深过冷

摘要： 目的研究过冷Ni-0.5%Pb(原子数分数)合金过冷组织的演化行为,阐明其组织演化和晶粒细化的基本机制。方法采用熔融玻璃净化和循环过热方法制备出过冷度为0~255 K的试样,并结合枝晶生长的动力学-热力学模型,研究其深过冷快速凝固行为机制。结果在0~255 K过冷度范围内,随着过冷度的增大,Ni-Pb偏晶合金的微观组织发生了2类晶粒细化现象,组织形态由粗大树枝晶向粒状等轴晶转变。结论第1类粒状晶的形成是由于枝晶熟化和再辉重熔导致发达枝晶破碎,第2类粒状晶的形成是由于在应力和应变能的作用下,枝晶碎变和再结晶引起了晶粒细化。

摘要： 本文采用自由落体技术模拟空间环境条件,实现了液滴直径144~1530µm的Mo-48%Ni合金的微重力快速凝固与组织调控.理论计算表明,液态合金的冷却速率和过冷度均随液滴直径减小而指数增大,分别可达2.41×10^(4) Ks^(−1)和322 K(0.19 T_(L)).实验发现,快速凝固组织由初生NiMo枝晶和(Ni+NiMo)共晶构成,急冷条件抑制了后续固态相变.随着液滴冷速和过冷度增大,粗大的NiMo枝晶逐渐细化,溶质Ni含量呈现先减小再增大的变化趋势;共晶形貌由规则层片转变为非规则组织,其中溶质Mo的含量先增大再减小.初生相和共晶组织的弹性模量均单调递减;初生相显微硬度先缓慢增大后减小,共晶组织显微硬度整体呈现出递减的规律.同时,合金磁化强度减小,但其矫顽力增大,耐温性能得到显著提升.

摘要： 利用静电悬浮实验技术研究Zr熔体的深过冷和枝晶生长动力学机制,并测定了液态Zr的密度、黏度和表面张力等热物理性质.结果表明:液态Zr的超过冷临界过冷度为524 K(0.25Tm),平均比热为41.03 J/(mol?K).基于热平衡方程测定出液态Zr在1752～2315 K温度区间内的辐射率随温度升高而增大,熔点处其值为0.312.液态Zr的密度、黏度和表面张力均随温度降低呈上升趋势.同时,通过高速CCD摄像方法测得纯Zr的枝晶生长速度随过冷度以幂函数形式增大,在最大过冷度376 K(0.18Tm)处,枝晶生长速度达到48 m/s.此外对其凝固组织的研究发现,随着过冷度的增大,纯Zr的凝固组织显著细化且趋于均匀,微观硬度也随之增高.

摘要： 三元共晶凝固过程涉及三个固相在同一液相中的竞争形核和协作生长,可以形成丰富多样的凝固组织,对发展原位复合材料制备技术和研究自发模式形成现象都具有重要的意义.空间环境中的微重力和无容器效应消除了重力引起的对流、 沉降以及器壁引起的异质形核,为深入研究非平衡快速凝固规律提供了理想的实验条件.由于空间实验机会十分难得,人们发展了自由落体、 悬浮、 抛物飞行、 探空火箭等多种空间环境的地面模拟方法,部分的或一定程度的实现空间的微重力和无容器效应.对国内外采用浸浮净化、 落管、 超声悬浮等地面模拟方法开展的三元共晶合金凝固研究工作进行了综述,并对未来发展趋势进行了展望.%The solidification of ternary eutectic alloys involves competitive nucleation and cooperative growth of three solid phases in the same mother liquid phase, which generates plenty of microstructural morphologies.This is of importance for the methodological exploration of in situ composite material preparation as well as theoretical study of pattern formation phenomena. The microgravity effect and containerless state in space environment eliminate the convection and buoyancy induced by gravity,and avoid the heterogeneous nucleation originated from container walls, providing an ideal experimental condition for rapid solidification of metastable melts.Because of the extremely rare opportunity for space experiment, various ground based approaches (e.g.free fall, levitation, parabolic flight, and sounding rocket) are developed to achieve the microgravity and containerless effects to a certain degree .This paper reviews the recent progress of ternary eutectic solidification researches that are performed with ground simulation methods such as glass fluxing, drop tube, and acoustic levitation.The prospective developing trends are also discussed.

