Origin for the enhanced copper spin echo decay rate in the pseudogap regime of the multilay
基于Origin的金属线膨胀系数实验数据处理方法
其 中 的 比例 系 数 a 为 固体 的线 膨 胀 系数 ( 称 线 胀 系 数 ) 称 简 . 实验还发现 , 同一 材 料 在 不 同温 度 区域 , 线 胀 系 数 不 一 定 相 同 . 是 , 温 度变 化不 大 的 范 围 内 , 胀 系 数 仍 可 认 为 是 其 但 在 线
误差.
关 键 词 : ii 件 ; 据 处理 ; 属 线 膨 胀 系数 ; 差 法 Or n软 g 数 金 逐 中图 分 类 号 : 4 5 0 3 文献标志码 : B
金 属 线 膨 胀 系 数 测 量 是 大 学 物 理 实 验 中 的 基 础 实 验 之 一 , 常 实 验 采 用 热 学 实 验 综 合 仪 进 行 , 量 过 程 比较 简 单 . 通 测 但 是 , 验 数 据 的处 理 相 对 复 杂 , 且人 为 因 素较 多. 实 而 目前 , 主要 采 用 等 差 法 、 乘 法 等 进 行 数 据 处 理 , 是 这 些 方 法 主观 性 大 , 二 但
作者简介 : 刘
研究.
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2 2用 逐 差 法处 理 实 验 数 据 .
刘 杨 : 于 Or i 基 i n的金 属 线 膨 胀 系 数 实 验 数 据 处 理 方 法 g
要 : O ii 件 对金 属 线膨 胀 系数 实验 数 据 进 行 了 线性 拟 舍 与作 图 , 合 的 结 果 与 所 作 图形 均 与 逐 差 法 进 行 数 用 r n软 g 拟
据处理的结果相吻合. 实验 表 明 : 用 O ii 件 处 理 实验 数 据 具 有 简 洁 、 捷 与 直 观 等 特 点 , 免 了人 为 因素 所 造 成 的 利 r n软 g 快 避
AE自带插件中英文对照
AE自带插件中英文对照3D Channel (3D通道)3D Channel Extract-------------3D通道扩展Depth Matte--------------------深厚粗糙Depth of Field-----------------深层画面Fog 3D-------------------------3D 雾化ID Matte-----------------------ID 粗糙Adjust (调整)Brightness & Contrast----------亮度与对比度Channel Mixer------------------通道混合器Color Balance------------------色彩平衡Color Stabilizer---------------色彩稳压器Curves-------------------------曲线Hue/Saturation-----------------色饱和Levels-------------------------色阶Levels (Individual Controls)---色阶 (分色RGB的控制) posterize----------------------色调分离Threshold----------------------阈值Audio (音频)Backwards----------------------向后Bass & Treble------------------低音与高音Delay--------------------------延迟Flange & Chorus----------------边缘与合唱团 * High-Low Pass------------------高音/低音Modulator----------------------调幅器Parametric EQ------------------EQ参数Reverb-------------------------回音Stereo Mixer-------------------立体声混合器Tone---------------------------音调Blur & Sharpen (模糊与锐化)Clannel Blur-------------------通道模糊Compound Blur------------------复合的模糊Directional Blur---------------方向性的模糊Fast Blur----------------------快污模糊Gaussian Blur------------------高斯模糊Radial Blur--------------------径向模糊Sharpen------------------------锐化Unsharp Mask-------------------锐化掩膜 *Channel (通道)Alpha Levels-------------------ALPHA 层通道Arithmetic---------------------运算Bland--------------------------柔化Cineon Converter---------------间距转换器Compound Arithmetic------------复合运算Invert-------------------------反向Minimax------------------------像素化Remove Color Matting-----------去除粗颗粒颜色 *Set Channels-------------------调节通道Set Matte----------------------调节粗糙度Shift Channels-----------------转换通道Distort (变型)Bezier Warp--------------------Bezier 变型Bulge--------------------------鱼眼Displacement Map---------------画面偏移Mesh Warp----------------------网状变形Mirror-------------------------镜像Offset-------------------------偏移量Optics Compensation------------光学替换 (可制作球体滚动效果) Polar Coordinates--------------极坐标Reshape------------------------重塑Ripple-------------------------涟漪Smear--------------------------涂片Spherize-----------------------球型变形Transform----------------------变换Twirl--------------------------旋转变形Wave Warp----------------------波型变形Expression Controls (表达式控制)Angle Control------------------角度控制Checkbox Control---------------复选框控制Color Control------------------颜色控制Layer Control------------------图层控制Point Control------------------锐化控制Slider Control-----------------滑块控制Image Control (图像控制)Chaner Color-------------------改变颜色Color Balance (HLS)------------色彩平衡 (HLS)Colorama-----------------------着色剂Equalize-----------------------平衡Gamma/Pedestal/Gain------------GAMMA/电平/增益Median-------------------------中线PS Arbitrary MapPS-------------任意的映射Tint---------------------------去色Keying (键控制)Color Difference Key-----------差异的色键Color Key----------------------色键Color Range--------------------色键幅度Difference Matte---------------不同粗粗糙 (以粗颗粒渐变到下一张图) Extract------------------------扩展Inner Outer Key----------------内部、外部色键Linear Color Key---------------线性色键Luma Key-----------------------LUMA键Spill Suppressor---------------溢出抑制器Matte Tools (粗糙工具)Matte Cloker-------------------粗糙窒息物 *Simple Choker------------------简单的窒息物 *Paint (油漆)Vector Paint-------------------矢量油漆Perspective (透视)Basic 3D-----------------------基本的3DBevel Alpha--------------------倾斜 ALPHABevel Edges--------------------倾斜边Drop Shadow--------------------垂直阴影Render (渲染)4-Color Gradient---------------4色倾斜度Advanced Lightning-------------高级闪电Audio Spectrum-----------------音频光谱Audio Waveform-----------------音频波形Beam---------------------------射线Cell Pattern-------------------单元模式Ellipse------------------------椭圆Fill---------------------------填充Fractal------------------------分数维Fractal Noise------------------粗糙的分数维Grid---------------------------网格Lens Flare---------------------镜头光晕Lightning----------------------闪电Radio Waves--------------------音波Ramp---------------------------斜面Stroke-------------------------笔划 (与stylize-write on功能类似) Vegas--------------------------维加斯Simulation (模拟)Particle Playground------------粒子运动场Shatter------------------------粉碎Stylize (风格化)Brush Strokes------------------笔刷Color Emboss-------------------颜色浮雕Emboss-------------------------浮雕Find Edges---------------------查找边缘Glow---------------------------照亮边缘Leave Color--------------------离开颜色Mosaic-------------------------马赛克Motion Tile--------------------运动平铺Noise--------------------------噪音Roughen Edges------------------变粗糙边Scatter------------------------分散Strobe Light-------------------匣门光 *Texturize----------------------基底凸现Write-on-----------------------在.....上写 (与render-stroke功能类似)Text (文本)Basic Text---------------------基本的文本Numbers------------------------数字文本Path Text----------------------路径文本Time (时间)Echo---------------------------回响Posterize Time-----------------发布时间Time Difference----------------时间差别 *Time Displacement--------------时间偏移Transition (转场)Block Dissolve-----------------块溶解Gradient Wipe------------------斜角转场Iris Wipe----------------------爱丽斯转场 (三角形转场)Linear Wipe--------------------线性转场Radial Wipe--------------------半径转场Venetian Blinds----------------直贡呢的遮掩 (百叶窗式转场)Video (视频)Broadcast Colors---------------广播色Reduce Interlace Flicker-------降低频闪Timecode-----------------------时间码。
ASTMB33-2000电气用镀锡软的或退火的铜丝的标准规范
以下附件為ASTM B33 美國行業標准 對各種規格的導體做出相應要求!如延伸!敬請關注: 电线电缆专业网裡面又你需要的電纜專業資料.shall be determined by the wrapping and immersion test in accordance with6.5.5.6Joints—Necessary joints in the completed wire and in the wire and rods prior tofinal drawing shall be made in accordance with the best commercial practice.5.7Finish—The coating shall consist of a smooth continu-ous layer,firmly adherent to the surface of the copper.The wire shall be free of all imperfections not consistent with the best commercial practice.6.Test Methods6.1Tensile Strength and Elongation(Explanatory Note 5)—No test for tensile strength shall be required.The elonga-tion of wire whose nominal diameter is larger than0.0808in.(2.052mm)in diameter shall be determined as the permanent increase in length,expressed in percent of the original length, due to the breaking of the wire in tension,measured between gage marks placed originally10in.(254mm)apart upon the test specimen.The elongation of wire whose nominal diameter is0.0808in.and under may be determined as described above or by measurements made between the jaws of the testing machine.When the latter method is used,the zero length shall be the distance between the jaws at the start of the tension test and be as near10in.as practicable and thefinal length shall be the distance between the jaws at the time of rupture.The fracture shall be between gage marks in the case of specimens so marked or between the jaws of the testing machine and not closer than1in.(25.4mm)to either gage mark or either jaw.6.2Resistivity(Expanatory Note4)—The electrical resistiv-ity of the material shall be determined in accordance with Test Method B193.The purchaser may accept certification that the wire was drawn from rod stock meeting the international standard for annealed copper instead of resistivity tests on the finished wire.6.3Dimensional Measurements—Dimensional measure-ments shall be made with a micrometre caliper equipped with a vernier graduated in0.0001in.(0.0025mm).Measurements shall be made on at least three places on each unit selected for this test.If accessible,one measurement shall be taken on each end and one near the middle.The average of the three measurements shall determine compliance with the require-ments.6.4Continuity of Coating:6.4.1Specimens:6.4.1.1Length of Specimens—Test specimens shall have a length of about6in.(152mm).They shall be tagged or marked to correspond with the coil,spool,or reel from which they were cut.6.4.1.2Treatment of Specimens—The specimens shall be thoroughly cleaned by immersion in a suitable organic solvent such as benzene,ether,or trichloroethylene for at least3min; then removed and wiped dry with a clean,soft cloth(Caution-see Explanatory Note5).The specimens thus cleaned shall be kept wrapped in a clean,dry cloth until tested.That part of theTABLE1Tensile Requirements Diameter Area at20°Cin.mm cmil in.2mm2Elongation in10in. (250mm), %max0.460011.6840211600.000.166190107.219330 0.409610.4038167772.160.13176885.011430 0.36489.2659133079.040.10452067.432130 0.32498.2525105560.010.08290753.4880300.28937.348283694.490.06573342.408625 0.2576 6.543066357.760.05211733.624025 0.2294 5.826852624.360.04133126.665225 0.2043 5.189241738.490.03278121.1492250.1819 4.620333087.610.02598716.765725 0.1620 4.114826244.000.02061213.298025 0.1443 3.665220822.490.01635410.550925 0.1285 3.263916512.250.0129698.366925 0.1144 2.905813087.360.01027879 6.631525 0.1019 2.588310383.610.00815527 5.261520 0.0907 2.30388226.490.00646107 4.168420 0.0808 2.05236528.640.00512758 3.3081200.0720 1.82885184.000.00407150 2.626820 0.0641 1.62814108.810.00322705 2.082020 0.0571 1.45033260.410.00256072 1.652120 0.0508 1.29032580.640.00202683 1.307620 0.0453 1.15062052.090.00161171 1.039820 0.0403 1.02361624.090.001275560.822920 0.03590.91191288.810.001012230.653020 0.03200.81281024.000.000804250.5189200.02850.7239812.250.000637940.411620 0.02530.6426640.090.000502730.324320 0.02260.5740510.760.000401150.258820 0.02010.5105404.010.000317310.204715 0.01790.4547320.410.000251650.162415 0.01590.4039252.810.000198560.128115 0.01420.3607201.640.000158370.102215 0.01260.3200158.760.000124690.0804150.01130.2870127.690.000100290.064715 0.01000.2540100.000.000078540.050710 0.00890.226179.210.000062210.040110 0.00800.203264.000.000050270.032410 0.00710.180350.410.000039590.025510 0.00630.160039.690.000031170.020110 0.00560.142231.360.000024630.015910 0.00500.127025.000.000019630.0127100.00450.114320.250.000015900.010310 0.00400.101616.000.000012570.008110 0.00350.088912.250.000009620.006210 0.00310.07879.610.000007550.004910TABLE2Electrical Resistivity RequirementsNominal Diameter Resistivity at20°C in.mm V·lb/mile2V·g/m2 0.460to0.290,incl11.7to7.4,incl896.150.15695 Under0.290to0.103,incl Under7.4to2.6,incl900.770.15776 Under0.103to0.0201,incl Under2.6to0.51,incl910.150.15940 Under0.0201to0.0111incl Under0.51to0.28,incl929.520.16279 Under0.0111to0.0030,incl Under0.28to0.076,incl939.510.16454TABLE3Permissible Variations in Diamter Nominal Diameter of WirePermissible Variations in Diameterin.mm in.mm plus minus plus minus Under0.0100Under0.250.00030.000100.00760.0025 0.0100and over0.25and over3%1%3%1%specimen to be immersed in the test solution shall not be handled.Care shall be taken to avoid abrasion by the cut ends.6.4.2Special Solutions Required:6.4.2.1Hydrochloric Acid Solution(HCl)(sp gr1.088)—Commercial HCl(sp gr1.12)shall be diluted with distilled water to a specific gravity of1.088measured at15.6°C(60°F).A portion of HCl solution having a volume of180mL shall be considered to be exhausted when the number of test specimens prescribed in Table4of a size as indicated in6.4.3have been immersed in it for two cycles.6.4.2.2Sodium Polysulfide Solution(sp gr 1.142)(Ex-planatory Note7)—A concentrated solution shall be made by dissolving sodium sulfide cp crystals in distilled water until the solution is saturated at about21°C(70°F),and adding sufficient flowers of sulfur(in excess of250g/L of solution)to provide complete saturation,as shown by the presence in the solution of an excess of sulfur after the solution has been allowed to stand for at least24h.The test solution shall be made by diluting a portion of the concentrated solution with distilled water to a specific gravity of1.142at15.6°C(60°F).The sodium polysulfide test solution should have sufficient strength to blacken thoroughly a piece of clean untinned copper wire in 5s.A portion of the test solution used for testing samples shall not be considered to be exhausted until it fails to blacken a piece of clean copper as described above.6.4.3Procedure:6.4.3.1Immersion of Specimens—Immerse a length of at least41⁄2in.(114mm)from each of the clean specimens,in accordance with the following cycles,in test solutions main-tained at a temperature between15.6and21°C(60and70°F): (1)Immerse the specimen for1min in the HCl solution described in 6.4.2,wash,and wipe dry;(2)immerse the specimen for30s in the sodium polysulfide solution described in6.4.2,wash,and wipe dry;(3)immerse the specimen for1 min in the HCl solution,wash,and dry;(4)immerse the specimen for30s in the sodium polysulfide solution,wash,and wipe dry.6.4.3.2Washing Specimens—After each immersion,imme-diately wash the specimens thoroughly in clean water and wipe dry with a clean,soft cloth.6.4.3.3Examination of Specimens—After immersion and washing,examine the specimens to ascertain if copper exposed through openings in the tin coating has been blackened by action of the sodium polysulfide.The specimens shall be considered to have failed if,by such blackening,exposed copper is revealed.No attention shall be paid to blackening within0.5in.(12.7mm)of the cut end.A grayish brown appearance of the coating shall not constitute failure.6.5Adherence of Coating:6.5.1Specimens:6.5.1.1Length of Specimens—Test specimens shall be ap-proximately12in.(305mm)in length and shall be tagged or marked to correspond with the coil,spool,or reel from which they are cut.6.5.1.2Treatment of Specimens—The specimens shall be thoroughly cleaned,if required,by immersion in a suitable organic solvent such as benzene,ether,or trichloroethylene for at least3min,then removed and dried(Caution-see Explana-tory Note6).The specimens thus cleaned shall be kept wrapped in a clean dry cloth until tested.That part of the specimens to be immersed in the test solution shall not be handled.Care shall be taken to avoid abrasion of the surface to be subjected to test.Wire of sizes0.005in.(0.13mm)and smaller may be cleaned after wrapping around the mandrel.6.5.2Procedure:6.5.2.1Wrapping—Slowly wrap the test specimen in a suitable manner in an open helix around a polished mandrel having rounded ends and a diameter not to exceed four times the nominal diameter of the specimen.Take care not to stretch the specimen during the wrapping operation.The spacing of the consecutive turns shall be approximately equal to the diameter of the wire.For sizes0.021in.(0.53mm)and smaller, not more than six helical turns shall be used for the test,and for wire larger than0.021in.,not more than three turns shall be used.6.5.2.2Immersion Test—Remove the helically wrapped portion of the test specimen from the mandrel and immerse completely in the sodium polysulfide solution(see6.4.2)for30 s at the temperature prescribed in6.4.3.On removal from the sodium polysulfide solution,immediately rinse the specimen in clean water and remove the excess by shaking.6.5.2.3Examination of Specimens—Examine visually the outer peripheral surface of the helically wrapped portion of the specimen.For wires0.021in.