2090+Ce铝锂合金时效组织形成及其强化机制

以2090铝锂合金作为参照,细致地观察了2090+Ce铝锂合金时效组织特征及其形成规律。首次利用图形分析等手段,对比研究了2090和2090+Ce铝锂合金中沉淀相尺寸分布规律,通过对两合金中δ′相和T_1相生长、粗化行为的研究,探讨了微量稀土Ce的作用机制。研究中发现添加微量稀土Ce,对时效初期δ′相的生长有一定的抑制作用,而对T_1相的析出却有一定的促进作用,其T_1相表现出较小的长厚比。在深入观察2090+Ce合金位错组态特征的基础上,计算了δ′相、T_1相的强化贡献及其综合效应。发现合金中位错组态随时效条件发生变化。T_1相与位错间的交互作用形式是切过和绕过的混合型,两相复合强化形式与时效时间有关。对比研究了2090和2090+Ce铝锂合金板材屈服强度各向异性及其形变织构、人工时效等因素的影响作用,探究了沉淀相强化作用与两合金板材屈服强度各向异性间的内在联系以及微观形变和断裂特征随取向角、时效条件的变化。结果表明T_1相等沉淀相对铝锂合金屈服强度各向异性以及断裂特征有着直接的影响,并提出了一修订的塑性内合物模型。     

微量钪对高Cu/Mg比Al-Cu-Li-Mg合金组织与性能的影响

利用金相显微镜、透射电子显微镜和拉伸试验等手段,研究了微量Sc对高Cu/Mg比Al-3.5Cu-1.5Li-0.5Mg-0.12Zr合金组织和拉伸性能的影响.结果表明:在Al-3.5Cu-1.5Li-0.5Mg-0.12Zr合金中加入0.10%Sc消除了合金铸态枝晶组织,有效抑制合金再结晶,明显提高了合金的强度和塑性,但晶粒细化效果不明显;添加0.15%和0.25%Sc显著细化合金铸态晶粒组织,塑性随Sc增加而提高,但添加0.25%Sc促进合金再结晶,合金强度显著降低.     

Li含量对Al-Mg-Si合金时效析出行为的影响

采用透射电镜研究Li含量对Al-3.0Mg-0.6Si合金时效析出行为的影响,分析不同Li含量合金在170℃人工时效过程中析出相的演化与分布.结果表明:Li元素的添加改变了Al-3.0Mg-0.6Si合金的时效析出行为.添加2.15％(质量分数,下同)Li的合金,球状的δ'-Al3Li相成为晶内优先析出相,而针状的β″-Mg2Si相在时效后期阶段才逐渐析出,并在时效192 h后形成了明显的球状δ'相加针状β″相的双相析出.而添加3.12％Li的合金在所观察的时效阶段内均未发现有β″相析出.另外,未发现含Li合金晶界位置有析出相存在,晶界附近是无沉淀析出带(δ'-PFZs)和δ'相.在时效100 h后发现添加2.15％Li的合金在δ'-PFZ区域有针状β″相析出.添加2.15％Li的合金δ'-PFZ的半宽尺寸和增长速率均大于2.68％,3.12％Li添加量的合金.     

高强高韧Mg-8.5Gd-2.0Y-1.0Ag-0.4Zr合金的组织与性能

研究了高强高韧Mg-8.5Gd-2.0Y-1.0Ag-0.4Zr(wt.%)合金的显微组织和力学性能。结果表明,该合金铸态组织细小,主要由α-Mg固溶体、晶界析出相Mg5(GdY)以及分布在晶粒内部的Zr核组成;T4态时晶界析出相基本完全消失,但出现了一些方块相γ;合金具有明显的时效硬化效果,且随着时效温度的提高,合金的峰值时效硬度下降,峰值时间相应缩短。经200℃峰值时效处理后表现出极为优异的室温力学性能,抗拉强度(UTS)和延伸率分别达到396MPa和9.1%,显著的时效强化是该合金具有优异力学性能的主要原因。如此优异的强度和塑性在常规铸造镁合金中是极为罕见的,对于推广镁合金的应用具有重要意义。     

Si对Al-Mg-Cu合金时效析出行为的影响

向不同镁含量的Al-Mg-Cu合金中添加Si元素,研究Si对该合金时效强化行为的影响,并在此基础上探究自然时效处理对合金后续人工时效行为的影响.研究结果表明,在2.0％Mg的基础上添加0.15 wt％Si可以显著增强合金的人工时效强化效果,但是合金强度随Si含量的进一步增加而增加的幅度较小;Si对合金的时效强化效果是由...     

