微粒撞击高参数汽轮机调节级喷嘴壁面特性研究

固体颗粒冲蚀严重影响超常参数汽轮机调节级喷嘴寿命.本文根据相似理论并借助PIV技术,进行了三种喷嘴内固体微粒运动特性及其材料抗冲蚀特性的试验研究,并通过三维数值模拟进一步研究了单一参数变化对粒子运动特性的影响.发现同一粒子再次撞击角度比初次撞击角度平均小5°～15°;约45%～80%的粒子撞击在离喷嘴出口边约15%的区域;粒子对前加载型线喷嘴有更严重的冲蚀,可以预测采用合适型线的后加载喷嘴或缩短喷嘴宽度能有效降低粒子冲蚀.     

安装角对旋转翼型结冰分布影响实验研究

为开展风力机叶片翼型在旋转状态下不同安装角表面结冰分布规律的研究,基于自行设计建造的一种利用自然低温的结冰风洞试验系统,完成了对称翼型NACA0018在0°、10°及20°三种安装角下的结冰风洞试验,试验中选取了200 r/min、400 r/min及600 r/min三种转速,选取了6 m/s及8 m/s两种风速,并利用高速摄像机获得了叶片表面的结冰分布,拍摄时间分别设定为15 min、30 min、45 min及60 min。利用前期研究提出的一种不规则冰形评价方法,对不同工况下叶片表面的结冰冰形进行了定量分析,利用相对迎风面与绝对迎风面定性分析了不同安装角对叶片表面的结冰区域的影响。研究结果表明,安装角对叶片表面的结冰分布影响较大,同一工况下不同安装角的叶片表面结冰有较大差异,转速也是影响结冰的关键因素,而风速对结冰分布的影响较小。本研究可为风力机叶片防/除冰技术提供参考。     

三轴振动激励下悬挂座椅垂向传递率试验研究

针对三轴激励下无源空气弹簧悬挂座椅垂向振动传递特性进行了试验研究。其中,垂向激励幅值设置为0.25 m/s²r.m.s.、0.5 m/s² r.m.s.或1.0 m/s² r.m.s.,纵向和横向激励幅值同为0 m/s² r.m.s.、0.5 m/s² r.m.s.或1.0 m/s² r.m.s.;座椅靠背倾角设置为0°、10°或20°。研究表明,垂向和水平方向振动激励幅值的增加均引起悬挂座椅传递率共振频率的降低,并影响座椅有效幅值传递率;在较小幅值(0.25 m/s² r.m.s.)的垂向振动激励下,靠背倾角对该共振频率也有一定影响。此外,垂向和水平振动幅值对座椅传递率的影响存在轴间耦合效应,当垂向振动的幅值增大时,水平振动幅值从0.25 m/s² r.m.s.增大到1.0 m/s²r.m.s.所造成的传递率峰值的变化程度将减小,反之亦然。     

含尘流透平叶片冲蚀的数值分析

本文在含尘流透平叶片流道内气固两相流动数值模拟的基础上,发展了叶片冲蚀的数值分析方法,提出了便于工程应用的有限区域内质量加权、面积平均的冲蚀率统计分布计算方法;对建造中的江苏徐州贾旺增压流化床联合循环中试电站燃气轮机叶片冲蚀问题进行了数值模拟,给出了计算结果的数据图象资料,就叶片冲蚀状况进行了分析。     

飞秒激光冲击AZ31B镁合金过程的数值模拟

采用有限元分析法对飞秒激光冲击AZ31B镁合金进行数值模拟,研究了激光冲击处理对镁合金变形过程的影响,分析了单脉冲激光冲击下材料内部的位移、动能、应力和应变的分布情况,得到了材料的瞬态速度和应变率变化过程.仿真结果表明,单脉冲飞秒激光冲击镁合金产生的塑性变形,可在材料表面形成微米级凹坑,中心点处最大位移为34μm,最大变形速度390m/s;在冲击初期,材料表面的应力和应变主要分布在冲击区域中心节点和边缘附近,并且得到镁合金的最大应力和最大应变率分别为955 MPa和1.8×106 s-1.研究结果能够为深入分析飞秒激光与镁合金作用时材料变形参量的变化规律提供数值理论依据.     