(0.53mm)and smaller,a magnification not greater than three times may be used.Any cracking or parting of the coating in this area shown by blackening of the copper shall be cause for rejection.A grayish brown appearance of the coating after immersion shall not constitute failure.6.6Finish—Surface-finish inspection shall be made with the unaided eye(normal spectacles excepted).7.Inspection7.1General(Explanatory Note8and Note9)—Unless otherwise specified in the contract or purchaser order,the manufacturer shall be responsible for the performance of all inspection and test requirements specified.7.1.1All inspections and tests shall be made at the place of manufacture unless otherwise especially agreed upon between the manufacturer and the purchaser at the time of purchase.7.1.2The manufacturer shall afford the inspector represent-ing the purchaser all reasonable manufacturer’s facilities to satisfy him that the material is being furnished in accordance with this specification.7.1.3Unless otherwise agreed upon between the purchaser and the manufacturer,conformance of the wire to the various requirements listed in Section5shall be determined on samplesTABLE4Limiting Number of Test Specimens for Coating TestsNominal Diameter,in.Maximum Number of Specimens to be Tested for2Cycles in180mL of Acid Solution0.460to0.141,incl2 Under0.141to0.0851,incl4 Under0.0851to0.0501,incl6 Under0.0501to0.0381,incl10 Under0.0381to0.0301,incl12 Under0.0301to0.0030,incl14taken from each lot of wire presented for acceptance.7.1.4The manufacturer shall,if requested prior to inspec-tion,certify that all wire in the lot was made under suchconditions that the product as a whole conforms to therequirements of this specification as determined by regularlymade and recorded tests.7.2Definitions Applicable to Inspection :7.2.1lot (Explanatory Note 8)—any amount of wire of onetype and size presented for acceptance at one time,suchamount,however,not to exceed 25000lb (11350kg).7.2.2sample —a quantity of production units (coils reels,etc.)selected at random from the lot for the purpose ofdetermining conformance of the lot to the requirements of thisspecification.7.2.3specimen —a length of wire removed for test purposesfrom any individual production unit of the sample.7.3Sample Size (Explanatory Note 9)—The number ofproduction units in a sample shall be as follows:7.3.1For elongation and resistivity determinations,thesample shall consist of four production units.For continuityand adherence of coating tests,the sample shall consist of eightproduction units.From each unit,one test specimen of suffi-cient length shall be removed for the performance of therequired tests.7.3.2For dimensional measurements,the sample shall con-sist of a quantity of production units shown in Table 5underthe heading “First Sample.”7.3.3For surface-finish inspection and for packaging in-spection (when specified by the purchaser at the time of placingthe order)the sample shall consist of a quantity of productionunits shown in Table 6.8.Conformance Criteria (Explanatory Note 9)8.1Any lot of wire,the samples of which comply with theconformance criteria of this section,shall be considered ascomplying to the requirements of Section 5.Individual pro-duction units that fail to meet one or more of the requirementsshall be rejected.Failure of a sample group from a lot to meetone or more of the following criteria shall constitute cause forrejection of the lot.The conformance criteria for each of theprescribed properties given in Section 5are as follows:8.1.1Elongation —The lot shall be considered conformingif the average elongation of the four specimens is not less thanthe appropriate elongation value in Table 1plus 2.8%;however,any individual production unit,the specimen fromwhich has an elongation less than the appropriate elongationvalue in Table 1,shall be rejected.8.1.1.1The lot shall be considered to have failed to meet the elongation conformance criterion if the average of the four specimens is less than the elongation in Table 1plus 2.8%and the elongation of any of the individual specimens is less than the value in Table 1.8.1.1.2If the average of the four specimens is less than the elongation in Table 1plus 2.8%and the elongation of each of the individual specimens is equal to or more than the value in Table 1,six additional specimens from six production units other than the four originally sampled shall be tested.The lot shall be considered conforming if the elongation of each of the ten specimens is not less than the appropriate elongation value in Table 1,and the average of the ten specimens is not less than that value plus 2.8%.The lot shall be considered to have failed to meet the elongation requirement if any of the ten specimens is less than the appropriate elongation value in Table 1or if the average of the ten specimens is less than that value plus 2.8%.8.1.2Resistivity —The electrical resistivity of each of the four specimens shall conform to the requirements of 5.2.Failure to meet these requirements shall constitute failure to meet the resistivity conformance criterion.8.1.3Dimensions —The dimensions of the first sample (Table 5)shall conform to the requirements of 5.3.If there are no failures,the lot conforms to this requirement.If there are failures,but the number of these does not exceed the allowable defect number c 2(Table 5)for the respective number of units in the sample,a second sample equal to n 2shall be taken and the total defects of the n 1plus n 2units shall not exceed the allowable defect number,c 2.Failure to meet this requirement shall constitute failure to meet the dimensional conformance criterion.8.1.4Continuity of Coating —The continuity of the coating of each of the eight specimens shall conform to the require-ments of 5.4.Failure of more than two specimens shall constitute failure to meet the continuity criterion.If not moreTABLE 5Sampling for Dimensional MeasurementsNumber of Units in Lot First SampleSecond Sample Number of Units inSample,n 1Allowable Number of Defects in First Sample,c 1.Number of Units in Sample,n 2n 1plus n 2Allowable Number of Defects in Both Samples,c 21to 14,incl all0.........15to 50,incl 140.........51to 100,incl 19023421101to 200,incl 24046702201to 400,incl 290761053401to 800,incl 3301121454Over 8003401161504TABLE 6Sampling for Surface Finish and Packaging Inspection Number of Units in Lot Number of Units in Sample,n Allowable Number of Defective Units,c 1to 30,incl all 031to 50,incl 30051to 100,incl 370101to 200,incl 400201to 300,incl 702301to 500,incl 1002501to 800,incl 1303Over 8001554than two specimens fail to meet the continuity criterion,eightadditional specimens from the lot shall be tested,all of whichshall conform to the continuity criterion.However,any indi-vidual production unit,the specimen from which failed to meetthe continuity criterion,shall be rejected.8.1.5Adherence of Coating —The adherence of the coatingof each of the eight specimens shall conform to the require-ments of 5.5.Failure of more than two specimens shallconstitute failure to meet the adherence criterion.If not morethan two specimens fail to meet the adherence criterion,eightadditional specimens from the lot shall be tested,all of whichshall conform to the adherence criterion.However,any indi-vidual production unit,the specimen from which failed to meetthe adherence criterion,shall be rejected.8.1.6Surface Finish —The surface finish of the samplestaken in accordance with Table 6shall conform to the require-ments of 5.7.The number of units in the sample showingsurface defects not consistent with commercial practice shallnot exceed the allowable defect number c ,in Table 6.Failureto meet this requirement shall constitute failure to meet thesurface-finish conformance criterion.8.1.7Packaging —Conformance to the packaging require-ments specified by the purchaser shall be determined in accordance with Table 6.The number of units in the sample showing nonconformance to the requirement shall not exceed the allowable defect number,c ,in Table 6.Failure to meet this requirement shall constitute failure to meet the packaging conformance criterion.9.Density (Explanatory Note 10)9.1For the purpose of calculating linear densities,cross sections,etc.,the density of the copper shall be taken as 8.89g/cm 3(0.32117lb/in.3)at 20°C.10.Packaging and Shipping 10.1Package sizes shall be agreed upon by the manufac-turer and the purchaser in the placing of individual orders.10.2The tinned wire shall be protected against damage in ordinary handling and shipping.11.Keywords 11.1tinned annealed copper wire;tinned copper electrical wire;tinned soft copper wireEXPLANATORY NOTESN OTE 1—It is necessary that the coating of tin on the wire becontinuous.The test in the sodium polysulfide is for the purpose ofdetermining whether or not the wire carries a continuous envelope of puretin.The thickness of the tin coating is necessarily varied.Under the sameconditions of tinning,the coating on all sizes of wire,excepting on finewire,is approximately the same.The coating on fine wire is in generalrelatively heavier than that on coarse wire.It is not,therefore,correct toapply a larger number of cycles in the test on coarse wire than is appliedto fine wire.It is probable that one cycle of the dip test would be sufficientto discover defects in tinned wire,but in order to make certain that nopartially covered spots may escape attention,provision has been made fortwo cycles.It has been found that the tin coating on copper wire consistsof two parts,an envelope of pure tin on the outside,with an intermediatelayer of copper-tin alloy.This tin alloy,as well as the amount of tinpresent,has an effect on the resistivity of the wire.Since the relativeamount of tin coating and alloy is greater on the small wire than it is onthe coarser wire,the resistivity of the wire increases as the size decreases.This also accounts for the decrease in elongation due to tinning soft wire.N OTE 2—The values of the wire diameters in Table 1are given to thenearest 0.0001in.and correspond to the standard sizes given in Specifi-cation B 258.The use of gage numbers to specify wire sizes is notrecognized in this specification because of the possibility of confusion.Anexcellent discussion of wire gages and related subjects is contained in NBSHandbook 100of the National Bureau of Standards.N OTE 3—Other tests than those provided in this specification have beenconsidered at various times,such as twist tests,wrap tests,etc.It is theopinion of the committee that twist tests on soft wire serve no usefulpurpose and that wrap tests,other than that provided for in 6.5,which is a test for adhesion,are likewise undesirable and inconclusive as to results and significance.N OTE 4—“Resistivity”is used in place of “percentage conductivity.”The value of 0.15328V ·g/m 2at 20°C is the international standard for the resistivity of annealed copper equal to 100%conductivity.This term means that a wire 1m in length and weighing 1g would have a resistance of 0.15328V .This is equivalent to a resistivity value of 875.20V ·lb/mile 2,which signifies the resistance of a wire 1mile in length weighing 1lb.It is also equivalent,for example,to 1.7241µV /cm of length of a bar 1cm 2in cross section.A complete discussion of this subject is contained in NBS Handbook 100of the National Bureau of Standards.The presence of tin and of copper-tin alloy in the coating of the wire increases the resistance of the finished wire as mentioned in Note 1.Relationships that may be useful in connection with the values of resistivity prescribed in this specification are as shown in Table 7,each column containing equivalent expressions at 20°C.N OTE 5—In general,tested values of tensile strength are increased and tested values of elongation are reduced with increase of speed of the moving head of the testing machine in the tension testing of copper wire.In the case of tests on soft or annealed copper wire,however,the effects of speed of testing are not pronounced.Tests of soft wire made at speeds of moving head,which under no-load conditions are not greater than 12in./min,do not alter the final results of tensile strength and elongation determinations to any practical extent.N OTE 6—Caution:Consideration should be given to toxicity and flammability when selecting solvent cleaners.N OTE 7—It is important that the polysulfide solution be of propercomposition and strength at the time of test.A solution that is not saturatedTABLE 7Resistivity ValuesConductivity at 20°C,%100.0097.6697.1696.1694.1693.15V ·lb/mile 2875.20896.15900.77910.15929.52939.51V ·g/m 20.153280.156940.157750.159400.162790.16454V ·cmil/ft10.37110.61910.67410.78511.01511.133V ·mm 2/m0.0172410.0176540.017745.0179300.0183120.018508µV ·in.0.678790.695040.698630.705900.720920.78267µV ·cm 1.7241 1.7654 1.7754 1.7930 1.83121.8508with sulfur or that has been made from decomposed sodium sulfidecrystals may give a false indication of failure.Therefore,the requirementthat the solution be tested by observing its blackening effect on a brightcopper wire is significant.Significant also is the requirement that thesolution be saturated with sulfur by allowing the solution to stand at least24h after preparation.Attention is called also to the necessity for the useof sodium sulfide that has not deteriorated through exposure to air;and ifexposure has occurred,the crystals should be tested for purity.The“Standard Reagents Tests”of the American Chemical Society are useful inthis connection.N OTE 8—A lot should comprise material taken from a product regularlymeeting the requirements of this specification.Inspection of individuallots of less than 5000lb of wire cannot be justified economically.Forsmall lots of 5000lb or less,the purchaser may agree to the manufactur-er’s regular inspection of the product as a whole,as evidence of acceptability of such small lots.N OTE 9—Cumulative results secured on the product of a single manu-facturer,indicating continued conformance to the criteria,are necessary to ensure an over-all product meeting the requirements of this specification.The sample sizes and conformance criteria given for the various charac-teristics are applicable only to lots produced under these conditions.N OTE 10—The value of density of copper is in accordance with the International Annealed Copper Standard.The corresponding value at 0°C is 8.90g/cm 3(0.32150lb/in.3).In calculations involving density it must be borne in mind that the apparent density of coated wire is not a constant but a variable function of wire diameters.The smaller the diameter,the greater the percentage of coating present and hence the greater departure from the density of copper.The American Society for Testing and Materials takes no position respecting the validity of any patent rights asserted in connection with any item mentioned in this ers of this standard are expressly advised that determination of the validity of any such patent rights,and the risk of infringement of such rights,are entirely their own responsibility.This standard is subject to revision at any time by the responsible technical committee and must be reviewed every five years and if not revised,either reapproved or withdrawn.Your comments are invited either for revision of this standard or for additional standards and should be addressed to ASTM Headquarters.Your comments will receive careful consideration at a meeting of the responsible technical committee,which you may attend.If you feel that your comments have not received a fair hearing you should make your views known to the ASTM Committee on Standards,at the address shown below.This standard is copyrighted by ASTM,100Barr Harbor Drive,PO Box C700,West Conshohocken,PA 19428-2959,United States.Individual reprints (single or multiple copies)of this standard may be obtained by contacting ASTM at the above address or at 610-832-9585(phone),610-832-9555(fax),or service@ (e-mail);or through the ASTM website().。
乒乓球运动的发展英语作文
乒乓球运动的发展英语作文Title: The Development of Table Tennis。
