真空雾化法制备MCrAlTaY合金粉末

为了满足现代航空发动机高推比的要求,用真空雾化法制备了MCrAlTaY合金粉末,同时对合金粉末的相貌、微观组织和合金元素的作用进行了分析。研究结果表明:用该技术生产的粉末球形度高,微观组织均匀,第二相的析出细小,保证了满足涂层的使用性能。     

CuCr50合金粉末的制备及微观组织分析

开发了高温高真空气雾化技术 ,并利用该技术制备了CuCr5 0合金化粉末 ,对合金粉末的相貌、微观组织和合金元素成分分布进行了分析。研究结果表明 :粉末球形度高 ,合金化状况良好 ,微观组织均匀 ,Cr析出相细小 ,有利于提高触头材料的综合使用性能。     

高能球磨制备高铝锌铝合金粉末的研究

首先采用一步球磨法制备了成分为Zn-30Al-6Si-0.5Cu(质量分数/%)和Zn-30Al-3Si-3Cu(质量分数/%)的高铝锌铝合金粉末,其次采用二步球磨法制备了成分为Zn-30Al-6Si-0.5Cu(质量分数/%)的合金粉末,并利用XRD、SEM粒度分析仪对粉末的物相组成、颗粒形貌及粒度进行了表征和分析。结果表明:含硅量为6%的合金粉末的颗粒尺寸比含硅量为3%的合金粉末更为细小,尺寸分布更为集中,球磨12h之后的粉末其金相组织主要由富Al的α相、富Zn的η相以及Si相组成。经过二步球磨后的Zn-30Al-6Si-0.5Cu粉末中Al9Si相基本消失,Si相含量增加;二步球磨法制备的粉末颗粒尺寸更为细小。通过扫描电镜观察发现粉末形貌不规则,且分布不够均匀,粉末中基本未观察到类似焊片的颗粒。     

气体雾化LaNi5型储氢合金粉末特性的研究

采用金相显微镜、扫描电镜、俄歇能谱探针、Ｘ射线衍射对气体雾化法制备的储氢合金粉末的物理特性、表面化学状态、显微组织结构进行了初步探讨，并将其与熔铸破碎法所制备的合金粉末相比较。结果表明：气体雾化法制备的储氢合金粉末氧含量低，呈球形无表面缺陷；物相组成为单一ＬａＮｉ５相；显微结构呈细小胞状晶和枝状晶组织。     

W-20%Cu超细复合粉末的制备和烧结

采用喷雾干燥-氢气还原法制备出W-20%Cu超细复合粉末,并对由该复合粉末所制得的压坯进行了烧结,利用SEM、XRD等分析手段对复合粉末的特性和烧结体的组织进行了表征和观察.试验结果表明:用该方法制备的W-20%Cu超细复合粉末颗粒细小,平均尺寸在200nm左右;喷雾干燥后的氧化物复合粉末在还原后产生了新的合金相(Cu0.4W0.6),还原后的复合粉末由Cu0.4W0.6相和Cu相组成,而且两相的晶粒度达到纳米级,其中Cu0.4W0.6相的晶粒约为33nm,Cu相的晶粒约为63nm;复合粉末具有很高的烧结特性,经烧结后合金相对密度达到98%以上,而且金相组织分布均匀.     

一种粉末冶金制备钼合金TZM的方法

一种粉末冶金制备钼合金TZM的方法,涉及一种采用粉末冶金工艺制备难熔金属合金方法。其特征在于是选用费氏粒度在5～10μm,最大颗粒不大于10μm的氢化钛和氢化锆颗粒,采用粉末冶金的方法制备TZM钼合金的。本发明的采用粉末冶金工艺制备钼合金TZM的方法,通过添加颗粒细小的合金元素粉末;由于第二相颗粒尺寸小,使烧结过程扩散均匀;提高了材料组织的均匀性,     

