. We argue in the present letter that this can be achieved by giving a nontrivial topology to the spatial coordinate. If we impose a compactified spatial coordinate x, it naturally generates a periodic boundary condition φ(x = 0) = φ(x = L), where φ is arbitrary scalar field and L is a circumference of a compactified spatial coordinate. On the other hand, the decay transition of a metastable state at finite temperature is governed by classical configuration which satisfies another periodic boundary condition at temporal coordinate: φ(τ = τ0 ) = φ(τ = τ0 + 1/T ), where 2