Table tennis, also known as ping pong, has witnessed remarkable growth and evolution since its inception. Fromits humble origins to becoming an Olympic sport, thejourney of table tennis exemplifies the fusion of tradition and modernity in sports. In this essay, we will explore the key milestones and factors contributing to the developmentof table tennis.Firstly, let's delve into the historical roots of table tennis. The origins of table tennis can be traced back to Victorian England in the late 19th century. Initiallyplayed as an after-dinner parlor game among the upper class, it soon gained popularity across social strata due to its accessibility and engaging nature. The early version oftable tennis involved makeshift equipment, such asmakeshift paddles and simple balls, and improvised playing surfaces like dining tables.The modernization of table tennis began in the early20th century, particularly with the establishment of formal rules and regulations. The formation of the International Table Tennis Federation (ITTF) in 1926 marked a significant milestone, providing a platform for standardization and global governance of the sport. With standardized equipment specifications and competition guidelines, table tennis transitioned from a recreational pastime to a competitive sport.Throughout the mid-20th century, table tennis experienced a surge in popularity, especially in Asia. Countries like China, Japan, and South Korea emerged as dominant forces in the sport, showcasing exceptional skill and technique on the international stage. The emergence of iconic players such as Zhuang Zedong, Deng Yaping, and Jan-Ove Waldner further propelled the global appeal of table tennis and inspired generations of enthusiasts.The inclusion of table tennis in the Olympic Games in 1988 marked a watershed moment for the sport, elevating itsstatus to that of a mainstream athletic discipline. Since then, table tennis has been a staple feature of the Olympics, captivating audiences worldwide with its fast-paced rallies and precision gameplay. The Olympic platform not only provides exposure and recognition to top players but also fosters grassroots development and participation in table tennis across diverse demographics.In recent years, technological advancements have revolutionized the landscape of table tennis. Innovations such as high-performance rubbers, carbon-fiber blades, and automated training systems have enhanced the speed, spin, and control of the game. Furthermore, the advent of online platforms and digital coaching resources has democratized access to training and knowledge, empowering enthusiasts to improve their skills and connect with the global table tennis community.Looking ahead, the future of table tennis appears promising, fueled by ongoing efforts to expand its reach and relevance. Initiatives such as Table Tennis for All (TT4ALL) aim to promote inclusivity and diversity withinthe sport, ensuring that table tennis remains accessible to people of all ages, backgrounds, and abilities. Moreover, collaborations between the ITTF and other organizationsseek to innovate and adapt table tennis to evolvingsocietal trends and preferences, thereby sustaining its appeal in the modern era.In conclusion, the development of table tennis embodies a rich tapestry of tradition, innovation, and globalization. From its origins as a leisurely diversion to its status asa global sporting phenomenon, table tennis continues to captivate hearts and minds around the world. Through strategic partnerships, technological advancements, and a commitment to inclusivity, the future of table tennisshines brightly, promising new heights of excellence and enjoyment for generations to come.。
超高强铜钛合金的研究现状
Metallurgical Engineering 冶金工程, 2020, 7(3), 121-129Published Online September 2020 in Hans. /journal/menghttps:///10.12677/meng.2020.73018超高强铜钛合金的研究现状崔振山1,黄岚1,孟祥鹏2,雷前1*,肖柱3,李周31中南大学粉末冶金国家重点实验室,湖南长沙2宁波博威合金材料股份有限公司,浙江宁波3中南大学材料科学与工程学院,湖南长沙收稿日期:2020年8月11日;录用日期:2020年8月24日;发布日期:2020年8月31日摘要超高强弹性铜合金是一类具有优异强度和导电导热性能的材料,目前已经广泛应用于载流元器件、电磁继电器以及航空航天器件等领域,其中Cu-Ti系合金因其优异的力学性能和加工成型性而得到关注。
本文综述了超高强铜钛合金的合金成分设计、制备加工工艺和相关物理性能,在此基础上分析了铜钛合金开发应用中所需要解决的问题,并对铜钛合金的未来发展趋势进行了分析和展望。
关键词高耐热铜合金,高强,高导,时效强化Research Progress of Ultrahigh-StrengthCopper-Titanium AlloysZhenshan Cui1, Lan Huang1, Xiangpeng Meng2, Qian Lei1*, Zhu Xiao3, Zhou Li31State Key Laboratory of Powder Metallurgy, Central South University, Changsha Hunan2Ningbo Powerway Alloy Material Co. Ltd, Ningbo Zhejiang3School of Materials Science and Engineering, Central South University, Changsha HunanReceived: Aug. 11th, 2020; accepted: Aug. 24th, 2020; published: Aug. 31st, 2020AbstractUltra-high strength elastic copper alloys with excellent strength, conductive and thermal conduc-*通讯作者。
双核铜配合物,电子结构
© 2013 American Chemical Society
■
INTRODUCTION
metal ions;8 in cases where these are redox active, the overall redox sequence may be even more multifaceted than for porphyrins and their mononuclear complexes.9 However, few studies have yet addressed in detail the redox processes and redox sites in expanded porphyrins.9,10 A prominent expanded porphyrin scaffold is [28]hexaphyrin that can be chemically oxidized to [26]hexaphyrin 1 (Scheme 1), which is associated with a switch from Möbius to Hückel aromaticity.11 The metalation of expanded porphyrins, such as hexaphyrin 1 and its N-confused isomer, is versatile, though not always predictable.6b For example, in homobimetallic complexes of 1 two AuIII are found with an {N2C2} donor set,12 while two HgII were observed binding in an {N2C} fashion.13
Origin Effects DELUXE61 用户手册说明书
OWNER’S MANUALVersion 1.0ORIGIN EFFECTS® is a registered trademark of Origin Effects Limited.All other product names and trademarks are the propertyof their respective owners and are hereby acknowledged.MARSHALL® is a registered trademark of Marshall Amplification PLC.Origin Effects has no affiliation with Marshall Amplification PLC.BOSS® is a registered trademark of the Roland Corporation.Origin Effects has no affiliation with the Roland Corporation.FENDER® is a registered trademark of Fender Musical Instruments Corporation.Origin Effects has no affiliation with Fender Musical Instruments Corporation.No part of this publication may be reproduced in any form or by any means,whether mechanical or electronic,without the written permission of Origin Effects Limited. Origin Effects Limited reserves the right to change the features and specifications described herein without notice or obligation.Origin Effects Limited cannot be held responsible for any loss or damage arising directly or indirectly from any error or omission in this manual.PLEASE READ ALL INSTRUCTIONS,PAY ATTENTION TO SAFETY WARNINGS.Document version 1.0© Origin Effects Limited 2021IMPORTANT:This product is designed to be powered from a 9VDC, >100mApower supply with 2.1mm centre-negative barrel connector.ContentsIntroducing the DELUXE61 4 Connecting the DELUXE61 5 Main Controls: 6 POST-DRIVE EQ Controls 7 Setting Your POST-DRIVE EQ 8 Sample Settings 9 Appendix A: Physical Specification 10 Appendix B: Performance Specification 10 Appendix C: Connector Pin Out 10 Appendix D: Safety Notices11 Appendix E: Warranty 12Introducing the DELUXE61The DELUXE61 is an all-analogue amp recreation which captures the thick overdrive tones and beautiful bias tremolo of the revered Fender® Brown Deluxe amp. We have gone to great lengths to recreate every detail of this iconic amplifier, bringing you the tones, feel and response of this classic combo in one industrial-grade pedal.First released in 1961, this modest, little amp is still one of history’s most sought-after guitar tones, thanks largely to its tremolo circuit. Bias tremolo is considered by many to be the most musical of all the tremolo types due to its natural, pulsating character. Because the tremolo acts on the amp’s output valves, overdriven sounds will let you “play through” the tremolo. The effect disappears when you pick hard, slowly fading back in as the note dies away – you can control the tremolo effect with your picking dynamics or your guitar’s volume knob! The DELUXE61’s circuit includes an entire push-pull output stage, complete with an output transformer and reactive load, which means this pedal’s tremolo is every bit as responsive as the real thing – but with the added versatility of tap tempo and a speed multiplier switch.With our powerful Post-Drive EQ, the warm cleans and gritty overdrive of the DELUXE61 will always sound their best, whether it’s plugged into an amp, a flat power amp or direct to a recording interface or PA. Key Features:All-Analogue Amp Recreation Including:• Rich clean tones and growly overdrive voiced after the 1961 Fender® Brown Deluxe• True bias tremolo with authentic, touch-sensitive dynamic response• Complete valve amp-style signal pathusing discrete, transistor-based circuitry Flexible, Intuitive Controls:• Footswitch input jack for tap tempo and effects swither integration• Powerful tone-shaping POST-DRIVE EQ Peerless Build Quality:• High-current, low-noise electronics • Ultra-high input impedance• High-quality buffered bypass• Advanced power supply filtering and protection• Premium components throughout • Designed and built in EnglandConnecting the DELUXE61Main ControlsON (footswitch):independently.DRIVE:TONE:-cies above the 12 o’clock poisition and cut highs below 12 o’clock. With DRIVE pushed past 12 o’clock, the TONE control progressively loses the ability to boost until, with DRIVE at maximum, it’s essentially a high cut control.OUTPUT: The output control sets the pedal’s overall output level. This control comes after the pedal’s simulated valve amp circuitry, meaning that you can adjust output level without affecting the tone or character of the overdrive.SPEED: Turn clockwise to increase the rate of the tremolo effect. The range of the SPEED control is set by the three-position MULTI switch.INTENSITY: The INTENSITY knob controls the depth of the tremolo – in other words, how much the tremolo will vary the amplitude of the signal. Turn clockwise to increase the depth of the effect.Main Controls (continued)MUL TI: The MULTI switch multiplies the tremolo speed set by the SPEED knob (x1, x2 or x3). This is par-ticularly useful when using an external tap tempo footswitch, letting you set tremolo speeds much faster than your foot can tap.SHAPE: The SHAPE switch allows you to choose between two different LFO waveforms.SINE WAVE (up) – This is the classic bias tremolo sound – ultra-smooth, rounded and musical.FULL WAVE (down) – This setting uses an asymmetrical waveform with a ‘choppier’ feel. Thismore obvious tremolo sound can be useful at slower speeds or when playing with more overdriven sounds.POST-DRIVE EQ ControlsThe POST-DRIVE EQ ensures compatibility with a wide range of amplifiers. Instead of altering your amp or its tone controls to suit the DELUXE61, set your amp for the desired clean sound then use the EQ controls to tailor the pedal’s output accordingly.POST-DRIVE EQ switch: This switch offers a choice of three different output filters.P/AMP: Use this setting when plugging into a flat-response power amp, mixer or recording interface. Select-ing the P/AMP setting disengages the ADJ variable filter control (see below).EQ1: Designed to suit the response of a Black Panel Fender®-style amp, EQ1 applies a low-pass filter to roll off excessive highs. Use this setting when plugging into a bright-voiced guitar amp.EQ2: Voiced for connecting to a Marshall®-style amp, EQ2 applies a high shelf cut to gently rein in high fre-quencies. Use this setting when plugging into a fuller-sounding, mid-rich amp.POST-DRIVE EQ Controls (continued)ADJ: When EQ1 or EQ2 is selected, the ADJ knob lets you fine-tune the pedal’s output to suit the individ-ual response of your amp and the way its controls are set. As you turn the ADJ knob counterclockwise, this proprietary filter design gradually rolls off bass and adjusts the high shelf response. The end result is a very powerful and intuitive control. If your amp sounds too bright or thin with the DELUXE61 engaged, turn the ADJ control clockwise. If it sounds too dark and wooly, turn the ADJ control counterclockwise. Setting Y our POST-DRIVE EQUse the tables below to help you set up the DELUXE61 for the first time with a new guitar amplifier orflat-response device. Working through Steps 1 and 2 allows you to “set-and-forget” the POST-DRIVE EQ controls and move on to having fun dialling in your ideal tone with the main controls.Step 1: Set POST-DRIVE EQ switch for the connected amp or device.Step 2: Fine-tune the POST-DRIVE EQ with the ADJ control**Please note: the ADJ control is not active when the POST-DRIVE EQ switch is in the P/AMP position.Sample SettingsAppendix A: Physical SpecificationAppendix B: Performance SpecificationAppendix C: Connector Pin Out Footswitch 1/4” TRS socket:Instrument & Amplifier 1/4” TS Sockets:Appendix D: Safety NoticesGeneral SafetyKeep these instructions and heed all warnings. Do not use this apparatus near water. Clean only witha dry cloth. Do not install near any heat sources such as radiators, heat registers, stoves or other apparatus (including amplifiers) that produce heat. Refer all servicing to qualified service personnel. When using an external power supply, use only attachments/accessories specified by Origin Effects. Protect the power cord from being walked on or pinched particularly at plugs, convenience receptacles, and the point where they exit from the apparatus. Do not defeat the safety purpose of the polarised or grounding-type plug. A polarised plug has two blades with one wider than the other. A grounding type plug has two blades and a third grounding prong. The wide blade or the third prong are provided for your safety. If the provided plug does not fit into your outlet, consult an electrician for replacement of the obsolete outlet. Unplug this apparatus during lightning storms or when unused for long periods of time.CAUTION! No user-servicable parts inside. In the event of damage to the unit service orrepair must be done by qualified service personnel only.This Product is CE compliant.This product is UKCA compliant.FCC CertificationThis equipment has been tested and found to comply with the limits for a Class B digital device, pursuant to part 15 of the FCC Rules. These limits are designed to provide reasonable protection against harmful interference in a residential installation. This equipment generates, uses and can radiate radio frequency energy and, if not installed and used in accordance with the instructions, may cause harmful interference to radio communications. However, there is no guarantee that interference will not occur in a particular installation. If this equipment does cause harmful interference to radio or television reception, whichcan be determined by turning the equipment off and on, the user is encouraged to try to correct the interference by one or more of the following measures:• Reorient or relocate the receiving antenna.• Increase the separation between the equipment and receiver.• Connect the equipment into an outlet on a circuit different from that to which the receiver is connected.• Consult the dealer or an experienced radio/TV technician for help.Appendix D: Safety Notices (continued)The crossed out wheely bin symbol indicates this product is classified as Waste Electricaland Electronic Equipment (WEEE) in the European Union and should not be discardedwith household waste. Other territories may vary. Contact your local authority or OriginEffects for more information.This product conforms to the European Union’s directive 2011/EU on Restrictions ofHazardous Substances (RoHS).WARNING: This product can expose you to chemicals including nickel, which is known to the State of California to cause cancer. For more information, go to Evaluation of apparatus based on altitude not exceeding 2000m. There may be some potential safety hazard if the apparatus is operated at altitude exceeding 2000m. Evaluation of apparatus based on temperate climate conditions only. There may be some potential safety hazard if the apparatus is operated in tropical climate conditions.Appendix E: WarrantyThis product is covered by a 2-year manufacturer’s warranty from the date of purchase. This applies only to original purchasers who have bought their product from an authorised Origin Effects dealer or directly from Origin Effects.All returns or servicing should be arranged through the original dealer. Proof of original ownership may be required in the form of a purchase receipt.For full warranty details visit /warranty .RoHS。
GE磁共振简称
An apparatus maintaining a very low constant temperature. The cryostat consists of one concentric, cylindrical container housed in an outer vacuum tight vessel. The magnet and shim coils are mounted in the inner container. The container is filled with liquid helium. The shields surrounding the inner container are kept cold by a refrigeration device.
ICW
Installation Calibration Wizard. This wizard is available in two different modes: Install and Upgrades. It can be found in the proprietary Common Service Desktop under the "Calibration" tab. Maintenance mode is available after all calibrations and tasks in the install mode are complete.