铜粉末动态压缩行为的多颗粒有限元分析

颗粒金属材料的宏观力学性能与其细观特性密切相关,金属粉末的冲击压缩问题有待深入研究。选用实验结果较为丰富的铜粉末作为研究对象,基于多颗粒有限元法建立了颗粒金属材料的二维数值分析模型,研究了铜粉末在冲击压缩下的力学行为。数值计算结果表明,在较高速度冲击下颗粒金属材料呈现出高度局部化的变形带,变形带如同冲击波一样从冲击端向支撑端传播。利用速度场计算方法,计算得到了塑性冲击波波阵面的位置,进而获得了不同孔隙率(0.25～0.60)铜粉末的粒子速度与冲击波波速之间的Hugoniot关系,其在较高冲击速度(200～300 m/s)下与实验结果吻合较好。发展了以动态锁定应变为唯一参数的冲击波模型,较好地表征了铜粉末在较高速度冲击下的Hugoniot关系和波后应力。     

SPH方法在宽速域岩石侵彻问题中的应用

采用光滑粒子流体动力学(SPH)方法对花岗岩靶板受碰撞侵彻的大应变、高应变率变形问题进行了数值模拟。为了描述弹目材料的非线性变形及破坏特性,对花岗岩靶板引入了Holmquist-Johnson-Cook(HJC)本构模型及损伤模型,对弹体引入含损伤的Johnson-Cook(J-C)本构方程和Grüneisen状态方程,靶板与弹体均离散成拉格朗日粒子。通过自编程序仿真计算0～4 m/s的着靶速度下花岗岩靶板的三维侵彻过程,对比分析了钢珠在不同弹体条件下的侵彻结果,在固体侵彻、半流体侵彻和流体侵彻的区域内拟合了侵彻深度随着靶速度的变化曲线。数值计算结果显示,侵彻深度随着靶速度的增加在固体侵彻区间(v01421 m/s)呈现递增趋势,在半流体侵彻区间(1421 m/s?v0?1700 m/s)呈现递减趋势,在流体侵彻区间(v0 1700 m/s)呈现递增趋势并逐渐趋于平滑,达到峰值。     

316不锈钢在含沙两相射流中长时间冲蚀的实验研究

采用含沙射流对316不锈钢进行了20 h以上的长时间冲蚀行为研究。对三个不同冲击角度下不锈钢的质量损失和表面形貌进行了研究和分析。结果表明,冲击角度为90°时,不锈钢的质量损失最大,冲击角度为60°时,不锈钢的质量损失最小。在90°连续冲击18 h之后,不锈钢质量损失趋于平缓,几乎不再发生变化;而在75°和60°连续冲击28 h后不锈钢的质量损失仍然呈上升趋势。SEM结果表明,90°冲击下的样品表面出现多个冲击坑,75°冲击下样品表面出现划痕,60°冲击下样品表面出现的刮痕较多且较长,这与不同冲击角度时不同的磨损机理有关。冲击角较大时,石英砂颗粒对材料的破坏机理是以正碰为主,冲击角较小时,颗粒对材料的破坏机理则是犁削作用。     

窗口声阻抗对锆相变动力学的影响

基于磁驱动加载装置CQ-4开展了锆的斜波压缩相变实验,研究了锆样品后表面窗口声阻抗对相变波形的影响.实验结果显示,锆后表面为较低声阻抗窗口(自由面和LiF窗口)时,相变起始对应的特征粒子速度约331.0 m/s,而高阻抗蓝宝石窗口时,特征粒子速度约301.9 m/s,特征速度对应的压力从约9.14 GPa下降到8.27 GPa.相变对应的速度特征拐点是与多种因素相关的实验信息,因此它对应的压力并不是材料属性参数相变压力.结合基于热力学Helmholtz自由能的多相状态方程和非平衡相变动力学方程开展了锆的相变动力学数值模拟研究,相变弛豫时间为30 ns,计算结果与三种情况的实验结果符合良好,可以较好地模拟斜波压缩下锆的弹塑性转变、相变等物理过程.在压力-比容和温度-压力热力学平面,相变前锆的准等熵线与冲击绝热线差异很小,相变后准等熵线都位于冲击绝热线下方,随着压力的增加准等熵线和冲击绝线偏差越来越大,温度-压力平面中在20 GPa时相差约100 K.相变开始后,由于相变引起比容的间断,导致锆的拉氏声速迅速下降约7%,相变完成后拉氏声速恢复到体波声速.     

冲击波加热的氩气的发射光谱

为了研究弱冲击条件下氩气的辐射特性,从二级轻气炮发射的89 W飞片以2.00 km/s的速度撞击封装有常态下氩气的LY12铝靶,用六通道瞬态高温计和示波器记录到受一次冲击压缩的氩气的光辐射信号随时间的变化规律:从405 nm到700 nm的5个通道信号为直线段,800 nm通道的信号为指数曲线段,并测量出相应的冲击波速度为4.10±0.09 k m/s.实验表明,冲击压缩的氩气对可见光的吸收系数较小,气体的光学厚度沿长波方向从光学薄向光学厚转变.二次冲击压缩氩气的辐射信号上升前沿的时间分辨光谱用OMA系统记录,并观察到450 nm附近有较强的发射光谱带,但没有观察到明显的线状光谱.通过冲击波后参数和氩气电离度的理论计算,解释了冲击压缩下氩气的发射光谱特性.     

