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diffusion of
相关语句
  扩散
    Rheological Behavior and Atomic Diffusion of Pd-based and Zr-based Bulk Metallic Glasses
    Pd基Zr基大块金属玻璃的流变及原子扩散行为研究
短句来源
    DIFFUSION OF HYDROGEN IN Ta
    氢在Ta中的扩散
短句来源
    The Diffusion of Hydrogen in Metal Glass Fe_(39)Ni_(39)Si_8B_(12)Mn_2 and the Effect of Hydrogen on its Young's Modulus
    氢在金属玻璃Fe_(39)Ni_(39)Si_8B_(12)Mn_2中的扩散及其对弹性模量的影响
短句来源
    ISOTHERMAL DILATATION AND OXYGEN DIFFUSION OF Ba_2YCu_3O_(7-δ) WITH TETRAGONAL STRUCTURE
    四方结构Ba_2YCu_3O_(7-δ)的等温膨胀与氧扩散
短句来源
    DIFFUSION OF HYDROGEN IN (α+γ) DUPLEX STAINLESS STEEL
    氢在(α+γ)双相不锈钢中的扩散
短句来源
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  中扩散
    During mechanical alloying of the powder,the supersaturated solid solution of Al,Ti,B in Fe,Fe(Al,Ti,B),is formed by the diffusion of the Al,Ti,B atoms into the Fe lattice.
    研究表明,Fe-Al-Ti-B四元粉体的机械合金化通过Al、Ti、B原子向Fe晶格中扩散形成Fe(Al,Ti,B)过饱和固溶体。
短句来源
    The heat treatment experiments of carbon fiber with Ta powder at 2300'C prove that TaC was formed by diffusion of C into Ta.
    炭纤维和Ta粉2300℃热处理实验表明,由于发生了C向Ta中扩散而生成TaC。
短句来源
    Examination of the microprobe photographs and of the scans clearly indicates that diffusion of Re into Ir coating predominates with little diffusion of Ir into the Re.
    通过显微探针图和线扫描分析表明,工r/Re复合材料中的扩散基本上是一个单向扩散过程,即大量的Re元素向Ir涂层中扩散,而Ir元素向Re基体中的扩散却很少;
短句来源
    It was indicated that the rate of Mg evaporation is simultaneously controlled by the diffusion of Mg through the liquid boundary layer and by the evaporation of Mg at the metal pool/atmosphere interface, rather than its diffusion through the gas boundary layer, when the furnace Ar pressure kept under 100—400 mmHg.
    结果表明,真空感应熔炼过程中,当炉内Ar压力保持在100—400mmHg时,合金中Mg挥发速率受Mg在液相边界层中扩散及金属熔池/气相界面挥发反应双重控制,而非受控于气相边界层中Mg的扩散。
短句来源
    During the process of the transformation from mixture to amor- phous,there is diffusion of Al into the lattice of Ti.
    在混合物向非晶的转变过程中,Al 原子向 Ti 的晶格中扩散
短句来源
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  扩散规律
    The diffusion of rhenium in iridium coating of the iridium/rhenium composite was studied by wave disperse spectrum of SEM.
    应用电子扫描波谱法探针研究了Ir/Re复合材料界面Re元素在Ir涂层中的扩散规律
短句来源
  “diffusion of”译为未确定词的双语例句
    The oxidation resistance of C/SiC was improved greatly bymulti-deposition of SiC coating. However, the oxidation of C/SiC-SiC was controlledby diffusion of oxygen through coating microcracks and coating gap, which led to theweight losses of C/SiC-SiC in all range of temperature.
    通过沉积三次SiC涂层显著提高了C/SiC的抗氧化性能,但是涂层微裂纹和涂层间隙缺陷对C/SiC-SiC的氧化行为起着控制作用,这导致C/SiC-SiC在全温度范围内表现为氧化失重;
短句来源
    The possible ranking order of these phases in radial direction from the core of WC to the Co is like this: WC-*W2C-*CoxWyCz(Co3W9C4> C03W3C) -? CoaC-^Co. With the diffusion of C to the outside, the W:C atomic ratios increase.
    4)喷涂粒子高速撞击基体并迅速冷却,涂层中除了WC相外,还有Co_xW_yC_z(Co_3W_9C_4、Co_3W_3C)、Co_3C、W_2C、W及非晶的出现。
短句来源
    Mutual diffusion of Nd and Fe atoms results in better homogeneity of HDDR-processed powders of Nd-Fe-B alloy with high-Nd,which has great effect on themicrostructures and properties of HDDR-processed Nd-Fe-B powders。
    对于高Nd含量的Nd-Fe-B合金,处理过程中Nd与Fe的相互扩散是HDDR法处理的Nd-Fe-B粉末成分变得均匀、磁性能得以改善的基本原因.
短句来源
    The miniaturization caused the XRD peak of silver disappear based on the theory of Lewis-Campbell, the increase of activation energy for surface diffusion of the substrate was estimated to be 0.058 eV, and the increase of adsorption energy was estimated to be 0.08~0.42 eV.
    由Lewis -Campbell理论分析估算得到 ,镧的引入使基底表面徙动激活能增加约 0 0 5 8eV ,相应的基底原子吸附能增加约 0 0 8~ 0 42eV。
短句来源
    Otherwise, a complex strong binding force accompanied by elemental diffusion of Si and Ti in HA-BG-Ti ternary composites could theoritically explain the great difference of mechanical properties between HA-BG-Ti ternary composites and HA-Ti binary composites.
    物相分析和微观结构分析表明 :HA BG Ti复合陶材料中的HA Ti相间界面依靠生物玻璃以复杂的强键相结合 ,是HA BG Ti系复合材料的力学性能优于HA Ti二元系复合材料力学性能的原因。
短句来源
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  diffusion of
One DR peak associated with the short-distance diffusion of oxygen vacancies was observed in both temperature and frequency spectra.
      