PS
Power Supply
PSD
Pulse sequence data base
PT
Patient Transport or Patient Table
QUENCH
oc调整金属材质的反射强度 索引
oc调整金属材质的反射强度索引摘要:一、OC 简介1.OC 是什么2.OC 在游戏中的作用二、金属材质反射强度的调整1.调整反射强度的方法2.影响反射强度的因素3.实际操作案例三、索引的作用1.索引的定义2.索引的重要性3.如何使用索引正文:OC,全称OverClock,是指对计算机硬件进行超频操作,以提高硬件性能。
在游戏领域,OC 常用于提高显卡性能,让玩家在游戏中获得更好的画面效果和流畅度。
金属材质在游戏中的表现,很大程度上取决于其反射强度。
调整金属材质的反射强度,可以有效地改善游戏画面的真实感和视觉体验。
下面将详细介绍如何调整金属材质的反射强度。
首先,我们需要了解调整反射强度的方法。
一般来说,我们可以通过修改材质的贴图文件,或者直接修改游戏的配置文件来实现反射强度的调整。
具体操作方法因游戏和材质而异,需要玩家自行研究。
影响金属材质反射强度的因素有很多,例如材质的表面光滑度、颜色、光照强度等。
在进行调整时,需要综合考虑这些因素,以达到理想的效果。
以下是一个实际操作案例:某游戏中的金属材质反射强度过高,导致画面过于刺眼。
为了解决这个问题,我们首先找到该材质的贴图文件,然后使用图片编辑软件调整贴图中的反射强度。
经过多次尝试,最终找到了一个合适的反射强度值,使得画面效果更加舒适。
索引在调整金属材质反射强度过程中也起着重要作用。
索引是一种对材质、纹理、光照等信息进行整理和分类的方式,可以帮助玩家更快地找到需要调整的参数。
在进行调整时,可以借助索引快速定位到相关内容,提高调整效率。
总之,调整金属材质的反射强度是一项需要技巧和经验的工作。
ASME_SB-359-2007_带内鳍的铜和铜合金无缝冷凝器和热交换器管子
2007SECTION II,PART B SB-359 SPECIFICATION FOR COPPER AND COPPER-ALLOY SEAMLESS CONDENSER AND HEAT EXCHANGERTUBES WITH INTEGRAL FINSSB-359(Identical with ASTM Specification B359-95for the alloys covered except for editorial differences.Certification has been made mandatory.)1.Scope1.1This specification describes seamless copper and copper alloy tubing on which the external or internal sur-face,or both,has been modified by a cold-forming processto produce an integral enhanced surface for improved heat transfer.The tubes are used in surface condensers,evapora-tors,and heat exchangers and are normally made from the following copper or copper alloys:Copper orCopperAlloyUNS No.Type of MetalC12200DHP phosphorized,high residual phosphorusC44300Admiralty Metal Types B,C44400C,andC44500DC7060090-10Copper-NickelC7100080-20Copper-Nickel Type AC7150070-30Copper-NickelNOTE1—Refer to Practice E527for explanation of Unified Numbering System(UNS).1.2The following safety hazard caveat pertains onlyto the test methods described in this specification.1.2.1This standard does not purport to address allof the safety concerns,if any,associated with its use.It is the responsibility of the user of this standard to establish appropriate safety and health practices and determine the applicability of regulatory limitations prior to use.NOTE2—A complete metric companion,B359M,has been developed; therefore,no metric equivalents are presented.2.Referenced Documents2.1ASTM Standards:B153Test Method for Expansion(Pin Test)of Copper and Copper-Alloy Pipe and Tubing481B154Test Method for Mercurous Nitrate Test for Copper and Copper AlloysB170Specification for Oxygen-Free Electrolytic Cop-per—Refinery ShapesB359M Specification for Copper and Copper-Alloy Seam-less Condenser and Heat Exchanger Tubes with Integral Fins[Metric]E3Methods of Preparation of Metallographic Specimens E8Test Methods for Tension Testing of Metallic Materials E29Practice for Using Significant Digits in Test Data to Determine Conformance With SpecificationsE53Methods for Chemical Analysis of CopperE62Test Methods for Chemical Analysis of Copper and Copper Alloys(Photometric Methods)E112Test Methods for Determining Average Grain Size E118Test Methods for Chemical Analysis of Copper-Chromium AlloysE243Practice for Electromagnetic(Eddy-Current)Exami-nation of Copper and Copper-Alloy TubesE255Practice for Sampling Copper and Copper Alloys for Determination of Chemical CompositionE478Test Methods for Chemical Analysis of Copper AlloysE527Practice for Numbering Metals and Alloys(UNS)3.Terminology3.1Definitions:3.1.1flattening—this term shall be interpreted as that condition which allows a micrometer caliper,set at three times the wall thickness,to pass over the tube freely throughout theflattened part,except at the points where the change in element offlattening takes place.3.1.2lengths—straight pieces of the product.--````,,`````,`,`,,,```,,,`,,`-`-`,,`,,`,`,,`---SB-3592007SECTION II,PART B3.1.2.1lengths,specific—straight lengths that are uniform in length,as specified,and subject to established length tolerances.3.1.3tube,seamless—a tube produced with a contin-uous periphery in all stages of operation.3.1.3.1tube,condenser—See tube,heat exchanger.3.1.3.2tube,heat exchanger—a tube manufac-tured to special requirements as to dimensional tolerances,finish,and temper for use in condensers and other heat exchangers.3.1.3.3tube,heat exchangers with integral enhanced surface—a tube having an external or internal surface,or both,modified by a cold forming operation,to produce an enhanced surface for improved heat transfer. The enhancement may take the form of longitudinal or helicalfins or ridges,or both,as well as modifications thereto.3.1.4unaided eye—corrective spectacles necessaryto obtain normal vision may be used.4.Ordering Information4.1Purchase for tubes described in this specification should include the following,as required,to describe the tubes adequately.4.1.1ASME designation and year of issue,4.1.2Alloy,4.1.3Temper,4.1.4Dimensions:diameter,wall thickness,length and location of unenhanced surfaces,and total tube length. Configuration of enhanced surfaces shall be as agreed upon between the manufacturer and the purchaser(Refer to Figs. 1,2,and3),4.1.5Whether the product is to be subsequently welded,4.1.6Quantity,4.1.7Certification,which is mandatory,4.1.8Mill test report,when required,4.1.9When heat identification or traceability is required.5.General Requirements5.1Tubes covered by this specification shall normallybe furnished with unenhanced ends,but may be furnished with enhanced ends or stripped ends from which the outside diameter enhancement has been removed by machining.482FIG.1OUTSIDE DIAMETER ENHANCED TUBENOMENCLATURENote—The outside diameter over the enhanced section will not normally exceed the outside diameter of theunenhanced section.dd od rd ix px ft t=======outside diameter ofunenhanced sectionoutside diameter of theenhanced sectionroot diameter of the enhancedsectioninside diameter of the enhancedsectionwall thickness of theunenhanced sectionwall thickness of theenhanced sectiontransition taper5.1.1The enhanced sections of the tube in the as-fabricated temper are in the cold-worked condition pro-duced by the enhancing operation.The unenhanced sec-tions of the tube shall be in the annealed or light drawn temper,and shall be suitable for rolling-in operations.6.Materials and Manufacture6.1The material shall be of such quality and purity that thefinished products shall conform to the requirements prescribed in this specification and shall be cold-worked to the specified size.To comply with this specification,the enhanced and unenhanced material must be homogeneous.6.2Due to the discontinuous nature of the processing of castings into wrought products,it is not practical to identify specific casting analysis with a specific quantity offinished material.6.3When heat identification is required,the purchaser shall specify the details desired in the purchase order or contract.7.Chemical Composition7.1The tubes shall conform to the chemical require-ments specified in Table1.2007SECTION II,PART B SB-359 FIG.2OUTSIDE DIAMETER AND INSIDE DIAMETER ENHANCED TUBE NOMENCLATUREd d o d r d i x p x f t t =======outside diameter ofunenhanced sectionoutside diameter over theenhanced sectionroot diameter of the enhancedsectioninside diameter of the enhanced sectionwall thickness of theunenhanced sectionwall thickness of theenhanced sectiontransition taperFIG.3INSIDE DIAMETER ENHANCED TUBE NOMENCLATURETABLE1CHEMICAL REQUIREMENTSCopper Composition,%orCopper Nickel,Other Alloy incl Lead,Man-Named UNS No.Copper A Tin Aluminum Cobalt Max.Iron Zinc ganese Arsenic Antimony Phosphorus Chromium Elements C1220099.9min............................0.015–0.040......C4430070.0–73.00.9–1.2......0.070.06max.Remainder...0.02–0.06............C4440070.0–73.00.9–1.2......0.070.06max.Remainder......0.02–0.10.........C4450070.0–73.00.9–1.2......0.070.06max.Remainder.........0.02–0.10......C70600Remainder......9.0–11.00.05 1.0–1.8 1.0max.B 1.0max.......B...B C71000Remainder......19.0–23.00.050.50–1.0 1.0max.B 1.0max.......B...B C71500Remainder......29.0–33.00.050.40–1.0 1.0max.B 1.0max.......B...BA Copper(including silver).B When the product is for subsequent welding applications,and so specified in the contract or purchase order,zinc shall be0.50%max.,lead0.02%,phosphorus0.02%max.,sulfur and carbon0.05%max.483--````,,`````,`,`,,,```,,,`,,`-`-`,,`,,`,`,,`---SB-3592007SECTION II,PART BTABLE2TENSILE REQUIREMENTSTensile YieldTemper Designation Strength,Strength,BMin.Min.Copper or Copper Alloy UNS No.Standard Former ksi A ksi AC12200O61Annealed309CC12200H55Light-drawn3630C44300,C44400,C44500O61Annealed4515C70600O61Annealed4015C71000O61Annealed4516C71500O61Annealed5218A ksi p1000psi.B At0.5%extension under load.C Light straightening operation is permitted.7.2These specification limits do not preclude the pres-ence of other elements.Limits for unnamed elements maybe established by agreement between manufacturer or sup-plier and purchaser.7.2.1For alloys in which copper is specified as the remainder,copper may be taken as the difference between the sum of the results for all specified elements and100%for the particular alloy.7.2.1.1When analyzed,copper plus the sum of results for specified elements shall be as shown in the following table.Copper Plus Named Copper Alloy UNS No.Elements,%minC7060099.5C7100099.5C7150099.57.2.2For alloys in which zinc is specified as the remainder,either copper or zinc may be taken as the differ-ence between the sum of the results of specified elements analyzed and100%.7.2.2.1When all specified elements are deter-mined the sum of results plus copper shall be as follows:Copper Plus Named Copper Alloy UNS No.Elements,%Min.C4430099.6C4440099.6C4450099.68.Temper8.1The tube after enhancing shall be supplied,as speci-fied,in the annealed or as-fabricated temper.8.1.1The enhanced sections of tubes in the as-fabri-cated temper are in the cold-worked condition producedby the fabricating operation.4848.1.2The unenhanced sections of tubes in the as-fabricated temper are in the temper of the tube prior to enhancing,annealed or light drawn,and suitable for roll-ing-in operations.8.1.3Copper alloys C44300,C44400,and C44500, furnished in the as-fabricated temper,must be stress relief annealed after enhancing and be capable of meeting the requirements of the mercurous nitrate test in section12. Stress relief annealing of the copper and other copper alloys described by this specification is not required.8.1.3.1Some annealed tubes,when subjected to aggressive environments,may be subject to stress-corro-sion cracking failure because of the residual tensile stresses developed in straightening.For such applications,it is rec-ommended that tubes of copper alloys C44300,C44400, and C44500,be subjected to a stress relieving thermal treatment subsequent to straightening.When required,this must be specified on the purchase order or contract.Toler-ance for roundness and length,and the condition for straightness,for tube so ordered,shall be to the require-ments agreed upon between the manufacturer and pur-chaser.8.1.4The enhanced sections of tubes in the annealed temper shall show complete recrystallization when exam-ined in the cross-section of the tube at a magnification of 75diameters.Average grain size shall be within the limits agreed upon between the manufacturer and purchaser, when measured in the wall of the tube outside of the enhanced area.9.Tensile Properties9.1Prior to the enhancing operations,the tube shall conform to the requirements for tensile properties pre-scribed in Table2.2007SECTION II,PART B SB-359TABLE3EXPANSION REQUIREMENTSExpansion of Tube Temper Designation Outside Diameter inCopper or Copper Alloy Percent of OriginalStandard Former UNS No.Outside DiameterO61Annealed C1220030H55Light-drawn C1220020061Annealed C44300,C44400,C4450020061Annealed C7060030061Annealed C7100030061Annealed C715003010.Expansion Test10.1The unenhanced sections of all tubes selected for test shall conform to the requirements prescribed in Table3when tested in accordance with B153.The expanded tube shall show no cracking or rupture visible to the unaided eye.11.Flattening Test11.1The unenhanced lengths of tube selected for tests shall beflattened on different elements and aflattened element shall show no cracking or rupture visible to the unaided eye.(Corrective spectacles necessary to obtain normal vision may be used.)12.Mercurous Nitrate Test12.1Each specimen shall withstand an immersion in the mercurous nitrate solution as prescribed in Test MethodB154without cracking.The enhanced specimens shall include thefinished tube ends.12.2This test is required only for copper alloysC44300,C44400,and C44500.13.Nondestructive Testing13.1Each tube shall be subjected to a nondestructive test.Tubes shall normally be tested in the as-fabricated temper,but,at the option of the manufacturer,may be tested in the annealed temper.Unless otherwise specified, the manufacturer shall have the option of testing the tubesby one of the following test methods.13.1.1Eddy-Current Test—The tubes shall be passed through an eddy-current testing unit adjusted per the requirements of19.3.3to provide information on the suitability of the tube for the intended application.13.1.1.1Tubes causing irrelevant signals becauseof moisture,soil,and like effects may be reconditioned and retested.Such tubes shall be considered to conform, should they not cause output signals beyond the acceptable limits.48513.1.1.2Tubes causing irrelevant signals because of visible and identifiable handling marks may be retested by the hydrostatic test prescribed in13.1.2or the pneumatic test prescribed in13.1.3.13.1.1.3Unless otherwise agreed,tubes meeting the requirements of either test shall be considered to con-form if the tube dimensions are within the prescribed limits.13.1.2Hydrostatic Test—Each tube,without show-ing evidence of leakage,shall withstand an internal hydro-static pressure sufficient to subject the material in the unenhanced region of the tube to afiber stress of7000psi, as determined by the following equation for thin hollow cylinders under tension.P p2St/(D−0.8t)where:P p hydrostatic pressure,psigt p thickness of tube wall,in.D p outside diameter of tube,in.S p allowablefiber stress of the material,psiThe tube need not be tested at a hydrostatic pressure of over1000psi,unless so specified.13.1.3Pneumatic Test—Each tube,after enhancing, shall withstand a minimum internal air pressure of250 psig for5s and any evidence of leakage shall be cause for rejection.The test method used shall permit easy visual detection of any leakage,such as having the tube under water,or by the pressure differential method.14.Dimensions and Permissible Variations14.1Diameter—The outside diameter of the unen-hanced sections shall not vary by more than the amount shown in Table4,as measured by“go”and“no go”ring gages.The diameter over the enhanced sections shall not exceed the diameter of the plain sections involved,as deter-mined by a“go”ring gage unless otherwise specified. 14.2Wall Thickness—No tube shall be less than the minimum thickness specified in the plain sections or in the enhanced sections.