球磨时间和热压温度对粉末冶金Nb-16Si-22Ti-2Al-2Hf-2Cr合金显微组织和室温力学性能的影响

采用粉末冶金法制备了Nb-16Si-22Ti-2Al-2Hf-2Cr合金,研究了粉末球磨时间（5、10、20 h）及热压烧结温度（1500、1600 ℃）对合金组织和室温力学性能的影响。结果表明：热压烧结后的合金由Nb基固溶体NbSS、Ti基固溶体TiSS和硅化物Nb5Si3三相组成。随着球磨时间的延长,Nb5Si3和TiSS的含量增加,而NbSS的含量减少。室温硬度随球磨时间延长和热压烧结温度的升高而提高,20 h/1600 ℃热压烧结合金硬度值最高,HV硬度达到11500 MPa。1500和1600 ℃热压烧结下合金的断裂韧性随着粉末球磨时间的延长均呈下降的趋势,5 h/1500 ℃热压烧结合金断裂韧性值最高,为10.14 MPa·m1/2。     

合金化元素Ti对Laves相Cr_2Nb力学性能及耐蚀性的影响

采用真空非自耗电弧熔炼工艺制备了Cr2Nb-XTi(X=5,10,15,at%)合金,利用光学显微镜(OM),X射线衍射(XRD)仪,扫描电镜(SEM)对电弧熔炼态铸锭的组织进行了研究,探讨了合金化元素Ti的含量对Laves相Cr2Nb力学性能及耐蚀性的影响。结果表明:3种成分的电弧熔炼态合金凝固组织主要由C15-Cr2(Nb,Ti)相和六方的β-(Ti,Nb)以及体心立方结构的β-(Nb,Ti)相组成。在5Ti和10Ti合金冷速较小的铸锭上部凝固组织中出现了亚稳相C14-Cr2(Nb,Ti)。通过对合金力学性能研究表明,随合金化元素Ti含量的增加,Laves相Cr2Nb合金的显微硬度逐渐降低,断裂韧性增大,当Ti含量达到15at%时,合金的断裂韧性达到了3.1 MPa·m1/2,比单相Laves相Cr2Nb提高1倍。另外,对腐蚀性能的测试表明,Ti含量增加材料腐蚀性能下降,但15Ti合金仍表现出良好的耐蚀性。     

定向凝固Nb-Ti-Si基超高温合金的组织与室温条件断裂韧性

采用真空自耗电弧熔炼法制备了Nb-Ti-Si基超高温合金的母合金锭,在2050℃的熔体温度下实现了合金的有坩埚整体定向凝固.测定了电弧熔炼态与定向凝固试样的室温条件断裂韧性,采用SEM,EDS等方法分析了凝固速率V分别为10,20和50 μm/s的整体定向凝固组织、单边切口梁弯曲试样的断口形貌及裂纹扩展路径,并讨论了其断裂机理.结果表明:合金的整体定向凝固组织主要由沿着试棒轴向挺直排列的横截面为多边形的初生(Nb,X)5Si3 (X代表Ti,Hf和Cr元素)棒与耦合生长的层片状Nbss/(Nb,X)5Si3共晶团(Nbss表示铌基固溶体)组成.整体定向凝固显著提高合金的室温条件断裂韧性KQ,且V=50μm/s时的最高,达16.1 MPa·m1/2,较电弧熔炼态试样的KQ提高了50.5％.定向凝固试样中Nbss与(Nb,X)5Si3沿垂直于受力方向的定向排列以及粗糙的Nbss产生的裂纹桥接和偏转,增大了裂纹扩展阻力,从而提高了合金的室温条件断裂韧性.     

热处理对(Mo0.85Nb0.15)Si2单晶显微结构的影响

电弧熔炼制备的(Mo0.85Nb0.15)Si2合金为MoSi2(C11b结构)和NbSi2(C40结构)两相组织.以电弧熔炼得到的合金为母合金,通过光学悬浮区域熔炼法,选择适当的生长速度4 mm/h制备了(Mo0.85Nb0.15)Si2单晶,单晶结构为C40结构.对单晶在1 200～1 700℃进行不同时间的退火处理.研究了不同热处理制度对合金显微结构的影响规律.结果表明:经1 600℃,6 h退火处理后,在合金中形成了排列紧密、方向取向相同的全片层状结构,片层间距为200～300 nm.经EDS分析,这种片层结构由贫Nb的C11b相和富Nb的C40相组成.     