液态动压实铝锂合金在时效过程中的结构转变

采用液态动压实(LDC)工艺制备的四种铝锂合金在时效过程中强化相的析出规律进行了研究。用 TEM 观察了析出相在晶内、亚晶界和位错上的析出分布。结果表明:四种合金的共同析出相为δ′(Al_3Li),β′(Al_3Zr)和δ′(Al_3Li)的复合析出相。改变合金中的铜、镁、锂含量,对强化相θ′(Al_2Cu),T_1(Al_2CuLi)和 S′(Al_2CuMg)的形成有较大的影响。同时也发现在190℃时效有利于β′+δ′复合相,S′和 T_1相的析出.     

Cu-Ni-Si-Ag合金冷变形及动态再结晶研究

研究了时效温度和时效时间对不同冷变形条件下Cu-2.0Ni-0.5Si-0.15Ag合金组织和性能的影响.在Gleeble-1500D热模拟试验机上,采用高温等温压缩试验,对Cu-2.0Ni-0.5Si-0.15Ag合金在高温压缩变形中的流变应力行为和组织变化进行了研究.结果表明:合金经900℃固溶,在经不同冷变形后时效,能获得较高的显微硬度与导电率,当变形量为80%,时效温度达到450℃时,其显微硬度达到220Hv,导电率达到41%IACS.热模拟实验中,应变速率和变形温度的变化强烈地影响合金流变应力的大小,流变应力随变形温度升高而降低,随应变速率提高而增大,材料显微组织强烈受到变形温度的影响.     

形变量和时效对Al-Cu-Li合金组织性能的影响

为了改善铝合金的力学性能,利用形变和时效工艺提高Al-3.5Cu-1.5Li-0.12Zr合金的强度和塑性.采用TEM观察和室温拉伸试验等手段,研究了形变量和时效工艺对含钪Al-3.5Cu-1.5Li-0.12Zr合金微观组织与拉伸性能的影响.结果表明,时效前的变形能促进T1(Al2CuLi)相弥散细小析出,显著提高合金强度,使时效峰值提前.合金强度随形变量和时效时间增加而增加,到峰值后,随形变量增加和时效时间的延长,T1相长大粗化,合金强度和塑性降低.该合金合宜的形变量和时效工艺为3.5%预变形和160℃/24 h时效.     

时效时间对一种新型Al-Cu-Li系合金显微组织和力学性能的影响

研究了时效时间对一种新研制的Al-Cu-Li系合金组织性能的影响。研究发现:在不同时效状态下,该合金析出了δ′,T1,θ′,θ″,σ等第二相,时效过程中析出T1相始终保持稳定的数量和尺寸,θ″相随着时效的进行不断减少并且最终消失。力学性能随着析出相的种类和数量的不同而改变,T1相对合金起到了很好的强化效果,δ′相和θ′相的复合强化有效地改善了合金的力学性能,σ相对该合金的强化作用优于θ′相。     

自然时效对Al-Li-Cu-Mg-Zr合金的影响

采用透射电镜（TEM）和维氏硬度计详细研究淬火后与人工时效前的时间间隔（自然时效）对Al-Li-Cu-Mg合金的影响。研究发现,通过在人工时效前引入自然时效可以提高Al-2.4Li-1.16Cu-0.8Mg-0.1Zr(wt%）合金的硬度。合金硬度的增加主要来自于S相数量的增加和分布更均匀,在人工时效前引入自然时效对δ‘相的尺寸和分布没有影响,长时间的自然时效对合金的影响不大。     

Fe-Ni基合金中次生η相的析出机理

针对奥氏体合金中次生η相与基体位向关系存在的不同看法，研究了铁镍基奥氏体合金大量次生η相的析出机理，结果表明，η相与基体之间有良好的共格关系：{001}η／／{111}γ，（110）γ／／（210）η．晶界η相首先在一般无规晶界γ＇相处通过不全位错滑移产生堆垛层错带的方式形核，之后通过原子控制长程扩散机制的台阶方式在基体中长大，进入晶界另一侧与之匹配差的晶粒中，晶界随之一起迁动．η相的析出伴随着附近区域γ＇相的溶解和消失．     