--````,,`````,`,`,,,```,,,`,,`-`-`,,`,,`,`,,`---SB-3592007SECTION II,PART BTABLE4DIAMETER TOLERANCESSpecified Diameter,in.Tolerance,in.0.500and under±0.002Over0.500–0.740,incl±0.0025Over0.740–1.000,incl±0.003TABLE5LENGTH TOLERANCESSpecified Length,ft Tolerance,All Plus,in.Up to20,incl1⁄8Over20–30,incl5⁄32Over30–60,incl1⁄4TABLE6SQUARENESS OF CUTSpecified OutsideDiameter,in.ToleranceUp to5⁄8,incl0.010in.Over5⁄80.016in./in.of diameter 14.3Length—The length of the tubes shall not be less than that specified when measured at a temperature of 68°F,but may exceed the specified value by the amounts given in Table5.14.3.1The length of the unenhanced end(s)as mea-sured from the tube end to thefirstfin disk impression, shall not be less than that specified,but may exceed the specified value by1⁄2in.14.4Squareness of Cut—The departure from square-ness of the end of any tube shall not exceed the values given in Table6.15.Workmanship,Finish,and Appearance15.1Roundness,straightness,uniformity of wall thick-ness,and condition of inner and outer surfaces of the tube shall be such as to make it suitable for the intended application.Unless otherwise specified on the purchase order,the cut ends of the tubes shall be deburred by useof a rotating wire wheel or other suitable tool.15.2Annealed-temper or stress-relieved tubes shall be clean and smooth but may have a superficial,dull iridescent486film on both the inside and the outside surface.Tubes in the as-fabricated temper may have a superficialfilm of finning lubricant on the surfaces.16.Sampling16.1The lot size,portion size,and selection of sample pieces shall be as follows:16.1.1Lot Size—600tubes or10000lbs or fraction of either,whichever constitutes the greater weight.16.1.2Portion Size—Sections from two individual lengths offinished product.16.1.2.1Samples taken for purposes of test shall be selected in a manner that will correctly represent the material furnished and avoid needless destruction offin-ished material when samples representative of the material are available from other sources.16.2Chemical Composition—Samples for determining composition shall be taken in accordance with Practice E 255.The minimum weight of the composite sample shall be150g.16.2.1Instead of sampling in accordance with Prac-tice E255,the manufacturer shall have the option of sam-pling at the time castings are poured or sampling the semi-finished product.When samples are taken during the course of manufacture,sampling of thefinished product is not required and the minimum number of samples to be taken shall be as follows:16.2.1.1When samples are taken at the time cast-ings are poured,one sample shall be taken for each group of castings poured simultaneously from the same source of molten metal.16.2.1.2When samples are taken from the semi-finished product,one sample shall be taken to represent each10000lbs or fraction thereof,except that not more than one sample shall be required per piece.17.Number of Tests and Retest17.1Tests:17.1.1Chemical composition shall be determined as the arithmetic mean of at least two replicate determinations of each specified element.17.1.2All other tests specified in sections8through 12shall be conducted on specimens taken from each of the samples selected in accordance with16.1.17.2Retest:17.2.1One retest shall be permitted for each require-ment under the same conditions stated for the original test.17.2.2Should the result of a retest fail to conform with the requirements of the product specification,the material shall be rejected.2007SECTION II,PART B SB-35918.Specimen Preparation18.1Preparation of the analytical test specimen shallbe the responsibility of the reporting laboratory.18.2Specimens for the microscopic examination shallbe prepared in accordance with Methods E3.18.2.1The surface of the specimen shall approximatea radial longitudinal section of the tube.18.3Specimens for the expansion test shall be of suit-able length so that they can be expanded the required amount.Both ends shall either be faced square in a lathe,or suitably prepared so as to have a smooth surface free from scratches or burrs,and with both edges slightly cham-fered.18.4Specimens for theflattening test require no special preparation,but shall be of the length necessary to accom-modate the test.18.5Specimens for the mercurous nitrate test shall be6inches in length and shall be taken from the enhanced and unenhanced portion of each sample.18.6Tension test specimens shall be of the full sectionof the tube and shall conform to the requirements of the‘Test Specimen’section of Test Methods E8,unless the limitations of the testing machine precludes the use of such specimen in which case test specimens conformingto specimen No.1of Fig.13in Test Methods E8shallbe used.18.6.1Whenever test results are obtained from full-sized and machined specimens and they differ,the results from the full-sized specimen shall prevail for determining conformance to the specification.18.6.2Although a considerable range of testing speed is permissible,the range of stressing to the yield strength should not exceed100ksi/min.Above the yield strength the movement per minute of the testing machine head under load shall not exceed0.5in./in.of the gage length,or distance between grips for a full section specimen.19.Test Methods19.1Chemical Composition:19.1.1The methods used for routine determinationof specification compliance shall be at the discretion of the reporting laboratory.19.2Chemical composition for all other alloys,in caseof disagreement,shall be determined as follows:487Element Range Test Method Copper99.75to99.99E53,Electrolytic Copper70.0to99.75E478,ElectrolyticTin0.9to1.2E478,Photometric Aluminum 1.8to6.5E478Nickel incl.Cobalt 4.8to33.0E478,GravimetricLead0.05to0.10E478,Atomic Absorption Iron0.04to1.8E478Zinc14.0to30.0E478,TitrimetricZinc to1.0E478,Atomic Absorption Manganese to1.0E62Arsenic0.02to0.5E62Antimony0.02to0.1E62Phosphorus0.001to0.04E62Chromium0.30to0.70E11819.2.1Test methods for the determination of ele-ments resulting from contractual or purchase order agreements shall be as agreed upon between the manufac-turer or supplier and purchaser.(Refer to Table1,Foot-note D.)19.3The material shall conform to the physical require-ments and mechanical properties enumerated in this speci-fication when tested in accordance with the following methods:Test ASTM DesignationGrain Size E112Expansion(Pin Test)B153Mercurous Nitrate B154Tension E8Eddy-Current Test E24319.3.1Grain Size—The intercept method shall be used to determine grain size in case of dispute.19.3.2Test Method B154—Warning:This test method involves the use of a mercury compound that is classified as a health hazard in use and disposal.19.3.3Eddy-Current—Testing shall follow the pro-cedures of Practice E243,except that the sensitivity set-tings of the test equipment shall be adjusted using the hole sizes specified in Table7of this specification.The holes for sensitivity adjustment shall be drilled radially through an unenhanced portion of the standard tube or through a length of prime surface tube of the same size,temper,and composition.By mutual agreement between the manufac-turer or supplier and purchaser,discontinuities of other contours may be used on the calibration standard.19.3.3.1Tubes that do not actuate the signaling device on the eddy current tester shall be considered as conforming to the requirements of this test.20.Significance of Numerical Limits20.1For purposes of determining compliance with the specified limits of the properties listed in the following table,an observed or calculated value shall be roundedSB-3592007SECTION II,PART Bas indicated in accordance with the rounding method of Practice E29.Rounded Unit for ObservedProperty or Calculated Value Chemical composition Nearest unit in the last right-hand place offiguresTensile strength,yield strength Nearest ksiGrain size:Nearest multiple of0.005mmUp to0.055mm,incl,Over to the nearest0.010mm0.055mm21.Inspection21.1The manufacturer shall inspect and make neces-sary tests to verify that the tubes furnished conform to the requirements of this specification.21.2Should the purchaser additionally elect to perform his own inspection,the manufacturer shall,without charge, afford the inspector all reasonable facilities to determine that the tubes being furnished conform to the requirementsof this specification.21.2.1Except for chemical analysis all tests and inspection shall be made at the place of manufacture priorto shipment,unless otherwise specified,and shall be so conducted as not to interfere with the operation of the facility.21.3When automatedfinishing and inspection equip-ment is available at a facility,purchaser and manufacturer may,by mutual agreement,accomplish thefinal inspection simultaneously.22.Rejection and Rehearing22.1Material that fails to conform to the requirementsof this specification when inspected or tested by the pur-chaser,or purchaser’s agent,may be rejected.22.2Rejection shall be reported to the manufacturer,or supplier,promptly and in writing.22.3The manufacturer or supplier may make claim fora rehearing when dissatisfied with the test results.488TABLE7DIAMETER OF DRILLED HOLESNominal Diameter Over Diameter of Enhanced or Unenhanced Section,in.Drilled Holes,in. 1⁄4–5⁄8,incl0.042–No.58drill Over5⁄8–1,incl0.046–No.56drill23.Certification23.1A manufacturer’s certificate of compliance shall be furnished to the purchaser stating that samples represent-ing each lot have been tested and inspected in accordance with this specification and the requirements have been met.l Test Report24.1When specified on the purchaser order or contract, the manufacturer or supplier shall furnish to the purchaser a manufacturer’s test report showing results of the required tests.25.Packaging and Package Marking25.1The material shall be separated by alloy,size,and temper.It shall be packaged in such a manner as to ensure acceptance by common carrier for transportation and to afford protection from the normal hazards of transportation.25.2Each shipping unit shall be legibly marked with the name of supplier,purchase order number,metal or alloy designation,temper,size,total length or piece count, or both.25.3The specification number shall be shown when specified.26.Keywords26.1copper;copper alloys;seamless;condenser;heat exchanger;tube;integralfins,```,,,`,,`-`-`,,`,,`,`,,`---。
Origin三板斧,轻松处理XPS各种谱图
Origin三板斧,轻松处理XPS各种谱图Origin处理XPS多元素谱图1、将ASC码文件用NOTEPAD打开:2、复制Y轴数值。
打开ORIGIN,将Y轴数据粘贴到B(Y):3、如图:点击工具栏plot,选择line4、出现下图:点击B(Y),再点击<->Y,使B(Y)成为Y轴数据。
然后在“set X values”中输入起始值和步长。
5、点击OK,得到下图:6、利用ORIGIN提供的工具可以方便的进行平滑、位移。
A. 位移:1)如图:选择analysis→translate→vertical或horizontal可以进行水平或垂直方向的位移。
我们以水平位移为例进行讲解。
2)在图中双击峰顶,如图示(小窗口给出的是此点的X,Y值)3)然后在图中单击其他位置找到合适的X值(小窗口给出的是红十字的X,Y值)4)双击红十字的位置,峰顶就会位移到此处:位移可以反复多次的进行,垂直方向的位移和水平方向的一样。
B、平滑1)如图选择:2)出现下面的小窗口3)点击settings出现下面的界面(如果想用平滑后的代替原始的,选择“replace original”,如果想重新做图选“add to worksheet”,下面的数值不用改变)4)点击operation,选择savizky-golay进行平滑。
得到下图:Origin处理XPS剖面分析数据1、用写字板打开ASC码文件,选取所需要的元素2、打开ORIGIN软件,如图示:选择column→add new columns如果你的数据有九个cycle那么你要在下面的窗口选择8。
然后在B(Y)….J(Y)中依次输入不同cycle的Y轴数值点击图中下方工具栏的waterfall然后在下图中先输入X轴起始值及步长,再将Y值输入(点击B (Y),然后按住SHIFT键不放,再点击最后一个Y值选项:如E (Y)),松开SHIFT 键,点击ADD 键。
点击OK得到下图:应用修改工具得:(X OFFSET 设为0,Y OFFSET 设为100)注意谱线对应的CYCLE数如果想要得到其中某一个cycle的谱图,只要调出原来的worksheet(数据表),再次点击waterfall。
胶原蛋白在电镀铜中的作用
胶原蛋白在电镀铜中的作用英文回答:Collagen has demonstrated promising potential in enhancing the properties of electroplated copper for various applications. Its unique properties provide several advantages, including:1. Enhanced Adhesion: Collagen's inherent biocompatibility and ability to adhere to various substrates make it an ideal material for improving the adhesion of electroplated copper. It acts as an intermediate layer between the substrate and the copper deposit, facilitating strong bonding and preventing delamination.2. Reduced Porosity: Collagen can fill surface imperfections and voids in the substrate, reducing the porosity of the electroplated copper. This results in a more uniform and dense deposit with improved corrosionresistance and mechanical properties.3. Improved Conductivity: Collagen is an electrically conductive material, which can enhance the electrical conductivity of the electroplated copper. This is particularly beneficial in applications where highelectrical conductivity is crucial, such as in electrodes and electronic devices.4. Biocompatibility and Corrosion Resistance: Collagen is a biocompatible material that exhibits excellent corrosion resistance. It can protect the underlying substrate from corrosive environments and prevent copper oxidation, extending the lifespan of the electroplated component.5. Flexibility and Flexibility: Collagen is a flexible material that can withstand bending and deformation without compromising its properties. This makes it suitable for applications where flexibility is required, such as in flexible electronics and wearable devices.中文回答:胶原蛋白在电镀铜中的作用。
origin of the solar system托福阅读
origin of the solar system托福阅读The origin of the solar system is a fascinating scientific topic that has intrigued researchers for many years. Through careful examination of various celestial bodies and the analysis of different data, scientists have developed several theories to explain how our solar system came into existence. In this essay, we will discuss the two prevailing theories regarding the origin of the solar system: the nebular theory and the capture theory.The first and most widely accepted theory is the nebular theory, which suggests that our solar system formed from a rotating cloud of gas and dust called the solar nebula. According to this theory, approximately 4.6 billion years ago, a nearby supernova or a passing star triggered a shock wave that caused the solar nebula to contract and begin the process of gravitational collapse.As the solar nebula collapsed, it began to spin faster due to the conservation of angular momentum. This spinning motion caused the material in the nebula to flatten into a disk shape, with most of the mass accumulating in the center. This central region eventually became the Sun.Within the disk, smaller clumps of material called protoplanetary disks began to form. These disks were composed of gas, dust, and other particles. Over time, the particles within these disks began to collide and stick together, forming planetesimals. These planetesimals continued to grow through collisions and mergers, eventually forming the planets, moons, and asteroids observed in our solar system today.While the nebular theory is widely accepted, there are still some unanswered questions and limitations to this explanation. One of the main unresolved issues is the formation of giant planets, such as Jupiter and Saturn. According to the nebular theory, these gas giants should not have had enough solid material in the solar nebula to form their massive cores. To address this, scientists propose the concept of "core accretion" where a solid core forms first and then rapidly gathers gas from the surrounding nebula.Another theory that has been proposed to explain the origin of the solar system is the capture theory. This theory suggests that the Sun captured pre-existing planets and other celestial bodies from another nearby star system. Under this scenario, the solar system's formation is believed to have occurred due to the gravitational interactions between the Sun and these wandering celestial bodies.Supporters of the capture theory argue that it can explain certain peculiarities observed in our solar system, such as the highly inclined orbits of some planets and the presence of a massive Kuiper belt. However, the capture theory has not gained as much widespread acceptance as the nebular theory due to the lack of evidence supporting the notion of planets being captured by the Sun.In conclusion, the origin of the solar system has been a subject of scientific inquiry for many years. The nebular theory, which suggests that our solar system formed from a rotating cloud of gas and dust called the solar nebula, is the most widely accepted explanation. The concept of the capture theory, which proposes that the Sun captured pre-existing celestial bodies, remains a lesssupported alternative. However, both theories continue to be studied and refined, as scientists strive to gain a deeper understanding of the fascinating origins of our solar system.。
GE磁共振简称
ACGD
Advanced Concept Gradient Driver
AGP
Applications Gateway Processor [Board]
AP
Array Processor Board
APM
Analog Power Monitor [Board]
APS
Auto prescan: Auto-adjustment of data acquisition (scan) parameters
OM
Oxygen Monitor
OW
Operator Workspace
PAC
Physiological Acquisition Controller
PCI
Peripheral Component Interconnect
PDU
Power Distribution Unit
PMC
PCI Mezzanine Connecter
MAGNETIC RESONANCE (MR)
The absorption or emission of electromagnetic energy by nuclei in a static magnetic field, after excitation by a suitable radio frequency field.
