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高能球
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  high energy ball
    MECHANICAL ALLOYING PROCESS DURING HIGH ENERGY BALL MILLING
    高能球磨过程Fe-Ni机械合金化特点
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    Fe-6.5%Si alloy turned into a simple phase, supersaturated solid solution with the nanocrystalline structure, during high energy ball milling in argon shield;
    Fe-6.5%Si合金在氩气保护下高能球磨过程中成分稳定,球磨产物为纳米晶结构的过饱和固溶体;
    Study on the Orthogonal tests of Tungsen & Iron Nano-meter Powder Preparation by High Energy Ball Milling
    高能球磨法制备钨、铁纳米粉的正交实验研究
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    REACTION OF Ti WITH BN DURING HIGH ENERGY BALL MILLING PROCESS
    高能球磨过程中Ti与BN的反应
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    Preparation of Ultra-fine Zr Powder by High Energy Ball Milling
    高能球磨法制备吸气材料用超细锆粉
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  “高能球”译为未确定词的双语例句
    The effect of high-energy ball-milling and grinding on the powder shape and size, microstructure and magnetic properties of Sm2Fe16Ti1Nx nitride prepared by HDDR was investigated.
    在用HDDR法制备Sm2Fe16Ti1Nx氮化物过程中,研究了高能球磨对氮化物粉末的形貌、物相结构及磁性能的影响。
    Diffusion reaction during high-energy ball milling
    高能球磨固态扩散反应研究
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    Characteristics of High Energy Milled W-Ni-Fe Nanocomposite Powders
    高能球磨合成W-Ni-Fe纳米复合粉末特性
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    Microstructure Variation of Al-Pb-Cu Alloy During Ball Milling and Subsequent Sintering Process
    Al-Pb-Cu合金在高能球磨和烧结过程中的组织结构变化
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    Numerical simulation of extrusion of high energy milled Ti/Al powders
    高能球磨Ti/Al粉末挤压固结致密过程数值分析
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  high energy ball
Microwave permeability change of FeCo nanocrystalline during high energy ball milling
      
The microstructure and chemical bonds of β-C2S under the high energy ball grinding function
      
Preparation of MgTiO3 ceramics by high energy ball milling
      
Carbon microspheres produced by high energy ball milling of graphite powder
      
During high energy ball milling of graphite powder, carbon microspheres were produced from necklace-like carbon structures that were gradually peeled off and finally fractured into particles.
      
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Dispersion-strengthening Al-C alloys have been prepared by mechanical alloying technology. Its technological process was as follows: high energy milling of pure aluminium powder with carbon black or organic agents, cold isostatic compacting of the milled powder at 2—2.5 t/cm~2, packing the green compacts with pure aluminium sheet without scaling, heating the compacts to 550-600℃ in nitrogen atmosphere for 1 hr., and final hot extrusion consolidation to obtain extruded bars of diameter 13mm with reduction ratio...

Dispersion-strengthening Al-C alloys have been prepared by mechanical alloying technology. Its technological process was as follows: high energy milling of pure aluminium powder with carbon black or organic agents, cold isostatic compacting of the milled powder at 2—2.5 t/cm~2, packing the green compacts with pure aluminium sheet without scaling, heating the compacts to 550-600℃ in nitrogen atmosphere for 1 hr., and final hot extrusion consolidation to obtain extruded bars of diameter 13mm with reduction ratio of 26:1. In the present work, two methods of addition of carbon were used and compared: physical carbon method, in which carbon black was adoped directly; chemical carbon method, in which carbon was created through the decomposition of organic agents, such as stearic acid or methanol during milling or subsequent heat treatment. The experiment results showed that both the methods of carbon addition could achieve excellent mechanical properties at normal or elevated temperature, and the strength levels could reach or surpass those of coventionally produced SAP aluminium alloys. The tensile properties of the extruded bar with chemical 1.23 w.t% carbon at room temperature were σ_b 42—43 kg/mm~2(412—422 MN/m~2), δ 5—8%, ψ 18—21%, and that with physical 3wt.%carbon, σ_b 37—39 kg/mm~2 (363—382MN/m~2), σ 8—10%, ψ13—17%. It is evident that the effect of chemical carbon on mechanical properties is considerably better than that of physical carbon, which might be contributed to a more fine and more uniform distribution of dispersoids. But the addition of physical carbon is beneficial to the safety in operating of the milled powder, and the elemental composition can be accurately controlled. The technology of powder forging was also described briefly. In order to reduce the cold work hardening of milled powder and create in-situ Al_2O_3 and Al_4C_3 dispersoids, the milled powder was annealed in nitrogen atmo- sphere at 550—600℃ for 1 hr., and then the softened powder was die pressed into preforms of 9.2mm (width)×67.9mm(length) at 3—3.5t/cm~2, and finally the preforms were heated in dissociated ammonia at 600℃ and forged in a 60t frictional press to obtain billets of 12.6mm×70.2mm. The forging products, especially alloy with the addition of chemical carbon, possess good mechanical properties except low ductility, for example, the alloy containing chemical 0.99 wt.% carbon was σ_b 35—37kg/mm~2 (343—363MN/m~2), the elevated temparature tensile strength at 300 and 400℃ was 26—27kg/mm~2(255—265MN/m~2) and 19—20 kg/mm~2(186—196MN/m~2) respectively.