The method of NMR spin echo with the magnetic field pulse gradient was used for studying self-diffusion of water molecules in the radial root direction.
      
Diffusion of an Organic Cation into Root Cell Walls
      
Nonspecific pore-forming proteins (porins) are the major proteins of the outer membrane of Gram-negative bacteria responsible for diffusion of low-molecular-weight compounds.
      
Furthermore, these inhibitors not only reduce the local tissue damage but also retard the easy diffusion of systemic toxins and hence increase survival time.
      
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Internal friction in several molybdenum-titanium alloys containing oxygen was measured. Besides the 110℃ peak associated with the diffusion of oxygen between Mo-Mo interstitial sites, another peak around 55℃ was observed which was shown to be associated with the stress-induced micro-diffusion of oxygen between Mo-Ti interstitial sites. The activation energy for the latter process was found to be 22600 cal/g-atom. The condition for the appearance of the 55℃ peak is the presence of both titanium and...

Internal friction in several molybdenum-titanium alloys containing oxygen was measured. Besides the 110℃ peak associated with the diffusion of oxygen between Mo-Mo interstitial sites, another peak around 55℃ was observed which was shown to be associated with the stress-induced micro-diffusion of oxygen between Mo-Ti interstitial sites. The activation energy for the latter process was found to be 22600 cal/g-atom. The condition for the appearance of the 55℃ peak is the presence of both titanium and oxygen in molybdenum.The partition functions and the potential energy difference of oxygen atoms in the two interstitial sites were calculated by means of a standard statistical method. Furthermore, it was shown that titanium would enlarge the solubility of oxygen in molybdenum, thus lowering the ductile-brittle transition temperature of molybdenum-titanium alloys.

研究了含氧的几种Mo-Ti合金的内耗,观察到除了氧在Mo-Mo间隙位置扩散所引起的110℃内耗峯外,还有一个由于氧在Mo-Ti间隙位置扩散所引起的55℃内耗峯,后一过程所包含的激活能为22,600卡/克原子。用统计方法计算了氧原子在这两种间隙位置的配分函数及位能差。此外,还指出钛会扩大氧在钼中的溶解度,因而降低Mo-Ti合金的脆性转变温度。

The kinetics of hydrogen absorption in LaNi_5 has been investigated at initialpressures of 15--30 atm and temperatures in the range of 20--85℃. LaNi_5 was pre-pared in a ZrO_2 crucible in a graphite-tube furnace under vacuum. It is shownthat a linear relationship exists between the amount of hydrogen absorbed, W,and the time of reaction on a logarithmic scale and the rate of hydrogen absorp-tion depends on the initial pressure and the test temperature. The P-X-T curves of the LaNi_5 system have been determined....