CV
Control variable
DCB
Driver Control Board
DEWAR
A container with an evacuated space between two highly reflective walls used to keep low temperature substances at nearconstant temperatures. Liquid helium is usually stored and shipped in dewars
origin计算赝电容
origin计算赝电容
(实用版)
目录
1.介绍赝电容的概念
2.阐述 origin 软件在计算赝电容中的应用
3.讨论 origin 软件计算赝电容的具体步骤
4.总结 origin 软件在计算赝电容中的优势和局限性
正文
赝电容是一种电化学现象,指的是在电极表面与电解质溶液之间形成的一种电容。
这种电容的存在使得电极在充放电过程中能够更加快速地响应,从而影响电池的性能。
Origin 软件是一款功能强大的科学绘图和数据分析软件,它能够帮助科研人员快速准确地计算赝电容,从而优化电池性能。
使用 Origin 软件计算赝电容的主要步骤如下:
首先,需要准备电池的充放电曲线数据。
这些数据可以从实验中获取,也可以从文献中找到。
Origin 软件可以读取多种格式的数据文件,如Excel、CSV 等。
其次,在 Origin 软件中选择合适的函数来计算赝电容。
Origin 软件提供了多种数学函数,如积分、微分等,可以根据具体情况选择合适的函数来计算赝电容。
然后,通过 Origin 软件的绘图功能,将计算得到的赝电容结果进行可视化。
这样可以更直观地观察赝电容的变化趋势,便于后续的分析和优化。
最后,Origin 软件可以方便地对计算结果进行统计分析,如计算均值、标准差等,从而更加准确地描述赝电容的特性。
总的来说,Origin 软件在计算赝电容方面具有操作简便、计算准确等优势,是科研人员进行电池性能优化的得力助手。
关于点翠的英语作文
Pointing Cuì,also known as Dian Cui in Chinese,is a traditional Chinese art form that involves the application of kingfisher feathers to create intricate and colorful designs. This technique has been practiced for centuries and is highly valued for its unique aesthetic appeal.Here is an essay about Pointing Cuìin English:Title:The Artistry of Pointing Cuì:A Glimpse into Chinas Timeless TraditionIntroduction:In the rich tapestry of Chinese culture,there exists a unique and exquisite art form known as Pointing Cuì.This ancient craft has captivated the hearts and minds of generations, showcasing the unparalleled skill and creativity of Chinese artisans.Pointing Cuìis not merely a decorative art it is a testament to the cultural heritage and artistic sensibilities of the Chinese people.Historical Significance:The practice of Pointing Cuìdates back to the Han Dynasty206BCE220CE,where it was initially used for adorning the headdresses of royals and nobles.Over time,this art form evolved and became popular among the upper echelons of society,who sought to display their wealth and status through these ornate accessories.The use of kingfisher feathers in Pointing Cuìis not arbitrary these vibrant and iridescent feathers possess a natural beauty that enhances the overall aesthetic of the artwork.Techniques and Materials:The process of creating Pointing Cuìis a meticulous and laborintensive endeavor. Artisans carefully select the finest kingfisher feathers,which are then meticulously arranged and glued onto a base material,such as metal,wood,or paper.The design is first sketched onto the base,and the feathers are cut and shaped to fit the desired pattern. The final product is a stunning display of color and form,with each feather contributing to the overall visual impact.Cultural Symbolism:Pointing Cuìis not only an art form but also a symbol of cultural identity and heritage. The use of kingfisher feathers,which are associated with good fortune and prosperity, imbues the artwork with a deeper meaning.Moreover,the intricate designs often incorporate elements from Chinese mythology,folklore,and nature,reflecting the rich cultural narrative of the Chinese people.Modern Adaptations:While Pointing Cuìhas its roots in ancient tradition,it has not remained static. Contemporary artists have adapted this art form to suit modern sensibilities,incorporatingit into various forms of wearable art,such as jewelry,hairpins,and even fashion accessories.This evolution has ensured the continued relevance of Pointing Cuìin the contemporary world,allowing it to reach a wider audience and inspire new generations of artists.Challenges and Controversies:Despite its beauty and cultural significance,Pointing Cuìhas faced criticism in recent years due to the use of kingfisher feathers.Concerns about the sustainability of the species and the ethical implications of using bird feathers for art have led to calls for more responsible practices.Some artists have responded by using alternative materials or by sourcing feathers from captivebred kingfishers,ensuring the preservation of this unique art form while minimizing its impact on the environment.Conclusion:Pointing Cuìis a testament to the ingenuity and artistic prowess of the Chinese people.It is a living tradition that continues to evolve and adapt,reflecting the changing times and cultural landscape.As we appreciate the beauty of Pointing Cuì,we must also recognize the importance of preserving both the art form and the natural world from which it draws inspiration.By doing so,we can ensure that this timeless craft continues to flourish and enchant future generations.。
关于介绍朝代的英语作文
When discussing the dynasties of China,one must begin with the earliest known,the Xia Dynasty,which is said to have ruled from around2070BCE to1600BCE.The Xia is often considered the first dynasty in Chinese history,although its existence is still debated among historians due to the lack of archaeological evidence.Following the Xia,the Shang Dynasty16001046BCE is better documented,with archaeological sites such as Yin,the last capital of the Shang,providing substantial evidence of its existence.The Shang Dynasty is known for its advanced bronze work and the development of the earliest form of Chinese writing,known as oracle bone script.The Zhou Dynasty1046256BCE is one of the longestlasting dynasties in Chinese history. It is divided into two periods:the Western Zhou1046771BCE and the Eastern Zhou 770256BCE.The Eastern Zhou is further divided into the Spring and Autumn Period 770476BCE and the Warring States Period475221BCE.The Zhou Dynasty saw significant cultural and philosophical developments,including the rise of Confucianism and Daoism.The Qin Dynasty221206BCE,though shortlived,was pivotal in Chinese history as it was the first to unify China under a centralized government.The first emperor,Qin Shi Huang,is known for his ambitious projects,such as the construction of the Great Wall of China and the Terracotta Army.The Han Dynasty206BCE220CE is considered a golden age in Chinese history, marked by significant advancements in science,technology,and culture.The Silk Road,a network of trade routes,was established during this time,facilitating cultural exchanges with the West.The Tang Dynasty618907CE is renowned for its cultural achievements,particularly in poetry,and for its relatively open and inclusive society.The Tang Dynasty saw the peak of Chinese influence in Asia.The Song Dynasty9601279CE is known for its technological innovations,including the invention of gunpowder,the compass,and advancements in printing technology.The Song period also saw the development of NeoConfucianism,a revival and reinterpretation of Confucian thought.The Yuan Dynasty12711368CE was established by the Mongols and marked the first time that China was ruled by a nonHan Chinese ethnic group.The Yuan Dynasty expanded Chinas territory to its largest extent and facilitated cultural exchanges with the West.The Ming Dynasty13681644CE is known for its strong centralized government and cultural achievements,including the construction of the Forbidden City in Beijing.The Ming Dynasty also saw the voyages of Zheng He,which extended Chinese influence into the Indian Ocean.The Qing Dynasty16441912CE was the last imperial dynasty of China.It was marked by territorial expansion and cultural integration of nonHan Chinese groups.However,the Qing Dynasty also faced internal strife and foreign aggression,which eventually led to the fall of the imperial system and the establishment of the Republic of China in1912. Each of these dynasties contributed to the rich tapestry of Chinese history,shaping the nations culture,politics,and society in unique ways.。
自旋熵
OFFPRINTThe spin-entropy enhancement induced by Cedoping in Ca3Co4O9+δG.D.Tang,X.N.Xu,C.P.Tang,Z.H.Wang,Y.He,L.Qiu,L.Y.Lv,L.Xing and Y.W.DuEPL,91(2010)17002Please visit the new websiteT ARGET YOUR RESEARCHWITH EPLSign up to receive the free EPL table ofcontents alert./alertsJuly2010 EPL,91(2010) doi:10.1209/0295-5075/91/17002The spin-entropy enhancement induced by Ce dopingin Ca3Co4O9+δG.D.Tang1,X.N.Xu1,C.P.Tang1,Z.H.Wang1(a),Y.He2,L.Qiu1,L.Y.Lv1,L.Xing3and Y.W.Du1 1National Laboratory of Solid State Microstructures and Physics Department of Nanjing UniversityNanjing210093,China2College of Physics and Technology,Guangxi Normal University-Guilin541004,China3College of Science,Zhongyuan University of Technology-Zhengzhou450007,Chinareceived9March2010;accepted infinal form16June2010published online16July2010PACS72.20.Pa–Thermoelectric and thermomagnetic effectsPACS72.80.Ga–Transition-metal compoundsAbstract–We present measurements of the thermopower as a function of temperature underdifferent magneticfields,for Ce-doped Ca3Co4O9+δ.A strong magnetic-field suppression of thethermopower indicates a large spin-entropy contribution.The magnetothermopower is enhancedin all doped samples,which provides an experimental evidence for the enhanced spin entropyby Ce doping.Our magnetic results allow us to determine the decrease in Co4+concentrationwhich results in the spin-entropy enhancement.We adopt a suitable theoretical model toexplain our experimental observations.This investigation gives strong evidence that the enhancedthermopower mainly originates from enhancement of the spin entropy.Copyright c EPLA,2010Thermoelectric(TE)materials have been the focus ofattention for their potential in saving energy resourcesand reducing CO2emissions[1].The performance of TEmaterials is determined by the dimensionless thermo-electricfigure of merit ZT=Q2Tσκ,where T,Q,κ,andσare the absolute temperature,the thermopower,the thermal conductivity and the electrical conductivity, respectively.Obviously,for a good TE material,a large thermopower,a low electrical resistivity and thermal conductivity are required.For the development of prac-tical TE materials,a large thermopower is especially important from the technological point of view.Since the discovery of a large thermopower combined with low resistivity in the layered cobalt oxide NaCo2O4[2],similar layered cobalt oxides[3–5]have been attracting more research attention.In this family,cobaltite Ca3Co4O9+δ, which exhibits an extraordinary large thermopower,has been considered to be a promising candidate for p-type TE materials[6,7].In the meantime,considerable theo-retical and experimental efforts[8–10]have been directed toward disclosing the source of the large thermopower in cobalt oxides.Several theoretical studies suggest that the spin entropy plays an important role in improving the thermopower in these materials[10,11].Several (a)E-mail:zhwang@ experimental activities have been launched in an effort to support the spin entropy theory[4,12–14].In particular, Wang et al.[12]found a suppression of the thermopower in the presence of a longitudinal magneticfield at low temperatures in NaCo2O4and proposed the spin entropy as the main source for the large thermopower observed in this system.The spin-entropy contribution to the thermopower is related with the spin-entropy current and the population of free spins[12],which depends largely on the Co4+concentration and the degeneracy of the Co ions[10].The doping of Ca sites can change the Co4+concentration[8,15].In this respect,under-standing the microscopic mechanisms by which doping affects the spin entropy can pave an effective way to improve the thermopower for TE materials.In addition, it has been discovered that doping with metals such as rare earths(Dy,Gd,Eu,La,Nd,Y),alkali metals or transition metals can enhance the thermopower of Ca3Co4O9+δsystem[3,15–17]while the origin of this enhancement is still under debate.Some people argued on the basis of theoretical considerations[15,16]that the doping-induced decrease in Co4+concentration may give rise to the enhancement of thermopower.But no further experimental results are put forward to support this argument in the Ca3Co4O9+δsystem.On the other hand,a conventional Boltzmann transport theory wasG.D.Tang et al.Table 1:Lattice parameters a ,b 1,b 2,c ,βand Ce atoms position for Ca 3−x Ce x Co 4O 9+δ(x =0,0.1,0.3and 0.5)samples.Here b 1and b 2are the b -axis length for [Ca 2CoO 3]and [CoO 2]subsystems,respectively.x ,y ,and z are coordinates of Ce in [Ca 2CoO 3].x a (˚A)b 1(˚A)b 2(˚A)c (˚A)β(◦)x y z 0.1 4.8448(7) 4.5328(5) 2.8205(1)10.8116(1)97.14(1)0.32560(1)00.72445(1)0.3 4.8405(3) 4.5318(1) 2.8216(2)10.8109(6)97.74(2)0.34535(7)00.70045(1)0.54.8388(1) 4.5307(8) 2.8247(4)10.8102(4)97.35(6)0.36640(4)0.68385(8)Fig.1:XRD patterns of Ca 3−x Ce x Co 4O 9+δ.considered to explain the enhanced thermopower,blurring the role of the electron structure [9,18].The substitution of the rare-earth metals leads to an increase in the thermopower and simultaneously a decrease in thermal conductivity [15–17].Furthermore,the uppermost rare-earth ion Ce 3+has the largest ionic radius,and therefore Ce doping in Ca 3Co 4O 9+δseems to be an interesting and potential way in further improving the thermoelectric properties.In this letter,we investigate both magnetothermopower and magnetic properties for Ce-doped Ca 3Co 4O 9+δsamples in order to disclose the effect of Ce doping on the spin entropy.We find that the thermopower is enhanced by Ce doping.Our magnetothermopower results show that Ce doping largely enhances the spin entropy in the Ca 3Co 4O 9+δsystem,implying that the enhanced thermopower originates mainly from a spin-entropy enhancement.This study suggests a new mechanism to improve the thermopower for TE materials.All Ca 3−x Ce x Co 4O 9+δsamples were prepared using a sol-gel method.High-purity powders CaCO 3,Co(NO 3)2,Ce(NO 3)3,and citric-acid monohydrate in stoichiometric ratio were dissolved in distilled water.The gel uniformity was rapidly gained at 353K and the moisture in the gel was removed at 473K for 2h.Then it was calcined at 823K for 3h in air.After cooling,the powders were ground and sintered at 1173K for 12h.The resulting ceramics were annealed at 1173K for 24h in a flow of oxygen gas.X-ray diffraction (XRD)measurement was performed on a Rigaku diffractometer with Cu Kαradiation.The magnetic properties were measured withaFig.2:(Colour on-line)Temperature dependence of the thermopower for Ca 3−x Ce x Co 4O 9+δ(x =0,0.1,0.3and 0.5)samples.Quantum Design superconducting quantum interference device (SQUID).Both thermopower and magnetothermo-power measurements were carried out by a Quantum Design physical property measurement system (PPMS).Figure 1shows the X-ray diffraction (XRD)patterns for different Ca 3−x Ce x Co 4O 9+δsamples.All peaks are identical to the standard JCPDS card (No.21-0139)of Ca 3Co 4O 9+δ,identifying a single-phase in these compounds.The refined lattice parameters and Ce atoms position for Ca 3−x Ce x Co 4O 9+δ(x =0,0.1,0.3and 0.5)samples are given in table 1.These results show that the Ce atoms enter into the [Ca 2CoO 3]subsystem and not the [CoO 2]subsystem.Figure 2shows the temperature dependence of the thermopower (Q )for Ca 3−x Ce x Co 4O 9+δ(x =0,0.1,0.3and 0.5)from 4K to 335K.The positive Q for all materials suggests the hole conduction nature of the electrical transport.It is found that the Q increases with increasing temperature and the Ce content.The maximum Q value reaches up to 126µV /K at 336K for the Ca 2.5Ce 0.5Co 4O 9+δsample.The spin entropy was proposed as the main source for the observed large thermopower in the cobalt oxides [12].To investigate the effect of Ce doping on the spin entropy and furthermore to clarify the origin of the enhanced ther-mopower,we performed a series of magnetothermopower measurements for the Ca 3−x Ce x Co 4O 9+δ(x =0,0.1,0.3and 0.5)samples at 4and 8T,respectively.In fig.3,we show the temperature dependence of the thermopower forThe spin-entropy enhancement induced by Ce doping in Ca 3Co 4O 9+δFig.3:(Colour on-line)Temperature dependence of the ther-mopower at 0,4and 8T for Ca 3−x Ce x Co 4O 9+δ(a)x =0,(b)x =0.1,(c)x =0.3,(d)x =0.5.Ca 3−x Ce x Co 4O 9+δsamples with x =0,0.1,0.3and 0.5at 0,4,and 8T,respectively.We can see a clear field-induced thermopower reduction in all of these samples.Such a field-suppression behavior is a typical signature of the spin-entropy reduction due to a partial removal of the spin degeneracy by an applied magnetic field [12,13].The strong magnetic field suppression confirms therefore a large spin-entropy contribution to the thermopower.A similar suppression behavior was also observed by Liu et al.