预混合法和预合金法制备Cu-Sn粉末的显微组织和烧结性能

使用预混合法和预合金法制备了Cu-Sn粉末,研究了Cu-Sn粉末在烧结过程中的显微组织和物相变化规律,同时测试了Cu-Sn粉末在不同温度条件下的烧结性能。实验结果显示,通过预混合法制备的CuSn10、CuSn20粉末烧结态组织由α相和α+δ共析组织组成,而预合金法制备的CuSn10粉末烧结态组织则由单一的α相组成。两种方法制备的粉末在相同条件下烧结后,预混合Cu-Sn粉末的烧结体相对于生坯产生了膨胀,预合金铜锡粉末烧结体则表现为收缩,且预合金Cu-Sn粉末烧结后的断裂强度、含油率和有效含油率均高于预混合粉末。     

原料粉末对NiTi的选区激光熔化成形件性能的影响

分别以Ni+Ti元素混合粉末和NiTi预合金粉末为原料,采用选区激光熔化工艺打印成形.重点研究了在相同打印工艺参数下原料粉末对成形件致密度、物相组成、显微组织、显微硬度的影响,从而反馈说明所用打印粉末对成形件性能的影响.结果 表明:在相同打印工艺参数下,整体上NiTi预合金粉末成形件的致密度较高,而Ni+Ti混合粉末成形件的显微硬度较高.对于同一种粉末,随着能量密度的增大,成形件的致密度先增大后减小,而显微硬度先减小后增大.NiTi预合金粉末成形件有致密的微观结构且相分布均匀,但存在少量孔隙.Ni+Ti混合粉末成形件的微观结构有和构建方向垂直的贯穿式裂纹以及不均匀的基体相,但几乎没有孔隙.     

镍基双合金扩散偶的拉伸性能研究

采用热等静压(HIP)扩散连接工艺,获得了镍基单晶高温合金与粉末高温合金的扩散偶。研究了热等静压和热处理工艺对扩散偶的组织和拉伸性能的影响。结果表明,不同温度热等静压的扩散偶均实现了冶金结合,瞬时拉伸断口位置处于DD402侧,断裂面为{111}滑移面。随着HIP温度升高,DD402母材的γ′相粒子粗化,FGH95粉末合金母材的再结晶晶粒长大;1 166℃HIP扩散偶热处理后,FGH95粉末合金的γ′相由晶界大尺寸γ′相、晶粒内中等尺寸的和细小的γ′相组成。扩散偶试样的650℃抗拉强度受HIP温度影响小,而屈服强度随着HIP温度升高而降低。     

机械合金化结合激光熔覆技术制备CoCrMoNbTi难熔高熵合金

采用机械合金化方法制备CoCrMoNbTi难熔高熵合金粉末，并通过激光熔覆技术成功制备出CoCrMoNbTi高熵合金涂层。研究了球磨时间对合金粉末组织形貌的影响，并利用X射线衍射仪、扫描电子显微镜和能谱仪等分析了高熵合金粉末和涂层的微观结构。结果表明，随着球磨时间的增加，单质金属的衍射峰按其熔点由低到高陆续消失。粉末微观形貌随球磨时间变化明显，粉末由原始状态被挤压成片状，片状粉末逐渐焊合在一起形成扁平状粉末颗粒。在球磨时间达到40 h时，粉末实现完全合金化，此时粉末形貌趋于球形且得到了极大的细化，粉末中各元素分布均匀，形成了稳定的单相体心立方固溶体结构。CoCrMoNbTi难熔高熵合金激光熔覆层成形质量良好，主要由体心立方固溶体和少量Cr₂Nb、Co₂Ti化合物组成，树枝晶组织细小致密。     

TA7ELI粉末冶金材料力学性能与显微组织

以TA7 ELI钛合金棒为原料,用等离子旋转电极工艺制备出高品质钛合金球形粉末.采用热等静压成形工艺,将粉末压制成钛合金材料,并研究了材料的组织和力学性能.结果表明:等离子旋转电极工艺制备的钛合金球形粉末具有非常高的球形度和振实密度,粒度分布比较窄,非金属夹杂含量非常低;热等静压制备的低温钛合金达到全致密,其组织均匀细...     