The kinetics of hydrogen absorption in LaNi_5 has been investigated at initialpressures of 15--30 atm and temperatures in the range of 20--85℃. LaNi_5 was pre-pared in a ZrO_2 crucible in a graphite-tube furnace under vacuum. It is shownthat a linear relationship exists between the amount of hydrogen absorbed, W,and the time of reaction on a logarithmic scale and the rate of hydrogen absorp-tion depends on the initial pressure and the test temperature. The P-X-T curves of the LaNi_5 system have been determined. For each testtemperature there is a corresponding pressure plateau P_0 and it is therefore as-sumed that for every initial pressure P_0 there is a corresponding balance temperatureT_0, and T_0-T may be taken as the driving force of hydrogen absorption processin LaNi_5 at initial pressure P_0 and test temperature T. The absorption of hydro-gen takes place in three steps: (1) surface reaction, which seems to be rather com-plicated; (2) diffusion of hydrogen atoms and (3) phase transformation f LaNi_5 toa hydride phase. All these steps are thermal activation processes, and thereforethe e~(-U/RT) can be introduce in the hydrogen absorption process. The relatioshipbetween the absorption rate, the initial pressure, the test temperature and time isgiven as follow: dW/dt=A_0(T_0-T)e~(-U/RT)·1/tThe activation energy of the rate limiting step U is about 2 or 3.2 kcal/molaccording to whether the amount of hydrogen absorbed is less or more than 70%respectively. The parameter U of the rate-limiting step during hydrogen absorptionin LaNi_5 can be obtained as shown by our experiments.

在初始压力15—30atm、温度20—85℃的范围内研究了储氢材料LaNi_5在恒温时吸氢的动力学过程.实验结果表明:吸氢量与时间的对数呈线性关系;吸氢速率随初始压力的提高或吸氢温度的升高而改变.提出了表示吸氢速率对时间、初始压力、吸氢温度依赖性的关系式,实验结果与之一致.按这一关系式可以得到吸氢速率的限制性环节的激活能U.在吸氢量(以饱和度计)约70%以前,U约为2.0 kcal/mol H_2,吸氢量更高时约3.2 kcal/mol H_2.这些数据为进一步确定吸氢速率的限制性环节提供了重要参数.

The kinetics of Mg evaporation of a Ni-base superalloy, Ni-10Cr-15Co-6W-6Mo-4Al-2Ti, during VIM has been studied. It was indicated that the rate of Mg evaporation is simultaneously controlled by the diffusion of Mg through the liquid boundary layer and by the evaporation of Mg at the metal pool/atmosphere interface, rather than its diffusion through the gas boundary layer, when the furnace Ar pressure kept under 100—400 mmHg. The transfer coefficient of Mg evaporation K_(23) is 10~(-1)—10~(-2) cm....

The kinetics of Mg evaporation of a Ni-base superalloy, Ni-10Cr-15Co-6W-6Mo-4Al-2Ti, during VIM has been studied. It was indicated that the rate of Mg evaporation is simultaneously controlled by the diffusion of Mg through the liquid boundary layer and by the evaporation of Mg at the metal pool/atmosphere interface, rather than its diffusion through the gas boundary layer, when the furnace Ar pressure kept under 100—400 mmHg. The transfer coefficient of Mg evaporation K_(23) is 10~(-1)—10~(-2) cm. s~(-1) and K_4 is about 140cm. s~(-1). A simple mathematical model for Mg evaporation during VIM was proposed. This model provided that the predicted Mg contents are in excellent agreement with those analyzed in the experimental and industrial alloys. Thus, it is possible that the optimum Mg content may be accurately controlled by certain smelting parameters, such as, the amount of Mg added into the metal pool, the Ar pressure, the temperature and time of evaporation, etc.

研究了Ni基高温合金Ni-10Cr-15Co-6W-6Mo-4Al-2Ti真空熔炼过程中Mg挥发动力学。结果表明,真空感应熔炼过程中,当炉内Ar压力保持在100—400mmHg时,合金中Mg挥发速率受Mg在液相边界层中扩散及金属熔池/气相界面挥发反应双重控制,而非受控于气相边界层中Mg的扩散。双重控制时Mg的传质系数为10~(-5)—10~(-2)cm·s~(-2)数量级,而气相边界层中Mg的传质系数为140cm·s~(-1)左右。借助于动力学公式、回归方程及特殊的参数转换,建立了一个简单的Mg挥发数学模型,该模型计算结果与实验室及生产条件下试验数据很好地符合,因此,可通过控制熔炼参数,例如向金属熔池加Mg量,Ar压力,挥发温度及时间等来精确地控制最佳Mg含量。

 
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