三元青铜/环境界面上物质转移的化学行为

用模拟闭塞电池法(O.C.)研究了青铜在模拟环境介质0.028 mol·L-1NaCl 0.01 mol·L-1Na2SO4 0.016 mol.L-1NaHCO3中的局部腐蚀孔内或裂纹内的化学变化.通电32 h后闭塞区内溶液的Ph值由7.00降至5.02,与此同时Cl-和SO24-向闭塞区内迁移,其浓集倍数分别是6.31和2.93;测定了闭塞区内外Cu、Sn、Pb金属离子的浓度,据此计算出溶解因子fsn/Cu小于1,fpb/Cu大于 1,表明青铜中各元素选择性腐蚀的顺序为Pb＞Cu＞Sn,腐蚀速度Pb＞Cu＞Sn;用XRD分析了腐蚀产物的组成,解释了青铜文物表面腐蚀产物的分层现象,即从里到外为CuCl,CuCl和Cu2O,Cu的二价化合物.     

The effects of hydrostatic pressure on the ductility of metals and alloys

A law governing the change in the ductility of metals and alloys under pressure is given: $$\begin{gathered} \left( {\frac{P}{{\sigma _n }}} \right) = \tfrac{1}{2}\frac{1}{{\sigma _n }}\frac{{d\sigma }}{{d\varepsilon }}\{ \varepsilon _{local} (P)^{\tfrac{3}{2}} - \varepsilon _{local} (O)^{\tfrac{3}{2}} \} + \tfrac{1}{3}\frac{1}{{\sigma _n }}\frac{{d\sigma }}{{d\varepsilon }}\{ \varepsilon _{local} (P) - \varepsilon _{local} (O)\} + \hfill \\ {\text{ }} + \tfrac{1}{2}\{ \varepsilon _{local} (P)^{\tfrac{1}{2}} - \varepsilon _{local} (O)^{\tfrac{1}{2}} \} \hfill \\ \end{gathered}$$ where P is the hydrostatic pressure, ?_local is the strain accumulated from the start of necking to fracture, σ _n necking stress and (dσ/d?) the coefficient of linear work hardening. This relation is derived from a newly proposed criterion of ductile fracture, viz. “constancy of hydrostatic tensile stress”, which indicates that the change of ductility with pressure obeys a three halves power law. The observed increase in ductility of widely differing metals and alloys under pressure up to 10,000 kg/cm⁴ has confirmed that the proposed criterion is acceptable. It is further shown that the ductilities of some copper alloys with low stacking fault energy, such as Cu-Zn and Cu-Ge alloys, increases with pressure at the beginning but the increase stops at fairly low pressure, i.e. 3,500 ～ 4,000 kg/cm², and their ductilities become almost insensitive to the pressure applied. It is suggested that ductile fracture of metals with low stacking fault energy is dominated by a process which occurs not by the hydrostatic stress component but by shear stress only.     

Bend formability and strength of Cu–Be–Co alloys

The effects of addition of 0.01 and 0.03 wt% Mg on the bend formability and strength of a Cu–1.8 wt% Be–0.21 wt% Co alloy aged at 320 °C for 30 min have been investigated metallographically. The addition of Mg to the Cu–Be–Co alloy enhances the bend formability and strength of the alloy. The enhancement of strength is caused by the increase in volume fraction of g_\textI^￠ \gamma_{\text{I}}^{\prime } precipitates in the Cu matrix. In bending of the alloys with and without 0.01 and 0.03 wt% Mg, a number of micro necks first arise along grain boundaries, and part of them grows, resulting in surface wrinkles, which finally lead to surface cracking. The cracking is initiated from voids formed by destruction of bar-like γ precipitates in discontinuous precipitation (DP) cells and propagates along grain boundaries. The addition of Mg decreases the width of DP cells, resulting in better bend formability. This arises because smaller stress concentration due to less inhomogeneous deformation develops in cells and, as a result, destruction of the γ precipitates in cells occurs less easily as the cell width decreases.     