Investigation on ultrasonic cavitation erosion of TiMo and TiNb alloys in sulfuric acid solution

Two kinds of Ti-alloys, i.e., TiMo and TiNb alloys are manufactured in this paper, and their ultrasonic cavitation erosion behaviors in 0.1 M H₂SO₄ solution are evaluated by the mean depth erosion (MDE), SEM and white light photograph. The results show that MDE of TiMo and TiNb alloys obviously increase with increasing the cavitation erosion time, however, they evidently decrease with the increment of Mo or Nb content at each fixed cavitation erosion time, and even some large blank areas (uneroded areas) still exist on the sample surface after ultrasonic cavitation erosion for 2 h in the case of Ti10Mo and Ti20Nb samples, implying the enhanced anti-cavitation erosion property of Ti-alloy by adding Mo or Nb element. The MDE of Ti10Mo or Ti20Nb sample is lower than that of TC4 sample in the case of each cavitation erosion time, indicating the better cavitation erosion resistance of of Ti10Mo or Ti20Nb sample. The influences of Mo and Nb on the passivity of TiMo and TiNb alloys during the ultrasonic cavitation erosion are detected by potentiodynamic curves. The results display that Ti, TC4, TixMo (x = 1, 5, 10) and TixNb (x = 5, 10, 20) samples are all almost in the passive state within the potential region from 0V_SCE to 1.5V_SCE during ultrasonic cavitation erosion, and the passive current density evidently decreases with increasing Mo or Nb content, indicating the enhanced passive characteristic by adding Mo or Nb alloys during the ultrasonic cavitation erosion.     

高密度等离子体融断开关融蚀现象的粒子模拟研究

 利用自行研制的2.5维全电磁柱坐标粒子模拟程序对高密度等离子体融断开关融断区域中的融蚀现象进行了模拟研究,详细地介绍了计算模型的建立以及复杂边界的算法处理。模拟结果表明在融断开关导通电流的最后阶段,由于磁压力、磁场渗透作用和非中性静电融蚀作用,在融断区域的阴极附近会形成一定宽度的真空鞘层。由于等离子体密度的下降以及初始真空鞘层的存在,使得即使只有较小的离子电流,融蚀机制也完全可以导致PEOS最终断开。     

气体火花开关电极烧蚀研究

采用Mo,WCu和W分别作为三种气体火花开关的主电极材料,进行放电条件下电极烧蚀实验,研究开关电极烧蚀率和烧蚀形貌,分析电极烧蚀特征。结果表明,Mo,WCu和W开关的主电极烧蚀率分别为3.32×10-2 C-1·m-2,2.63×10-2 C-1·m-2和1.74×10-2 C-1·m-2,W开关主电极烧蚀率最小。实验后开关的主电极中心烧蚀严重,呈现明显裂纹和烧蚀坑。Mo主电极表面呈现明显熔融态,阴极表面形成大量裂纹(宽度达10μm)和孔隙(孔径达10μm);WCu和W主电极表面形成少量圆球状W突起(粒径达20μm及以上)。开关外壳内壁沉积了喷溅颗粒。WCu开关外壳沉积颗粒较大(粒径达10μm),Mo开关外壳沉积颗粒居中(粒径为2μm),W开关外壳沉积颗粒最小(近1μm)。因此可优先选用具有优异抗烧蚀性能的W作为气体火花开关电极材料。     

Effect of pearlitic morphology with varying fineness on the cavitation erosion behavior of eutectoid rail steel

The present work discusses the effect of the pearlitic morphology with varying fineness on the cavitation erosion behavior of eutectoid rail steel. Cavitation erosion of three different types of the pearlitic steels (furnace-cooled, air-cooled, and forced-air-cooled) consisting of coarse, fine, and very fine microstructures were tested in 3.5% NaCl solution and compared with that of the as-received pearlitic rail steel. The variation in the mean depth of erosion (MDE) and mean depth erosion rate (MDER) with erosion time was analyzed. Furthermore, the cavitation erosion resistance of the as-received, the air-cooled, and the forced-air-cooled was found to be 1.03, 1.51, and 2.14 times better than the furnace-cooled pearlitic steel, respectively. It was concluded that the cavitation erosion resistance of the pearlitic steel increased with the increase in the fineness of the microstructure.     