球磨时间和热压温度对粉末冶金Nb-16Si-22Ti-2Al-2Hf-2Cr合金显微组织和室温力学性能的影响

采用粉末冶金法制备了Nb-16Si-22Ti-2Al-2Hf-2Cr合金,研究了粉末球磨时间(5、10、20h)及热压烧结温度(1500、1600℃)对合金组织和室温力学性能的影响。结果表明:热压烧结后的合金由Nb基固溶体NbSS、Ti基固溶体TiSS和硅化物Nb5Si3三相组成。随着球磨时间的延长,Nb5Si3和TiSS的含量增加,而NbSS的含量减少。室温硬度随球磨时间延长和热压烧结温度的升高而提高,20h/1600℃热压烧结合金硬度值最高,HV硬度达到11500MPa。1500和1600℃热压烧结下合金的断裂韧性随着粉末球磨时间的延长均呈下降的趋势,5h/1500℃热压烧结合金断裂韧性值最高,为10.14MPa·m1/2。     

稀土Y对Nb-Ti-Si基超高温合金组织及抗氧化性能的影响

采用真空非自耗电弧熔炼法制备了5种成分为Nb-22Ti-15Si-5Cr-3Al-3Hf-x Y(x=0,0.03,0.06,0.12,0.30 at%)的合金,并在1250℃下分别进行了1、10、20和50 h的高温氧化实验,研究Y含量对合金电弧熔炼态组织及其高温抗氧化性能的影响。结果表明:添加Y不改变电弧熔炼态合金相组成,组织仍由Nbss及γ-(Nb,X)5Si3相组成,但细化了共晶组织。高温氧化实验结果表明,不同Y含量合金在氧化不同时间后,氧化膜均由Nb2O5,Ti O2,Ti2Nb10O29和Ti Nb2O7组成;随着Y含量的增加,氧化膜中的孔洞和裂纹减少,合金单位面积氧化增重也逐渐减小,表明Y的添加能够显著提高合金的高温抗氧化性能。     

定向凝固过共晶Nb-Si基合金的组织优化

采用液态金属冷却定向凝固炉制备Nb-16Si-24Ti-10Cr-2A1．2Hf合金,凝固速率分别为1．2、6、18、36、50mm／min,随后对定向凝固速率为50mm／min的合金进行（1400℃,10h）,（1450℃,10h）和（1500℃,10h）的热处理。研究了定向凝固速率和热处理温度对合金微观组织的影响。结果表明：合金的定向凝固组织主要由沿着试棒轴向生长的初生Nb5Si3相和耦合生长的Nbss／Nb5Si3共晶胞组成,在共晶胞边缘,有少量的Cr2Nb存在。横截面上共晶胞边界明显,随着凝固速率的增加,定向凝固组织明显细化,Nbss／Nb;Si,共晶胞形貌也发生变化。合金经过热处理,Nbss连成基体,部分CrENb相熔解,微观成分偏析减小。经过（1450℃,10h1热处理,实现了对过共晶Nb—Si基合金的组织优化。     

铸态Ti-22Al-25Nb合金的结构特征与力学性能

Ti2AlNb基合金是目前有望在650-800℃温度范围内取代高温镍基合金的金属间化合物。利用水冷铜坩埚感应悬浮熔炼法，通过调控熔炼工艺，制备了主相分别为B2/?相和O相 Ti-22Al-25Nb合金铸锭，通过XRD、SEM等手段进行了合金结构特征的表征，通过室温拉伸试验、室温压缩试验、纳米压痕试验测试了合金的力学性能并分析了断口形貌。研究表明，铸态Ti-22Al-25Nb合金晶粒尺寸达到数百微米。相组成对铸态Ti-22Al-25Nb合金的力学性能有一定影响，铸态O相合金的极限抗拉强度达到了1125MPa，超过了铸态B2/?相合金的1031MPa，但粗大晶粒导致合金塑性较差（铸态B2/?相与铸态O相合金的延伸率分布为1.82%与1.32%）。铸态Ti-22Al-25Nb合金的拉伸断口与压缩断口均具有明显的解理断裂特征，拉伸断口主要表现为沿晶断裂，压缩断口主要表现为穿晶断裂。     

凝固速率对铌基共晶自生复合材料定向凝固组织的影响

铌基共晶自生复合材料（NBISC）经真空自耗电弧熔炼成母合金锭，采用高温度梯度的电子束区熔装置制备定向凝固的试样，分析其组织特征。结果表明：Nb基固溶体（Nbss）相、（Nb，Ti）3Si相和（Nb，Ti）5Si3相为NBISC材料的主要组成相；在电了束区熔条件下，随着电子枪移动速率的提高，NBISC材料共晶组织变细，组织中片层状的共晶团增多，块状或板条状的（Nb，Ti）3Si／（Nb，Ti）5Si3相尺度减小、数量增多，组织趋于规则、分布更均匀，组织的定向性增强，定向效果显著。     