Processing and microstructure of Powder Metallurgy Al-Fe-Ni Alloys

Prealloyed rapidly solidified Al-Fe-Ni alloy powder with dispersoid volume fractions of 0.19, 0.25, and 0.32 FeNiAl₉ was produced by air atomization. The powder was degassed, canned, and consolidated to full density by vacuum hot pressing and extrusion or by direct extrusion. Microstructures in the alloy powder and consolidated material were characterized by means of optical, scanning (SEM), and transmission electron microscopy (TEM) and constituent phases identified by X-ray diffraction. The coarsening kinetics of the FeNiAl₉ dispersoid were moni- tored by differential scanning calorimetry (DSC) and by quantitative metallography. Atomized powders exhibited two scales of microstructures: optically featureless regions and regions with a coarse dispersoid morphology. Within the featureless regions, there are three morphologies, namely, a fine uniform precipitate microstructure, a cellular microstructure, and an eutectic microstructure. The only dispersoid observed in the atomized powders and consolidated material was FeNiAl₉). The two scales of microstructure were retained after consolidation, and after hot extrusion, the typical microstructure consisted of a recovered matrix structure with a grain size of 0.2 to 0.3 μm and equiaxed intermetallics of average diameter 0.1 μm. The microstructure was resistant to coarsening up to approximately 370 °C. Coarsening kinetics in this alloy system were consistent with a grain boundary diffusion model (activation energy 146 kJ/mol) and were not appreciably affected by dispersoid volume fraction.     

Mechanical properties and fracture behavior of an ultrafine-grained Al-20 wt pct Si alloy

The effect of powder particle size on the microstructure, mechanical properties, and fracture behavior of Al-20 wt pct Si alloy powders was studied in both the gas-atomized and extruded conditions. The microstructure of the as-atomized powders consisted of fine Si particles and that of the extruded bars showed a homogeneous distribution of fine eutectic Si and primary Si particles embedded in the Al matrix. The grain size of fcc-Al varied from 150 to 600 nm and the size of the eutectic Si and primary Si was about 100 to 200 nm in the extruded bars. The room-temperature tensile strength of the alloy with a powder size <26 μm was 322 MPa, while for the coarser powder (45 to 106 μm), it was 230 MPa. The tensile strength of the extruded bar from the fine powder (<26 μm) was also higher than that of the Al-20 wt pct Si-3 wt pet Fe (powder size: 60 to 120 μm) alloys. With decreasing powder size from 45 to 106 μm to <26 μm, the specific wear of all the alloys decreased significantly at all sliding speeds due to the higher strength achieved by ultrafine-grained constituent phases. The thickness of the deformed layer of the alloy from the coarse powder (10 μm at 3.5 m/s) was larger on the worm surface in comparison to the bars from the fine powders (5 μm at 3.5 m/s), attributed to the lower strength of the bars with coarse powders.     

Processing and microstructure of powder metallurgy Al-Fe-Ni alloys

Prealloyed rapidly solidified Al-Fe-Ni alloy powder with dispersoid volume fractions of 0.19, 0.25, and 0.32 FeNiAl₉ was produced by air atomization. The powder was degassed, canned, and consolidated to full density by vacuum hot pressing and extrusion or by direct extrusion. Microstructures in the alloy powder and consolidated material were characterized by means of optical, scanning (SEM), and transmission electron microscopy (TEM) and constituent phases identified by X-ray diffraction. The coarsening kinetics of the FeNiAl₉ dispersoid were monitored by differential scanning calorimetry (DSC) and by quantitative metallography. Atomized powders exhibited two scales of microstructures: optically featureless regions and regions with a coarse dispersoid morphology. Within the featureless regions, there are three morphologies, namely, a fine uniform precipitate microstructure, a cellular microstructure, and an eutectic microstructure. The only dispersoid observed in the atomized powders and consolidated material was FeNiAl₉. The two scales of microstructure were retained after consolidation, and after hot extrusion, the typical microstructure consisted of a recovered matrix structure with a grain size of 0.2 to 0.3 μm and equiaxed intermetallics of average diameter 0.1 μm. The microstructure was resistant to coarsening up to approximately 370 °C. Coarsening kinetics in this alloy system were consistent with a grain boundary diffusion model (activation energy 146 kJ/mol) and were not appreciably affected by dispersoid volume fraction.     