Mechanical erosion by flowing lava

Hot lava is a viscous fluid that, driven by gravity, moves along the Earth's surface. Intuitively, one attributes constructional properties to lava–it accumulates in volcanic landforms, compound lava fields and, in the end, entire mountains. On the other hand, there are also examples of the erosive power of lava: on Earth and especially on other planets in the Solar System, there exist channels incised by flowing lava. The origins of these erosive features have long been debated among volcanologists and planetologists. The dominant paradigm is thermal erosion, although it leaves many questions open. After the 2001 eruption on Mount Etna we found a lava channel whose features cannot be explained in the frame of thermal erosion. On the basis of our observations, we have developed a model for mechanical erosion that explains the main field observations, and opens alternative ways to describe erosion by flowing lava.     

Erosion craters on Ti3SiC2 anode

The erosion behavior of pure Ti₃SiC₂ anode under vacuum discharge was investigated. By means of X-ray diffraction, energy dispersive spectroscopy and micro-Raman spectroscopy, the decomposition of Ti₃SiC₂ into nonstoichiometric TiC_x, amorphous carbon and other by-products was proved. The surface morphology was revealed by scanning electron microscope and 3D super depth digital microscope. Different kinds of craters with diameters varying from a few microns to a few hundred microns were observed on the anode surface after arcing. The smaller craters contain some TiC_x, with a few tens of microns in diameter, are flower-like shaped with a protrusion pointing out from the center of the crater bottom. The larger craters are basically composed of TiC_x, have diameters greater than one hundred microns but without the central protrusions, and are surrounded by collapse-fissures.     

Experiment investigation on effects of elastic modulus on cavitation erosion of silicone rubber

Research into cavitation phenomena in various fields shows that the elastic modulus of a boundary has a potential impact on cavitation erosion. To obtain the direct relationship between the elastic modulus of the boundary and cavitiation erosion, single-layer samples with different chemical composition and moduli, and double-layer samples with different elastic moduli and the same surface layer material, were prepared with silicone rubber. The results of cavitation experiments on single-layer samples, show that the coating chemical composition and mechanical properties together affect the cavitation morphology of the coating, and dominant factors vary with erosion stage. Through the cavitation test of double-layer samples, it was found that there is a positive correlation between the elastic modulus of the coating and the degree of cavitation. This study helps us to understand the relationship between coating elastic modulus and cavitation more directly, and provides theoretical and technical guidance for the application of anti-cavitation for elastic coating in engineering.     

Cavitation erosion by shockwave self-focusing of a single bubble

The ability of cavitation bubbles to effectively focus energy is made responsible for cavitation erosion, traumatic brain injury, and even for catalyse chemical reactions. Yet, the mechanism through which material is eroded remains vague, and the extremely fast and localized dynamics that lead to material damage has not been resolved. Here, we reveal the decisive mechanism that leads to energy focusing during the non-spherical collapse of cavitation bubbles and eventually results to the erosion of hardened metals. We show that a single cavitation bubble at ambient pressure close to a metal surface causes erosion only if a non-axisymmetric energy self-focusing is at play. The bubble during its collapse emits shockwaves that under certain conditions converge to a single point where the remaining gas phase is driven to a shockwave-intensified collapse. We resolve the conditions under which this self-focusing enhances the collapse and damages the solid. High-speed imaging of bubble and shock wave dynamics at sub-picosecond exposure times is correlated to the shockwaves recorded with large bandwidth hydrophones. The material damage from several metallic materials is detected in situ and quantified ex-situ via scanning electron microscopy and confocal profilometry. With this knowledge, approaches to mitigate cavitation erosion or to even enhance the energy focusing are within reach.     

First Monte-Carlo modelling of global beryllium migration in ITER using ERO2.0

ERO2.0 is a recently developed Monte-Carlo code for modelling global erosion and redeposition in fusion devices. We report here on the code's application to ITER for studying the erosion of the beryllium (Be) first wall armour under burning plasma steady state diverted conditions. An important goal of the study is to provide synthetic signals for the design of two key diagnostics: the main chamber visible spectroscopy and the laser in-vessel viewing systems. The simulations are performed using toroidally symmetric plasma backgrounds obtained by combining SOLPS simulations extended to the wall using the OSM-EIRENE-DIVIMP edge code package. These are then further combined with a shadowing model using magnetic field line tracing to provide a three-dimensional correction for the flux patterns. The resulting plasma wetted area, which amounts to ∼10% of the total first wall area, is in excellent agreement with shadowing calculations obtained with the SMITER field line tracing code. The simulations reveal that the main Be erosion zones are located in regions intersected by the secondary separatrix, in particular the upper Be panels, which are close to the secondary X-point. For the particular high-density Q = 10 background plasma case studied here, ∼80% of the eroded Be is found to re-deposit on main chamber surfaces. The rest migrates in almost equal parts to the inner and outer divertor and is deposited close to the strike lines.