摘要： 采用落管自由落体方法实现了Ni45Fe40Ti15合金在微重力无容器条件下的快速凝固,获得了直径介于160—1050μm的合金液滴.理论计算表明冷却速率及过冷度随液滴直径减小而增大,并呈指数函数关系,实验获得的最大过冷度为210 K(0.14 TL).随着过冷度增大,凝固组织中粗大的γ-(Fe,Ni)枝晶逐渐细化,二次枝晶间距减小,溶质Ti在γ-(Fe,Ni)相中的固溶度显著扩展.对不同直径合金液滴的凝固样品进行磁学性能分析,结果表明随着凝固合金液滴直径减小,其饱和磁化强度增大,矫顽力减小,矩形比下降,软磁性能明显提高.%Ni-Fe-Ti ternary alloys, as a type of structural and magnetic material, have received more attention in the industrial fields in recent decades. For the purpose of providing necessary experimental data and theoretical basis for industrial appliance of these alloys, the researches of rapid solidification mechanism and relevant application performances of Ni45Fe40Ti15 ternary alloy are carried out in this paper. Rapid solidification of undercooled Ni45Fe40Ti15 ternary alloy is realized in a 3 m drop tube under the condition of containerless and microgravity state. In an experiment, the sample with a mass of 2 g is placed in aΦ16 mm × 150 mm quartz tube with a 0.3-mm-diameter nozzle at its bottom. The quartz tube is then installed in the induction coil on the top of the drop tube. The tube body is evacuated to a pressure of 2 × 10?5 Pa and backfilled with the mixture gas of Ar and He gases to about 1 × 105 Pa. After that the sample is melted by induction heating and superheated to about 200 K above its liquidus temperature. Under such a condition, the melt is ejected through the nozzle by a flow of Ar gas and dispersed into fine liquid droplets. These liquid droplets solidify rapidly during free fall, and the droplets with the diameters ranging from 160 to 1050 μm are achieved. As droplet diameter decreases, both cooling rate and undercooling of the alloy droplet increase exponentially, i.e., from 1.10 × 103 to 3.87 × 104 K·s?1 and from 42 to 210 K (0.14TL) respectively. The microstructure consists ofγ-(Fe, Ni) solid solution and interdendritic Fe2Ti intermetallic compound. As undercooling increases, the coarseγ-(Fe, Ni) dendrites become refined, the secondary dendrite arm spacing linearly decreases. Compared with the result in the glass fluxing experiment, the dendrites are much refined by drop tube processing due to the higher cooling rate obtained. The amounts of solute Ni and Ti content in the γ-(Fe, Ni) phase enlarge evidently with the increase of undercooling, suggesting the occurrence of solute trapping. The magnetic properties of thealloy droplets sre also analyzed. When droplet diameter decreases from 1100 to 300 μm, the saturation magnetization increases from 22.47 to 41.82 Am2·kg?1, the coercive force decreases from 3.33 to 0.80 KAm?1, and the squareness ratio decreases approximately by four times. This indicates that the soft magnetic properties of the alloy are improved remarkably by drop tube processing. Furthermore, the mechanism for substantial effect of undercooling on magnetic parameter such as coercive force needs to be further investigated.