Hf含量对Nb-Si基超高温合金组织的影响

采用真空非自耗电弧熔炼的方法制备了4种名义成分为Nb-22Ti-16Si-3Cr-3Al-x Hf(x=0,2,4,8,at%)的合金,并于1450℃保温50 h进行了均匀化处理,研究Hf含量对Nb-Si基超高温合金电弧熔炼态及热处理后组织的影响。结果表明:不含Hf的合金的组织主要由初生α(Nb,X)5Si3,Nbss枝晶以及2种共晶(即Nbss/α(Nb,X)5Si3和Nbss/γ(Nb,X)5Si3)构成;加入2 at%Hf,促进了初生γ(Nb,X)5Si3的形成并增加了Nbss/γ(Nb,X)5Si3共晶的含量;当Hf含量增加至4 at%和8 at%时,α(Nb,X)5Si3的形成受到完全抑制,合金中的硅化物仅以γ(Nb,X)5Si3的形式存在。经1450℃/50 h热处理后,原电弧熔炼态的Nbss枝晶与典型的共晶组织形貌基本消失,合金的组织均匀分布。对Hf含量为0 at%和2 at%的合金来说,热处理后的相组成没有发生改变,但α(Nb,X)5Si3的含量减少;而对Hf含量为4 at%和8 at%的合金来说,热处理后Cr2Nb Laves相消失,且在后一种合金中还观察到少量棒状的(Nb,X)3Si相。     

Mo effect on the phase stability and room-temperature fracture toughness of Nb/Nb_5Si_3 in-situ composites

Nb/Nb5Si3 in-situ composites are very attractive structural materials because these materials perform a good balance in mechanical properties, including high strength at high temperature (>1000℃) and reasonably high fracture toughness at room temperature. Metastable phase Nb3Si plays an important role in the properties of     

合金元素对Laves相增强Nb基合金的相组成

采用机械合金化与热压烧结工艺制备了添加合金元素V和Fe的Laves相增强的Nb基复合材料。研究了添加质量分数4%V和Fe的Nb/NbCr2-4.0V和Nb/NbCr2-4.0Fe配比成分的元素粉,经MA20h后在1250℃热压30min所获得的Nb/NbCr2合金的组织和性能。结果表明:在热压过程中原位合成出细小弥散分布的三元Laves相Nb(Cr,V)2和Nb(Cr,Fe)2,并且V和Fe原子只占据Laves相中的Cr原子位置。制备出的Laves相增强Nb基合金接近全致密,组织细小均匀,晶粒尺寸小于500nm。Nb/NbCr2-4.0V和Nb/NbCr2-4.0Fe合金的断裂韧性分别达到5.3和6.3MPa·m1/2,其中Nb/NbCr2-4.0Fe合金不仅抗压强度达到2256MPa,其屈服强度和塑性应变也分别达到2094MPa和6.03%。     

(Nb,Ti)C的制备方法对(Nb,Ti)C-35Ni金属陶瓷的微观结构及性能的影响

用自蔓燃高温合成（SHS）技术及电弧熔融法制备的（Nb，Ti）C固溶体作基体，制备（Nb，Ti）C－35Ni金属陶瓷。结果表明用电弧熔融法制备的（Nb，Ti）C为基的试样具较优的室温力学性能（σ＝1630MPa，KIC＝18．0MPa），其陶瓷颗粒均匀分行粘结相之中并是包裹结构；而用SHS法制备的（Nb，Ti）C为基的试样其力学性能相对较差，其陶瓷颗粒无包裹结构．     

Comparative studies on densification behavior,microstructure, mechanical properties and oxidation resistance of Mo-12Si-10B and Mo3Si-free Mo-26Nb-12Si-10B alloys

Two bulk Mo-Si-B based alloys (Mo-12Si-10B and Mo-26Nb-12Si-10B (at.%), abbreviated as 0Nb and 26Nb alloy respectively) were fabricated by mechanical alloying and then hot pressing. Comparative studies were carried out on the densification behavior, microstructure, room-temperature fracture toughness, elevated temperature compression and oxidation resistance of these two alloys. The results showed that alloy 0Nb was composed of (Mo), Mo₃Si and Mo₅SiB₂, while alloy 26Nb was free of Mo₃Si and had higher (Mo) content and a little γNb₅Si₃. Compared to the alloy 0Nb, alloy 26Nb presented better compactibility, higher room-temperature fracture toughness (8.84 ± 0.17 vs. 6.77 ± 0.20 MPa·m^1/2) and elevated temperature compression strength (851.7 ± 11.7 vs. 644.2 ± 10.2 MPa) but worse oxidation resistance.     