{\alpha^{\prime}}_{\text{H}} -Dicalcium silicate bone cement doped with tricalcium phosphate: characterization,bioactivity and biocompatibility

The influence of phosphorus doping on the properties of $ \alpha^{\prime}_{\text{H}} $ -dicalcium silicate (C₂S) bone cement was analyzed, in addition to bioactivity and biocompatibility. All the cements were composed of a solid solution of TCP in C₂S ( $ \alpha^{\prime}_{\text{H}} $ -C₂S_ss) as the only phase present. The compressive strength ranged from 3.8–16.3 MPa. Final setting times ranged from 10 to 50 min and were lower for cements with lower L/P content. Calcium silicate hydrate was the principal phase formed during the hydration process of the cements. The cement exhibited a moderate degradation and could induce carbonated hydroxyapatite formation on its surface and into the pores. The cell attachment test showed that the $ \alpha^{\prime}_{\text{H}} $ -Ca₂SiO₄ solid solution supported human adipose stem cells adhesion and spreading, and the cells established close contacts with the cement after 24 h of culture. The novel $ \alpha^{\prime}_{\text{H}} $ -C₂S_ss cements might be suitable for potential applications in the biomedical field, preferentially as materials for bone/dental repair.     

The role of protons in ionic diffusion in (Mg, Fe)O and (Mg, Fe)2SiO4

The presence of hydrogen dissolved within iron-magnesium oxides and silicates results in an increase in the rate of Fe–Mg interdiffusion. Experimental data and point defect models suggest that the increased interdiffusivity is due to an increase in the total metal-vacancy concentration through stabilization of proton-vacancy defect associates in a hydrous environment. In the case of (Mg_1–x Fe _x )O, interdiffusion experiments under hydrothermal conditions at a fluid pressure of ∼0.3 GPa yield similar dependencies of interdiffusivity on Fe-content, oxygen fugacity, and temperature as under dry conditions, but interdiffusion coefficients are a factor of ∼3 larger. These data suggest that the increased interdiffusivities in (Mg_1–x Fe _x )O result from incorporation of defect associates formed between a metal vacancy and a single proton, For (Mg_1–x Fe _x )₂SiO₄, interdiffusion under hydrothermal conditions over a range of fluid pressures reveals a significant difference in the dependence of interdiffusivity on Fe content than obtained under dry conditions, combined with a strong dependence on water fugacity. These data indicate that the increased diffusivities in (Mg_1–x Fe _x )₂SiO₄ result from incorporation of defect associates involving a metal vacancy and 2 protons, It is anticipated that, at higher water fugacities, Fe–Mg interdiffusion in both materials will become dominated by these latter defects and that the interdiffusivity will increase linearly with water fugacity but will be independent of oxygen fugacity and iron concentration.

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Dynamics of Rotating Two-phase System Under Transversal Vibration

Mean dynamics of light granular matter in liquid in the rotating horizontal cylinder subjected to transversal vibrations is experimentally investigated. The excitation of outstripping and lagging azimuth motion of the interface with respect to the cavity is revealed at definite ratios of rotation and vibration frequencies ${\Omega _\upsilon } \mathord{\left/ {\vphantom {{\Omega _\upsilon } {\Omega_r }}} \right. \kern-0em} {\Omega _r }$ . The motion is generated by the inertial oscillations arising in the system in a resonant way. The formation of regular spatial structures on the interface is revealed at intensive outstripping motion. These structures have azimuth and axial periodicity and their shape depends on the type of inertial waves arising in the cavity. Intensity and direction of azimuth flows as well as shape of patterns on the granular matter–liquid interface are determined by the ratio $ {\Omega _\upsilon } \mathord{\left/ {\vphantom {{\Omega _\upsilon } {\Omega _r}}} \right. \kern-0em} {\Omega _r }$ . It is shown, that the lagging motion exists at $ {\Omega _\upsilon } \mathord{\left/ {\vphantom {{\Omega _\upsilon } {\Omega _r }}} \right. \kern-0em} {\Omega _r }<1$ , and the outstripping one exists at $ {\Omega _\upsilon } \mathord{\left/ {\vphantom {{\Omega _\upsilon } {\Omega _r }}} \right. \kern-0em} {\Omega _r }>1 $ . Combined action of vibrations and rotation provides an efficient mechanism of mass transfer control, the intensity of mean flows in the cavity frame can be of the same order of magnitude as the rotation velocity.     

Fabrication and characterization of iron and fluorine co-doped BST thin films for microwave applications

The effects of fluorine co-doping by means of a post-thermal annealing process of iron-doped BST thin films in a fluorine-containing atmosphere have been investigated. XPS and ToF-SIMS sputter depth profiling verified a homogeneous fluorine distribution in the thin films. By employing EPR, it was shown that singly charged ( $ {\text{Fe}}_{\text{Ti}}^{\prime } $ – $ {\text{V}}_{\text{O}}^{ \cdot \cdot } $ )^· defect complexes, as well as ‘isolated’ $ {\text{Fe}}_{\text{Ti}}^{\prime } $ centres with a distribution of $ {\text{F}}_{\text{O}}^{ \cdot } $ sites in remote coordination spheres exist in the fluorinated films. Tunability enhancement due to fluorine co-doping as well as a Q-factor enhancement due to iron doping is demonstrated.     