摘要： 基于轴对称电磁悬浮模型,理论计算了二元Fe50 Cu50合金熔体内部的磁感应强度和感应电流,分析了其时均洛伦兹力分布特征,进一步耦合Navier-Stokes方程组计算求解了合金熔体内部流场分布规律.计算结果表明,电磁悬浮状态下合金内部流场呈现环形管状分布,并且电流强度、电流频率或合金过冷度的增加,均会导致熔体内部流动速率峰值减小,平均流动速率增大,并使流动速率大于100 mm·s?1区域显著增大.通过与静态凝固实验对比发现,电磁悬浮条件下熔体中强制对流使得合金内部富Fe和富Cu区的相界面呈波浪状起伏形貌,并且富Cu相颗粒在熔体上部分出现的概率增加.%In the electromagnetic levitation experiment, the liquid flow in the undercooled liquid alloy remarkably affects the relevant thermodynamic property measurement and solidification microstructure. Therefore, it is of great importance to understand the fluid convection inside the undercooled melt. Theoretical calculation and electromagnetic levitation experiment have been used to investigate the internal velocity distribution and rapid solidification mechanism of Fe50Cu50 alloy. Based on axisymmetric electromagnetic levitation model, the distribution patterns of magnetic flux density and inducted current for levitated Fe50 Cu50 alloy are calculated together with the mean Lorenz force. The Navier-Stokes equations are further taken into account in order to clarify the internal fluid flow. The results of the theoretical calculation reveal that the fluid velocity within levitated melt is strongly dependent on three factors, i.e., current density, current frequency and melt undercooling. As one of these factors increases, the maximum fluid velocity decreases while the average fluid velocity increases. Meanwhile, the area with fluid velocity larger than 100 mm·s?1 is significantly extended. Furthermore, the fluid flow within levitated melt displays an annular tubular distribution characteristic. The Fe50Cu50 alloy melt is undercooled and solidified under electromagnetic levitation condition. In this undercooling regime ?T <69 K, solidification microstructures are composed of dendrites, and a morphology transition of "coarse dendrites →refined dendrites" is observed with the increase of melt undercooling. Comparing with the critical undercooling of metastable liquid phase separation in the glass fluxing experiment, the forced flow within the Fe50Cu50 alloy melt has suppressed phase separation substantially. Once the undercooling attains a value of 150 K, metastable phase separation leads to the formation of layered pattern structure consisting of floating Fe-rich zone and sinking Cu-rich zone. A core-shell macrosegregation morphology with the Cu-rich zone distributed in the center and outside of the sample and Fe-rich zone in the middle occurs if the undercooling increases to 204 K. With the enhancement of undercooling after phase separation, the grain size of α-Fe dendrites in Cu-rich zone presents a decreasing trend. In contrast to the phase separated morphology of Fe50Cu50 alloy under the glass fluxing condition, the phase separated morphologies show obviously different characteristics. In such a case, the forced convection induced by electromagnetic stirring results in the formation of wavy interface between Fe-rich and Cu-rich zones, the distorted morphology of the Cu-rich spheres distributed in the Fe-rich zone, and the increased appearance probabilities of Cu-rich spheres at the upper part of electromagnetically levitated sample. Experimental observations demonstrate that the distribution pattern of Cu-rich spheres in Fe-rich zone is influenced by the tubular fluid flow inside the melt.