[13,14]and attributed to the decrease of the spin entropy.As seen in fig.3,the thermopower is further suppressed as the applied field increases from 4T to 8T,indicating that the spin entropy is further reduced.In fact,if the applied magnetic field is strong enough to remove the spin degeneracy,the spin entropy will be completely suppressed and reduced to zero.In addition,we can see that the magnetothermopower effect becomes less observ-able at low temperature from fig.3.As the temperature decreases to low temperature,only a small fraction of the spins behaves as free spins due to the onset of magnetic coupling interaction.Therefore,the spin entropy decreases rapidly,in agreement with the observed steep decrease of the thermopower at low temperatures in fig.2.Only a small fraction of residual spin entropy gives rise to a less field-dependent thermopower [13,14].To give more evidence to our claims,we studied the relationship between magnetization (M )and applied magnetic field (H )at both 300K and 20K on these doped samples.As shown in fig.4,a linear increase of the magnetization with the magnetic field is observed.It confirms that the magnetic field can partially remove spin degeneracy even at room temperature.Basically,a considerable number of free spins is aligned with the strong field thus partially removing their degeneracy and hence the spin entropy is reduced remarkably,resulting in the observed large magnetothermopower.The M -H curves also evidence that the spin entropy is markedly suppressed by raising the magnetic field from 4to 8T.M -H curves at 20K are shown in the inset of fig.4.We find that they do not exhibit a hysteresis at this tempera-ture.The M -H curves deviate from a linear behaviorforFig.4:(Colour on-line)The relationship between magnetiza-tion M and magnetic field H for Ca 3−x Ce x Co 4O 9+δ(x =0,0.1,0.3and 0.5)at 300K.The inset shows the relationship at 20K.Fig.5:(Colour on-line)The magnetothermopower,Q (8T)−Q (0T),as a function of temperature for Ca 3−x Ce x Co 4O 9+δ(x =0,0.1,0.3and 0.5).all doped samples due to the onset of magnetic coupling at low paring with M -H curves at 300K,they all exhibit larger magnetization values due to the enhanced magnetic coupling at low temperatures.In order to further elucidate the effect of Ce doping on the spin entropy,we plot the magnetothermopower,[Q (8T)−Q (0T)],in fig.5.A large negative magnetother-mopower is obtained in the higher-temperature regime for all doped samples.The magnetothermopower at 300K is about −22,−26,−41and −39µV /K for x =0,0.1,0.3and 0.5samples,respectively.The magnetothermopower ratios,defined as [Q (8T)−Q (0T)]/Q (0T),are estimated to be about −25%for x =0,−27%for x =0.1,−37%for x =0.3,and −33%for x =0.5at room paring with the undoped Ca 3Co 4O 9+δsamples,we find that the absolute values of the magnetothermopower are enhanced in all doped samples.This clearly implies that Ce doping can enhance the spin entropy in the Ca 3Co 4O 9+δsystem.As shown in fig.4,the relation-ship between magnetization and Ce content at 300K has the same trend as that between manetothermopower and Ce content.The magnetization of the x =0.1sample is the smallest among these samples,which indicates thatG.D.Tang etal.Fig.6:(Colour on-line)Temperature dependence of the recip-rocal of the susceptibility for Ca3−x Ce x Co4O9+δ(x=0,0.1, 0.3and0.5)samples.The inset shows the Ce3d XPS spectra of Ca3−x Ce x Co4O9+δsample with x=0.3.the magneticfield will have a small impact on free spins in Ca2.9Ce0.1Co4O9+δ,thus only a small magnetother-mopower is observed.The magneticfield exerts a great influence on the spins in the x=0.3sample,resulting in the largest magnetothermopower.The combination of magnetothermopower and magnetic results provides an experimental evidence for a large doping-induced spin-entropy enhancement in our samples.This investigation also supports the conclusion that the enhanced thermo-power by Ce doping mainly originates from the increase of the spin entropy.To give some insight into the positive effect of Ce doping on the spin entropy,we measured the temper-ature dependence of the susceptibility(χ)in the pres-ence of0.2T appliedfield.The curves of the inverse susceptibility(1/χ)are presented infig.6.The magnetic behavior for Ca3−x Ce x Co4O9+δwith x=0.1,0.3and0.5 above100K corresponds to paramagnetism and obeys the Curie-Weiss law.The negative Weiss constant values indicate the presence of strong antiferromagnetic interac-tions at low temperatures.These samples do not exhibit a clear ferrimagnetic transition which was observed in Ca3Co4O9+δ[19],according to M-H results.Our results are consistent with the previous reports which suggested that the ferrimagnetic transition was suppressed by R (R represents Sr,Y,Bi)doping into Ca sites for a Ca3−x M x Co4O9+δsystem[19].As discussed in litera-ture[20],the ferrimagnetic transition in Ca3Co4O9+δis caused by the interlayer coupling between the[Ca2CoO3] and[CoO2]subsystems.XRD studies indicate that Ce enters into the[Ca2CoO3]subsystem.We presume that Ce doping weakens the magnetic coupling between the two subsystems.To give more evidence to this argument, we performed X-ray photoemission spectroscopy(XPS)to determine the valence state of Ce for these samples.The Ce3d XPS spectrum for Ca2.7Ce0.3Co4O9+δis presented in the inset offig.6.Peaks around886.3eV and882.6eV are observed,which reveal that Ce3+and Ce4+ions do coexist in this composition series.The weakmagnetic Fig.7:(Colour on-line)Temperature dependence of the effec-tive magnetic moment for Ca3−x Ce x Co4O9+δ(x=0,0.1,0.3 and0.5)samples.coupling is probably due to antiferromagnetic interactions between magnetic Ce3+and Co4+ions in the[Ca2CoO3] subsystem.Therefore,no ferrimagnetic transition is found down to5K in these doped Ca3−x Ce x Co4O9+δsamples. Because the spins are easily oriented with a magnetic field in the case of magnetic ordering,it is plausible that the magnetothermopower becomes less observable at low temperatures owing to the absence of ferrimag-netic ordering,in agreement with the observation infig.3. Infig.7,we show the temperature dependence of the effec-tive magnetic momentµeff.As the temperature decreases,µeff for all doped samples reduces gradually,because of the increase of antiferromagnetic interactions.However,µeff for Ca3Co4O9+δdecreases with decreasing temper-ature down to15K,then it increases again below15K. We ascribe the increase to the onset of ferrimagnetism.It is worth noting thatµeff for all doped samples is lower than that of Ca3Co4O9+δover the whole studied temper-ature range and decreases with increasing Ce doping level below25K.Previous X-ray absorption and X-ray photoe-mission spectroscopy studies of Ca3Co4O9+δshowed that Co4+and Co3+ions were in low-spin states t52g and t62g, respectively[20,21].Based on the studies of other substi-tuted layer cobalt oxides[22],one can assume that the substitution of Ce for Ca does not change the spin states of both the Co3+and Co4+ions.Therefore,we consider that the doping-induced reduction ofµeff is related with the decrease in Co4+(S=1/2,µeff=1.73µB)concentra-tion.We estimate the Co4+concentration according to the value ofµeff at40K for all samples by ignoring the Ce3+ contribution to theµeff because of the small number of magnetic Ce3+ions.The dependence of the Co4+concen-tration on x for these samples is given infig.8.The Co4+ concentration is found to be reduced by doping and has a minimum around x=0.3.From the standpoint of charge balance,the valence of the Co ions decreases with increas-ing Ce3+and Ce4+content to balance the total valence, in agreement with the decrease in Co4+concentration.In the high-temperature limit,the spin-entropy contri-bution to the thermopower can be expressed by theThe spin-entropy enhancement induced by Ce doping in Ca3Co4O9+δFig.8:Relationship between Co4+concentration and dopantcontent x for Ca3−x Ce x Co4O9+δ(x=0,0.1,0.3and0.5)samples.The inset presents the calculated spin entropy atdifferent Ce content.modified Heikes formula[10,11]:S=−k Beln g3g4 c1−c .(1)where g3and g4are the spin orbital degeneracies for the Co3+and Co4+ions,respectively,c is the Co4+ concentration,and k B is the Boltzmann constant.The spin orbital degeneracies g3=1and g4=6are determined according to the low-spin states of both Co3+and Co4+ ions[11].On the basis of eq.(1),we can calculate the total spin entropy at high-temperature limit based on the estimated Co4+concentration.The spin entropy at different Ce content is displayed in the inset offig.8.It can be seen that the spin entropy is enhanced by the Ce doping.In short,the results of both magnetothermopower and magnetic properties provide an experimental evidence that Ce doping increases the spin entropy of Ca3Co4O9+δsystem.Our results also indicate that the thermopower enhancement in these materials is directly related to the spin entropy.In summary,the thermopower as a function of temper-ature has been investigated on Ce-doped Ca3Co4O9+δunder0,4and8T,respectively.A dramaticfield-induced decrease in the thermopower indicates a large spin-entropy contribution.We found that the magnetothermopower is enhanced in all doped samples investigated.Our results indicate that the spin entropy is increased by the Ce doping.Magnetic measurements allow us to determine the decrease in the Co4+concentration which is respon-sible for the spin-entropy enhancement.We propose a suitable theoretical model to explain the spin-entropy enhancement.This investigation also demonstrates that the enhanced spin entropy directly increases the thermo-power.∗∗∗This work was supported by the MOST973Program of China(No.2009CB929501)and the State Key Program for Basic Research of China(Grant No.2010CB923403). REFERENCES[1]Snyder G.J.and Toberer E.S.,Nature,7(2008)105.[2]Terasaki I.,Sasago Y.and Toberer E.S.,Phys.Rev.B,56(1997)R12685.[3]Liu C.J.,Huang L.C.and Wang J.S.,Appl.Phys.Lett.,89(2006)204102.[4]Limelette P.,Hbert S.,Hardy V.,Frsard R.,SimonC.and Maignan A.,Phys.Rev.Lett.,97(2006)046601.[5]Luo X.G.,Chen X.H.,Wang G.Y.,Wang C.H.,Xiong Y.M.,Song H. B.and Lu X.X.,Europhys.Lett.,74(2006)526.[6]Shikano M.and Funahashi R.,Appl.Phys.Lett.,82(2003)1851.[7]Lin Y.H.,Lan J.L.,Shen Z.J.,Liu Y.H.,Nan C.W.and Li J.F.,Appl.Phys.Lett.,94(2009)072107. [8]Asahi R.,Sugiyama J.and Tani T.,Phys.Rev.B,66(2002)155103.[9]Takeuchi T.,Kondo T.,Takami T.,Takahashi H.,Ikuta H.,Mizutani U.,Soda K.,Funahashi R., Shikano M.,Mikami M.,Tsuda S.,Yokoya T.,Shin S.and Muro T.,Phys.Rev.B,69(2004)125401. [10]Koshibae W.,Tsutsui K.and Maekawa S.,Phys.Rev.B,62(2000)6869.[11]Koshibae W.and Maekawa S.,Phys.Rev.Lett.,87(2001)236603.[12]Wang Yayu,Rogado N.S.,Cava R.J.and Ong N.P.,Nature,423(2003)425.[13]Liu C.-J.,Sheu C.-S.,Wu T.-W.,Huang L.-C.,HsuF.H.,Yang H.D.,WilliamsG.V.M.and Liu Chia-Jung C.,Phys.Rev.B,71(2005)014502.[14]Liu C.-J.,Nayak P.K.and Williams G.V.M.,Appl.Phys.Lett.,91(2007)123110.[15]Liu H.Q.,Zhao X.B.,Liu F.,Song Y.,Sun Q.,ZhuT.J.and Wang F.P.,J.Mater.Sci.,43(2008)4933.[16]SWang D.L.,Chen L.D.,Yao Q.and Li J.G.,SolidState Commun.,129(2004)615.[17]Wang D.L.,Chen L.D.,Yao Q.and Li J.G.,J.AlloysCompd.,376(2004)58.[18]Pei J.,Chen G.,Lu D.Q.,Liu P.S.and Zhou N.,Solid State Commun.,146(2008)283.[19]Sugiyama J.,Itahara H.,Tani T.,Brewer J.H.andAnsaldo E.J.,Phys.Rev.B,66(2002)134413. 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英语介绍兵马俑作文初中
As a high school student with a deep interest in history, I am always fascinated by the stories and artifacts from the past. One of the most remarkable historical sites Ive had the chance to learn about is the Terracotta Army of China. This incredible archaeological discovery is not just a testament to the ancient Chinese civilizations craftsmanship and military prowess, but it also offers a unique glimpse into the life and afterlife beliefs of the first Emperor of China, Qin Shi Huang.The Terracotta Army was discovered in 1974 by local farmers in Xian, Shaanxi province, and it has since become one of the most famous attractions in China. What makes this find so extraordinary is the sheer scale and detail of the figures. The army consists of thousands of lifesized terracotta soldiers, each with distinct facial features, hairstyles, and armor, standing in battle formation, ready to protect their emperor in the afterlife.When I first learned about the Terracotta Army, I was captivated by the idea that these figures were created over 2,000 years ago. The level of detail is so precise that each soldier has unique expressions, and its said that there are no two identical faces among the thousands. This level of individuality is astounding, especially considering the time period in which they were made.The craftsmanship of the Terracotta Army is a reflection of the Qin dynastys technological and artistic achievements. The figures were made using a combination of molding and sculpting techniques, and the armor, weapons, and other accessories were meticulously crafted to reflect the actual military equipment of the time. The discovery of the TerracottaArmy has not only provided historians with invaluable information about the Qin dynastys military and social structure but also about the artistic and cultural practices of the era.One of the most intriguing aspects of the Terracotta Army is the mystery surrounding its creation. It is believed that the construction of the tomb, which includes the Terracotta Army, began in 246 BCE and continued until the emperors death in 210 BCE. The sheer scale of the project required the labor of thousands of workers and artists, and its thought that many of them were buried alive with the emperor to ensure the secrecy of the tombs location.Visiting the Terracotta Army is an experience that I would recommend to anyone interested in history or archaeology. The site is massive, with three main pits housing the majority of the figures, and several smaller pits containing additional artifacts. Walking through the pits, seeing the rows of soldiers stretching out before you, is a humbling experience. Its hard not to feel a sense of awe and respect for the people who created these figures and the civilization that produced them.Moreover, the Terracotta Army has sparked numerous debates and research projects. Scholars continue to study the figures for clues about the Qin dynastys society, military strategies, and even the emperors personal life. The discovery has also led to advancements in archaeological techniques, as researchers work to preserve and restore the figures, many of which were damaged or destroyed by time and environmental factors.In conclusion, the Terracotta Army is more than just a collection of ancient statues its a window into the past that continues to inspire and educate people around the world. As a high school student, learning about the Terracotta Army has deepened my appreciation for history and the stories that artifacts can tell. Its a reminder of the enduring legacy of ancient civilizations and the importance of preserving and studying our shared cultural heritage.。
EPIC 矩形孔打磨器件 连接器配件 矩形孔打磨器件 为面板基板和SKINTOP 立方体用说明书