Effect of Al content on the microstructure and mechanical behavior of two-phase FeNiMnAl alloys

The effects of varying the Al content in the range of 11–15 at.% on the microstructure and room-temperature mechanical properties of lamellar-structured FeNiMnAl alloys with compositions close to Fe₃₀Ni₂₀Mn₃₅Al₁₅ have been studied, and the temperature dependence of the yield strength of one composition, i.e., Fe₃₆Ni₁₈Mn₃₃Al₁₃, has been investigated. All alloys consisted of B2 and fcc phases. Decreasing the Al content initially (13 and 14 at.% Al) led to marked increases in both the fcc phase fraction and fcc lamellar spacing, λ, but, on further reducing the Al content (11 and 12 at.% Al), the lamellar structure was no longer present. The elongation to fracture of the FeNiMnAl alloys increased with the decreasing Al concentration from 6.5 % at 15 at.% Al to 31.1 % at 11 at.% Al with a concomitant decrease in the yield stress from 820 to 255 MPa. For the lamellar-structured alloys, the yield stress, σ _y, obeyed a Hall–Petch-type relationship with λ, i.e., $ \sigma_{y } = \sigma^{\prime}_{0} + k^{\prime}\lambda^{ - 1} $ , where $ \sigma^{\prime}_{0} $ is the lattice resistance, and k′ is a constant. The compressive yield stress of Fe₃₆Ni₁₈Mn₃₃Al₁₃ was found to be independent of temperature up to 700 K, after which it decreased dramatically because of the softening of the B2 phase. All alloys showed ductile fracture modes.     

Influence of pH and bath composition on properties of Ni–Fe alloy films synthesized by electrodeposition

Fe?CNi films were electrodeposited on ITO glass substrates from the electrolytes with different molar ratio of Ni $^{\boldsymbol{2+}}$ /Fe $^{\boldsymbol{2+}}$ and different pH values (2 $\boldsymbol{\cdot}$ 1, 2 $\boldsymbol{\cdot}$ 9, 3 $\boldsymbol{\cdot}$ 7 and 4 $\boldsymbol{\cdot}$ 3) at 25 $\boldsymbol{^\circ}$ C. The properties of Fe?CNi alloy films depend on both Ni $^{\boldsymbol{2+}}$ and Fe $^{\boldsymbol{2+}}$ concentrations in electrolyte and pH values. The content of Ni increases from 38% to 84% as the mole ratio of NiSO $_{\boldsymbol{4}}$ /FeSO $_{\boldsymbol{4}}$ increasing from 0 $\boldsymbol{\cdot}$ 50/0 $\boldsymbol{\cdot}$ 50 to 0 $\boldsymbol{\cdot}$ 90/0 $\boldsymbol{\cdot}$ 10 in electrolyte and slightly decreases from 65% to 42% as the pH values increase from 2 $\boldsymbol{\cdot}$ 1 to 4 $\boldsymbol{\cdot}$ 3. The X-ray diffraction analysis reveals that the structures of the films strongly depend on the Ni content in the binary films. The magnetic performance of the films shows that the saturation magnetization ( $\boldsymbol{M}_{\boldsymbol{\rm s}})$ decreases from 1775 $\boldsymbol{\cdot}$ 01 emu/cm $^{\boldsymbol{3}}$ to 1501 $\boldsymbol{\cdot}$ 46 emu/cm $^{\boldsymbol{3}}$ with the pH value increasing from 2 $\boldsymbol{\cdot}$ 1 to 4 $\boldsymbol{\cdot}$ 3 and the saturation magnetization ( $\boldsymbol{M}_{\boldsymbol{\rm s}})$ and coercivity ( $\boldsymbol{H}_{\boldsymbol{\rm c}})$ move up from 1150 $\boldsymbol{\cdot}$ 44 emu/cm $^{\boldsymbol{3}}$ and 58 $\boldsymbol{\cdot}$ 86 Oe to 2498 $\boldsymbol{\cdot}$ 88 emu/cm $^{\boldsymbol{3}}$ and 93 $\boldsymbol{\cdot}$ 12 Oe with the increase of Ni $^{\boldsymbol{2+}}$ concentration in the electrolyte, respectively.