Mechanical properties and fracture behavior of an ultrafine-grained Al-20 wt pct Si alloy

The effect of powder particle size on the microstructure, mechanical properties, and fracture behavior of Al-20 wt pct Si alloy powders was studied in both the gas-atomized and extruded conditions. The microstructure of the as-atomized powders consisted of fine Si particles and that of the extruded bars showed a homogeneous distribution of fine eutectic Si and primary Si particles embedded in the Al matrix. The grain size of fcc-Al varied from 150 to 600 nm and the size of the eutectic Si and primary Si was about 100 to 200 nm in the extruded bars. The room-temperature tensile strength of the alloy with a powder size <26 μm was 322 MPa, while for the coarser powder (45 to 106 μm), it was 230 MPa. The tensile strength of the extruded bar from the fine powder (<26 μm) was also higher than that of the Al-20 wt pct Si-3 wt pct Fe (powder size: 60 to 120 μm) alloys. With decreasing powder size from 45 to 106 μm to <26 μm, the specific wear of all the alloys decreased significantly at all sliding speeds due to the higher strength achieved by ultrafine-grained constituent phases. The thickness of the deformed layer of the alloy from the coarse powder (10 μm at 3.5 m/s) was larger on the worn surface in comparison to the bars from the fine powders (5 μm at 3.5 m/s), attributed to the lower strength of the bars with coarse powders.     

Mechanical milling of gas-atomized Al-Ni-Mm (Mm = misch metal) alloy powders

Al-14Ni-14Mm (Mm = misch metal) alloy powders rapidly solidified by the gas atomization method were subjected to mechanical milling (MM). The microstructure, hardness, and thermal stability of the powders were investigated as a function of milling time using X-ray diffraction (XRD), transmission electron microscopy (TEM), and differential scanning calorimetry (DSC) methods. In the early stages of milling, a cold-welded layer with a fine microstructure formed along the edge of the milled powder (zone A). The interior of the powder remained unworked (zone B), resulting in a two-zone microstructure, reminiscent of the microstructures in rapidly solidified ribbons containing zones A and B. With increasing milling time, the crystallite size decreased gradually reaching a size of about 10 to 15 nm and the lattice strain increased reaching a maximum value of about 0.7 pct for a milling time of 200 hours. The microhardness of the mechanically milled powder was 132 kg/mm² after milling for 72 hours and it increased to 290 kg/mm² after milling for 200 hours. This increase in microhardness is attributed to a significant refinement of microstructure, presence of lattice strain, and presence of a mixture of phases in the alloy. Details of the microstructural development as a function of milling time and its effect on the microhardness of the alloy are discussed.     

超声雾化Sn-Pb焊锡粉的组织特征及其抗氧化性能

采用定氧仪、扫描电镜和俄歇表面谱仪研究了超声雾化制备的Sn-Pb焊粉的氧化速率、组织与形貌特征，并与离心雾化焊粉进行了对比。结果表明：超声雾化法制备的粉末形貌和球形度明显优于离心雾化，但在大气中放置粉末的增氧速度较快。显微组织对比发现超声雾化制备的粉末组织晶粒细小、两相分布更加均匀；俄歇分析表明超声雾化粉末表面Pb出现一定程度的富集；高频振动和快冷促进了粉末组织的细化，表面富铅、晶界和相界数量增加是造成焊锡粉室温抗氧化性不足的主要原因。