Mo-Si-B三元系中T2相合金制备及其室温力学性能

通过放电等离子烧结(SPS)制备T2(Mo5SiB2)相合金,并采用SEM、XRD及压痕、压缩和三点弯曲等实验对合金的微观组织和室温力学性能进行表征。结果表明:SPS法以独特的等离子活化烧结方式制备出纯度高、致密且晶粒细小的T2相合金。该合金在室温压缩下几乎没有塑性变形,抗压强度为2907MPa;维氏硬度为17.86GPa,压痕法测得的断裂韧性为3.23MPa·m1/2,与三点弯曲法测得的3.34MPa·m1/2接近,沿{001}面发生解理断裂。共价键交替排列,是T2相室温脆性、高强度、高硬度的根本原因。     

Effect of Yttrium on Microstructure and Properties of High Temperature Alloys

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Mechanical properties of Mo-Nb-Si-B quaternary alloy fabricated by powder metallurgical method

Mo-Si-B alloys composed of two intermetallic compound phases (Mo₅SiB₂ and Mo₃Si) and a molybdenum solid solution matrix phase have been investigated for use as high-temperature structural materials due to their high melting point and good creep resistance. However, despite these advantages, Mo-Si-B alloys are difficult to use in practical applications because they have insufficient fracture toughness at room temperature. So, in many researches, microstructure control and the addition of other elements in the α-Mo matrix phase are conducted as an effective way to improve the fracture toughness.In this study, niobium (Nb) was added to a Mo-Si-B alloy by a powder metallurgical method to improve the mechanical properties. First, the Mo and Nb powders were pulverized by high-energy ball milling. Then, the synthesized intermetallic compound powders, which were fabricated by continuous heat treatment under a H₂ atmosphere, were mixed with ball-milled Mo and Nb powder. Pressureless sintering was conducted at 1400 °C for 3 h under a H₂ atmosphere. The Vickers hardness and fracture toughness were measured to investigate the mechanical properties of the sintered Mo-Si-B and Mo-Nb-Si-B alloy. The Vickers hardness was about 425 Hv for a Mo-Nb-Si-B alloy, which was lower value of 165 Hv compared to Mo-Si-B alloy (590 Hv). On the other hand, the fracture toughness of the Mo-Nb-Si-B alloy (14.5 MPa·√m) greatly increased compared to that of the Mo-Si-B alloy (12.6 MPa·√m).     

Microstructural evolution and mechanical properties of as-cast and directionally-solidified Nb-15Si-22Ti-2Al-2Hf-2V-(2, 14) Cr alloys at room and high temperatures

Arc-melting (AC) and directional solidification (DS) techniques were used to prepare Nb-15Si-22Ti-2Al-2Hf-2V-(2, 14) Cr alloys (hereafter referred as to 2Cr and 14Cr alloys, respectively), and the microstructural evolution and mechanical properties, including Vickers hardness, room temperature fracture toughness and high temperature strength, of the two AC and DS alloys were compared. The results showed that with heat-treatment at 1350 °C for 50 h, the AC-2Cr alloy composed of Nb solid solution (Nb_SS) and α-Nb₅Si₃ silicide, while Laves C15-Cr₂Nb phase arose in the 14Cr alloy. With two-phase Nb_SS/α-Nb₅Si₃ microstructure, the AC-2Cr alloy showed excellent room-temperature fracture toughness (K_Q: 14.2 MPa m^1/2) and 0.2% yield strength at 1250 °C (σ_0.2: 315 MPa) and 1350 °C (σ_0.2: 294 MPa), better than the AC-14Cr alloy with tri-phase Nb_SS/α-Nb₅Si₃/C15-Cr₂Nb microstructure (K_Q: 9.4 MPa m^1/2, σ_0.2: 189 MPa at 1250 °C and 87 MPa at 1350 °C). The DS technique was found not to change the phase constituent of each alloy, but it made the microstructure slightly orient to the growth direction, resulting in a significant improvement in room-temperature fracture toughness (by ∼43%) and high-temperature yield strength σ_0.2 (by ∼55%), as compared with the AC samples.