高能球磨纯铝粉和碳,然后把处理好的粉末热挤压密实,制得了弥散强化Al-C合金。本研究工作采用并比较了两种添加碳的方法——物理碳法和化学碳法。结果表明,两种方法都能得到很好的室温和高温性能,而且强度水平达到和超过SAP铝合金。化学碳法对性能的影响明显地优于物理碳法,但是添加物理碳对合金粉末的安全操作是有利的,同时组份可以得到精确的控制。本文简要地叙述了粉末锻造工艺,除塑性差外锻造制品的其他机械性能也是良好的,特别是对添加化学碳的合金。

TiAlMn superalloy reinforced by dispersed ZrO_2 particles was prepared by means of P/M techniques, such as high energy ball-milling, general ball-milling, cold isostatic pressing and hot isostatic pressing. Microstructures, phase characteristics and properties of the superalloy were studied by X-ray diffractometry and electron microscopy. The results showed that the density of the best TiAlMn+ZrO_2 alloy was 3.972g/cm~3, and the bending strength of the alloy was 658.07 MPa.ZrO_2 particles were dispersed homogenously...

TiAlMn superalloy reinforced by dispersed ZrO_2 particles was prepared by means of P/M techniques, such as high energy ball-milling, general ball-milling, cold isostatic pressing and hot isostatic pressing. Microstructures, phase characteristics and properties of the superalloy were studied by X-ray diffractometry and electron microscopy. The results showed that the density of the best TiAlMn+ZrO_2 alloy was 3.972g/cm~3, and the bending strength of the alloy was 658.07 MPa.ZrO_2 particles were dispersed homogenously by high-energy ball- milling, and the alloy obtained fine grain size. The properties of the alloy made from high-energy ball-milling powders are superior to that of the alloy made from general ball- milled powder.

采用粉末冶金技术(高能球磨、滚动球磨、冷等静压和热等静压)研制出TiAlMn+ZrO_2弥散强化型高温合金,并利用X射线衍射仪、扫描电子显微镜(SEM)和三点弯曲等技术分析了该合金的组织结构和性能。结果表明,最佳的TiAlMn+ZrO_2合金的密度为3.972 g/cm~3,抗弯强度为658.07 MPa。结果还表明,高能球磨可使ZrO_2质点高度弥散分布,从而可获得细晶组织的合金;用高能球磨粉制得的合金性能优于滚动球磨粉制得的合金性能。

Crystal size and microstrain caused by mechanical alloying on Fe_(70)B_(30) powder were studiedby X-ray diffractometry and transrnission electronmicroscopy. During the mechanical alloying, thewidth of the x-ray diffraction lines increases withball milling time , it is caused both by the reductionof crystal size and the increase of microstrain. Byanalysing the x-ray diffraction lines,we got theresults as following: the crystal size of Fe_(70)B_(30)powder decreases when increaseing milling time inthe case of mechanical...

Crystal size and microstrain caused by mechanical alloying on Fe_(70)B_(30) powder were studiedby X-ray diffractometry and transrnission electronmicroscopy. During the mechanical alloying, thewidth of the x-ray diffraction lines increases withball milling time , it is caused both by the reductionof crystal size and the increase of microstrain. Byanalysing the x-ray diffraction lines,we got theresults as following: the crystal size of Fe_(70)B_(30)powder decreases when increaseing milling time inthe case of mechanical alloying of Fe and B powdermixtures.The microstrain increase with milling timeat the early stage of milling and begain to decreaseafter 80 h milling. The grain size of Fe_(70)B_(30) powderafter 80h milling is about 5 nm which is determinedby the Scherrer formula.

用X射线和电镜研究了Fe_(70)B_(30)粉末经不同时间高能球磨后晶粒尺寸和微观应力的变化。在机械合金化过程中,粉末的X射线衍射谱的宽度随球磨时间的增加逐渐加宽,这是晶粒细化和内部微观应力共同作用的结果。X射线衍射结果表明:随着机械合金化的进行,粉末的晶粒尺寸逐渐减小,球磨初期晶粒尺寸下降较快,经15h球磨,晶粒尺寸为25nm,机械合金化进行到一定时间后晶粒尺寸下降缓慢,80h球磨后晶粒尺寸可达5nm。在机械合金化过程中球磨所造成的微观应变不大,球磨初期粉末的内应力随球磨时间增加而增加,当粉末粒子尺寸很小时,随球磨的进行粉末中的微观应变显著下降。

 
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