EPIC rectangular hole punches provide a quick, accurate means ofcutting clearance holes for mounting HB Series rectangular panelmount bases and SKINTOP Cube multi-cable bushing systems, without sawing or filing. The dies include four drill guide holes for thebase’s screw mounting holes. Centering alignment marks are also in-cluded for easy squaring of the die with the panel cabinet. The unique2-piece die configuration simplifies scrap slug removal. The EPIC hole punches can be used with mild steel up to 14 gauge(2.0mm) thickness or aluminum up to 10 guage (2.54mm). These punches are intended for manual use with a ratchet or other suitablewrench or with a hand or foot operated hydraulic driver and ram using a 3/4” draw stud.Cutout Dimensions3/4” x 7” Draw Stud Set Part Number 61U00197Set includes: draw stud, drive nut, counternut, ball bearing, and spacer Punch and Die Sets SizePart Number Max. Panel Thickness HB661U00199Mild Steel 14GA (2.0mm)Aluminum 10GA (2.54mm)HB1061U00200HB1661U00201HB2461U002033/4” x 7” Draw Stud Only Part Number 61U00198For Manual Operation Order the Draw Stud Set and required size Punch & Die Set For Hydraulic Operation Order the required size Punch & Die Set, and if needed, the 3/4” Draw StudManual (wrench) OperationStep 1Determine the location for the cutout on your panel and drill a 1-1/8” diameter pilot hole in the center of the desired opening. Step 2Assemble the punch unit as shown in figure 1, by threading the Counter Nut onto the short threaded end of the Draw Stud. Then pass the Draw Stud through the Punch and then the pilot hole in the panel. On the other side of the panel, slide the Die over the Draw Stud (black portion up against the panel). Then add the Spacer and Ball Bearing, and thread on the Drive Nut. Using the alignment marks to square the die with the panel, firmly hand tighten the Drive Nut until all components are tightly secured as shown in figure 2.Step 3Using an 11/64”, size 18, or 4.3mm drill bit, drill out the four mounting screw holes. Using a 1-1/4” hex ratchet, or other suitable wrench, tighten the Drive Nut. This will draw the Punch through the panel and into the Die, completing the punch-ing operation (figure 3).Step 4Remove and disassemble the punch unit. The black and silver parts of the Die can be slid apart slightly to allow the panel slug to be easily removed and discarded.Figure 1Figure 2Figure 3Hydraulic OperationStep 1Determine the location for the cutout on your panel and drill a 1-1/8” diameter pilot hole in the center of the desired opening. Step 2Assemble the punch unit as shown in figure 4, by threading the short threaded end of the Draw Stud into the Hydraulic Ram. Then pass the Draw Stud through the Die (black portion up against the panel) and then the pilot hole in the panel. On the other side of the panel, slide the Punch over the Draw Stud and screw on the Counter Nut. Using the alignment marks to square the die with the panel, firmly hand tighten the Counter Nut until all components are tightly secured as shown in figure 5.Step 3Using an 11/64”, size 18, or 4.3mm drill bit, drill out the four mounting screw holes. Operate the hydraulic drive (not shown). This will pull the Draw Stud into the Hydraulic Ram, and the Punch through the panel and into the Die, complet-ing the punching operation (figure 6).Step 4Remove and disassemble the punch unit. The black and silver parts of the Die can be slid apart slightly to allow the panel slug to be easily removed and discarded.Figure 4Figure 5Figure 6。
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a r X i v :c o n d -m a t /0201244v 1 [c o n d -m a t .s t r -e l ] 15 J a n 2002Origin for the enhanced copper spin echo decay rate in the pseudogap regimeof the multilayer high-T c cupratesAtsushi Goto 1,2,W.G.Clark 1,Patrik Vonlanthen 1,Kenji B.Tanaka 1,Tadashi Shimizu 2,Kenjiro Hashi 2,P.V.P.S.S.Sastry 3,4,and Justin Schwartz 3,41Department of Physics and Astronomy,University of California,Los Angeles,CA,90095-15472National Institute for Materials Science,3-13,Sakura,Tsukuba,Ibaraki,305-0003,Japan 3National High Magnetic Field Laboratory,1800E.Paul Dirac Drive,Tallahassee,Florida 32310and 4Department of Mechanical Engineering,FAMU-FSU College of Engineering,Tallahassee,Florida 32306(Dated:February 1,2008)We report measurements of the anisotropy of the spin echo decay for the inner layer Cu site of the triple layer cuprate,Hg 0.8Re 0.2Ba 2Ca 2Cu 3O 8(T c =126K)in the pseudogap T regime below T pg ∼170K and the corresponding analysis for their interpretation.As the field alignment is varied,the shape of the decay curve changes from Gaussian (H 0 c)to single exponential (H 0⊥c).The latter characterizes the decay caused by the fluctuations of adjacent Cu nuclear spins caused by theirinteractions with electron spins.The angular dependence of the second moment (T −22M ≡<∆ω2>)deduced from the decay curves indicates that T −22M for H 0 c,which is identical to T −22G (T 2G is the Gaussian component),is substantially enhanced,as seen in the pseudogap regime of the bilayerparison of T −22M between H 0 c and H 0⊥c indicates that this enhancement is caused by electron spin correlations between the inner and the outer CuO 2layers.These results provide the answer to the long-standing controversy regarding the opposite T dependences of (T 1T )−1and T −22G in the pseudogap regime of bi-and trilayer systems.PACS numbers:74.72.Gr,74.25.Ha,76.60.-kThe pseudogap phenomenon has been one of the cen-tral issues in understanding the anomalous normal statesof high-T c cuprates.Since the discovery of the pseudogap [1],NMR has continued to be a basic tool for its inves-tigation.Temperature and doping dependences of the spin-lattice relaxation times (T 1)and the Knight shifts (K s )of the Cu sites have served as crucial tests for the theories describing the pseudogap.A controversy,how-ever,has arisen on the interpretation of the Gaussian component of a spin-spin relaxation time (T 2G ).In sys-tems such as YBa 2Cu 3O 6.6and YBa 2Cu 4O 8,T −22G contin-ues to grow as T is lowered towards T c ,whereas (T 1T )−1decreases in the pseudogap regime [2,3].If the same dynamical susceptibility χ(q ,ω)is responsible for both relaxation rates,an anomalous enhancement is expected at the high frequency part of Im χ(q ,ω)in the pseudo-gap regime.This rather peculiar conclusion has puzzled theorists,and other explanations have been sought.A key to resolve the problem is that the phenomenon is observed only in multilayer systems.One proposed mechanism is spin correlations between adjacent layers [4,5,6],which had been observed in spin echo double resonance (SEDOR)experiments [7,8,9].They are ex-pected to play essential roles in the systematic increase of T c with increasing the number of layers because they can provide attractive forces between layers and stabi-lize the superconductivity [10].In the bilayer systems,the two CuO 2layers in a unit cell are equivalent,so that the Cu nuclei on one of the layers behave as like-spins to the others in the echo decay process,and contributeto T −22G through the interlayer spin correlations.Unfortu-nately,since the contribution from the interlayer couping is indistinguishable from its intralayer counterpart for the identical layers,it is difficult to extract the effect exper-imentally in such systems.In order to identify experimentally the interlayer ef-fects on T 2G ,we have utilized the trilayer cuprate Hg 0.8Re 0.2Ba 2Ca 2Cu 3O 8(T c =126K)with a pseudo-gap (T pg ∼170K),where one inner and two outer CuO 2layers are crystallographically inequivalent.This enables us to separate the interlayer effects from the total decay rates.In this letter,we report the measurements of the angular dependence of the second moment in the inner Cu site,which identifies the role of interlayer correlations in the echo decay process in the pseudogap regime of a multilayer system.Our analysis of the results shows thatthe different behavior of (T 1T )−1and T −22G is caused by interlayer spin correlations.The powder sample was prepared using the method of Ref.11and magnetically oriented along the c-axis.Figure 1shows the angular dependence of the frequency spectrum for the 63Cu central transition at 135K.The angle θis that between H 0and the c-axis.Each curve was obtained by adding the real part of the FT spec-tra of the half echo measured at a few different frequen-cies [12].The relatively narrow and wide lines are as-signed to Cu(1)and Cu(2)sites in the inner and outer layers,respectively [13].We confirmed that K s and the quadrupole frequency (νQ )are consistent with previous results [14,15].The triangles in Fig.1indicate the po-sitions at which echo decays were measured.Since the Cu(1)and Cu(2)lines overlap at 10◦and 70o ,both lines contribute to the measured decay.The angular dependence of the echo decay curves at 135K is shown in Fig.2(a),where the Redfield contribu-tion from T 1has been removed by dividing the measured263Cu of (b)T −22M(T 1R )z ={I (I +1)−1/4}(W x +W y )+W z ,(1)where W γ(γ=x,y,z)is from the spin fluctuations in the γdirection and z is the quantization axis ( H 0).In thesame notation,(T 1)−1z is given by (T 1)−1z =W x +W y .Hence,for an arbitrary θ,[T 1R (θ)]−1={I (I +1)−1/4}[T 1(θ)]−1+[T 1(90◦−θ)]−1−0.5[T 1(0◦)]−1,(2)where the relation W a =W b is used (The subscripts a,b correspond to the crystalline axes).From the anisotropy of (T 1T )−1in Fig.2(b),[T 1R (θ)]−1is calculated.Figure 2(a)shows that the shape of the decay curve changes from Gaussian at 0◦to single exponential(Lorentzian spectrum)at 90◦.These data are fitted by the function,M (2τ)T 2L −1T 2G 2(3)with M 0,T 2L and T 2G as free parameters.The angulardependences of T −12L and T −12G thus obtained are shown inFig.2(c).For 0◦∼20◦,T −12L is nearly zero while T −12G iszero at 80o and 90o.In between,the decay curve crosses over between these two extremes.This change is a result of the NMR line narrowing caused by the following mech-anism.At finite T the effective interaction between ad-jacent nuclear spins is reduced because of rapid spin flips driven by the hyperfine interaction with the electrons,which averages out the nuclear fields at adjacent nuclear sites.As a result,the central part of the NMR line is nar-rowed and the spectrum approaches a Lorentzian rather than a Gaussian shape [17,18].The importance of the ef-fect depends on the ratio between the two time scales T 1and T 2M ≡ ∆ω2 −1/2,where ∆ω2 is the homogeneous second moment of the NMR absorption.The former and the latter characterize the time scales of the nuclear spin fluctuations and the echo decays,respectively.There are two limiting cases where analytical forms for the decays are known.One is the static limit (T 1/T 2M ≫1),where nuclear spins do not change their states be-tween pulses or a pulse and an echo because of the rel-atively long T 1.Consequently,the contributions from unlike-spins are canceled out at the time of the echo and only like-spins contribute to the echo decay.The decay in this case is described by a Gaussian [2],M (2τ)2 2τe −2τ/T 1R=M 0exp −2τ63T 165T 2M2,(5)where αT −22M ≡α ∆ω2 is the contribution from the α-nuclei (α=63,65)to the second moment of 63Cu,and αT 1is the spin-lattice relaxation time in the α-site.Note that 63T 2M corresponds to T 2G in the static limit.Here,65Cu also contributes to the 63Cu decay because they lose their memories of the initial states during the echo sequence due to the fluctuation effect,so that their contributions are not canceled out at the time of the 63Cu echo.In the present case,the transition from the static to the narrowing regime is caused by the large anisotropiesof T −11and T −12M .As will be shown later,T −12M decreases3by3.3fromθ=0◦to90◦,while T−11increases by2.1.Also,there is a qualitativecorrespondence between thetransition of the decay curve in Fig.2(a)and the simula-tions by Walstedt et al.for the various values of T1/T2M(Fig.4of Ref17).The angular dependence of T−22M de-duced from either T2G or T2L in Fig.2(c)is shown in Fig.2(d),where T2M=T2G while Eq.(5)is used to obtain63T2M from T2L along with the relations,(63γ)2·63T1=(65γ)2·65T1,(6) 65c·(65γn·65T2M)2=63c·(63γn·63T2M)2,(7) whereαc is the natural abundance for the isotopeα.The angular dependence of T−22M in Fig.2(d)is con-sistent with that of the hyperfine coupling constant.In the detuned limit,theflip-flop term(I+i I−j)in the nu-clear Hamiltonian is ineffective because of the mismatch in the Zeeman energies between adjacent nuclei.Hence, T−22Mis given only by the z-component term(I z i I z j),so that[T2M(θ)]−2∝{χ(Q)}2· q{F q(θ)}2,where F q(θ) is the form factor when H0is in theθdirection[3]. Here,we assume that the q-dependence ofχ(q)around Q≡(π,π)is weaker than that of F q,so thatχ(q)is represented byχ(Q)and taken out of the q-summation. We further assume that q{F q(θ)}2is proportional to {F Q(θ)}2at eachθ.Since theθdependence of F Q(θ)is {A(3cos2θ−1)+B}2where A and B are constants,theanisotropy of T−22Mis given by[T2M(θ)]−2/[T2M(90o)]−2=(sin2θ+ξcos2θ)4,(8) whereξ≡ q{F q(0◦)}2F Q(90◦) 1/2.(9) The value ofξcan be estimated from the anisotropyof T−11.Sinceχ(Q)≫χ(0)in this system,(T1)−1z∝{F x(Q)+F y(Q)}[14].Hence,ξis given by,ξ≈ F Q(0◦)(T1(0◦))−1−1 1/2.(10)From Fig.2(b),(T1(90◦))−1/(T1(0◦)−1= 2.1,so thatξ=1.79.The dashed curve in Fig.2(d)showsthe anisotropy of T−22M obtained from Eq.(8)with[T2M(90◦)]−2as a single adjustable parameter.It hasthe same tendency as the angular dependence of T−22G inspite of some assumptions.The analysis at0◦,10◦and70◦is not straightforward because of the overlap with the Cu(2)line.Since T−12M at Cu(2)is expected to be smaller than that of Cu(1)by a factor of0.75[14],the overlapped Cu(2)line reducesT−1 2M .T−22M,however,is not reduced at10◦,and is signif-icantly enhanced at0◦.At70◦,the shape of the decay curve itself is quite different from those at60◦and80◦. Below,we show that these features can be attributed to the interlayer spin correlations,which have the effect ofenhancing T−12M [4,6].FIG.3:Schematic view of the intra(i=j)and interlayer(i=j)spin susceptibilities(χij(q))in the trilayer system.Consider the echo decay process atθ=0◦.As seenin Fig.1,the Cu(1)and Cu(2)lines are situated closeto each other,so that not only Cu(1)but also a partof Cu(2)nuclei are excited,which also act as like-spinsfor the Cu(1)nuclei in the echo decay process.On theother hand,the intensity of the echo is obtained by in-tegrating only the Cu(1)part of the FT spectrum of theecho(shaded part of the spectrum in Fig.1),so thatonly the Cu(1)nuclei contribute to the intensity of thedecay curve in Fig.2(a).This is the same situation asthat in the SEDOR experiment where theπ-pulses forlike-and unlike-spins are applied simultaneously.Sinceall the like-spins contribute to the Gaussian decay in thestatic limit,[T2M(0◦)]−2is given by[6],[T2M(0◦)]−2∝ q[F q(0◦){χ11(q)+4ǫχ12(q)}]2,(11)where,χ11andχ12are the intra-and interlayer spinsusceptibilities associated with the auto-and cross-correlations within or between layers indicated in Fig.3.The second term in Eq.(11)corresponds to the con-tribution due to the interlayer correlations.The ratio ofthe excited Cu(2)nuclei(ǫ)is estimated to be about0.6.At the angles where the two Cu lines are separatedfrom each other,the second term in Eq.(11)does notappear in the echo decay process,whereas at10◦and70◦,both the Cu(1)and Cu(2)nuclei are excited andobserved,so that the second term in Eq.(11)also ap-pears,which enhances T−22M.This enhancement increasesT1/T2M,and brings the situation at70◦closer to thestatic limit,resulting in the appearance of the Gaussiancomponent in the decay curve.At10◦,a cancelation mayoccur between the reduction due to the overlapped Cu(2)line and the enhancement due to the interlayer spin cor-relations.Figure4(b)shows the T dependences of T−22Mat0o and90◦,which are quite different from each other;i.e.,while[T2M(90◦)]−2starts to decrease at T pg as does(T1T)−1shown in Fig.4(a),[T2M(0◦)]−2continues to grow downto T c.This difference is caused by theχ12term in Eq.(11).Provided again that the q-dependences ofχij(q)around Q are weaker than that of F q,T−22Mat0◦and90◦4◦and◦)}2,(12)ρ≡[T2M(0◦)]−2χ11(Q) 2,(13)which gives,χ12(Q)/χ11(Q)=(√。