摘要： Eutectic phase transition involves the competitive nucleation and coupled growth of two solid phases within one liquid phase. Phase selection especially under unequilibrium condition, may result in novel microstructures and thus affects the performances of eutectic alloys. Liquid Cu-10 wt.%Zr hypoeutectic, Cu-12.27 wt.%Zr eutectic and Cu-15 wt.%Zr hypereutectic alloys are rapidly solidified in the containerless process in a 3 m drop tube. During the experiments, the Cu-Zr alloys are heated by induction heating in an ultrahigh vacuum chamber and further overheated to 200 K above their liquidus temperatures for a few seconds. Then the liquid alloys are ejected out from the small orifice and dispersed into tiny droplets after adding the argon gas flow. The solidified samples are analyzed by Phenom Pro scanning electron microscope and HXD-2000 TMC/LCD microhardness instrument. The competitive nucleation and growth among (Cu) dendrite, Cu9Zr2 dendrite and (Cu+Cu9Zr2) eutectic phase become more and more intensive as droplet diameter decreases. The layer spacing in Cu-12.27 wt.% Zr eutectic alloy decreases when the undercooling increases. And the microstructural transition takes place from lamellar eutectic to anomalous eutectic. The microstructure of Cu-10 wt.% Zr hypoeutectic alloy is characterized by (Cu) dendrite and lamellar eutectic. Whereas the microstructure in Cu-15 wt.%Zr hypereutectic alloy consists of Cu9Zr2 dendrite and lamellar eutectic. For the Cu-10 wt.%Zr hypoeutectic alloy, with the decrease of droplet size, the primary (Cu) phase transforms from coarse dendrites into equiaxed grains, and the volume fraction of (Cu) dendrite becomes larger and larger. As for Cu-15 wt.% Zr hypereutectic alloy, the primary Cu9Zr2 intermetallic compound grows in a band manner, and with the decrease of droplet size and increase of cooling rate, the solidified microstructure transforms from band Cu9Zr2 dendrite plus lamellar eutectic into spherical cell structure. The three alloys reach maximal undercooling at 177 K, 156 K and 204 K, respectively. The Trivedi-Magnin-Kurz and Lipton-Kurz-Trivedi/Boetinger-Coriell-Trivedi models are used to analyze the dendritic and eutectic growth as a function of undercooling. Theoretical analysis indicates that both dendritic growth and eutectic growth are controlled by solute diffusion during liquid-solid phase transition. To further investigate the effects of cooling rate and undercooling on the mechanical properties of Cu-Zr eutectic alloys, the microhardness of each of different phases is determined. The microhardness of the primary (Cu) phase within Cu-10 wt.%Zr hypoeutectic alloy is strengthened with the increase of cooling rate. The microhardness of eutectic within the three alloys also increases with increasing the cooling rate and the initial alloy composition of the alloy.%采用落管方法实现了液态Cu-10 wt.%Zr亚共晶、Cu-12.27 wt.%Zr共晶和Cu-15 wt.%Zr过共晶合金在微重力无容器条件下的快速共晶与枝晶生长.Cu-12.27 wt.%Zr共晶合金的凝固组织随液滴直径减小由层片规则共晶向不规则共晶转变,且层片间距减小;Cu-10 wt.%Zr亚共晶合金的初生(Cu)相随液滴直径减小由粗大树枝晶向棒状晶转变,且所占体积分数增加,部分区域形成花状凝固组织,(Cu)相枝晶辐射向外生长;Cu-15 wt.%Zr过共晶合金初生相则为金属间化合物Cu9 Zr2相,呈条状生长,随液滴直径减小冷却速率增大,凝固组织由宏观弯曲生长向球状晶胞转变.理论计算表明,三个合金液固相变枝晶与共晶的生长均由溶质扩散控制.测定Cu-10 wt.%Zr亚共晶合金初生(Cu)相显微硬度随液滴直径减小而增大,三个合金的共晶相随合金初始成分增大而增大.

摘要： High temperature Fe-Al-Nb alloys will be prospectively applied to the industrial field,i.e.,aviation,gas turbine,etc.In this paper,rapid solidification of Fe67.5Al22.sNbg.7 ternary alloy under microgravity condition is realized by using drop tube containerless processing technique.Our purpose is to investigate the microstructural transition pattern and relevant micromechanical properties,and then to reveal the influence of rapid eutectic growth on application performance.The sample of 2 g is placed in a quartz tube with an orifice at the bottom,and the quartz tube is then placed at the top of 3 m drop tube.The sample is inductively melted and further superheated to a certain temperature with the protecting mixture gas composed of argon and helium.The alloy melt is ejected through the orifice by an argon gas flow and dispersed into fine droplets.The droplets are undercooled and finally rapidly solidified during their free fall in the drop tube.The alloy droplets with the diameter sizes ranging from 40 to 1000 μm are achieved.The liquidus temperature of the alloy is 1663 K.The microstructure of the alloy consists of Nb(Fe,Al)2 and (αFe) phases.In the master alloy prepared by arc melting,the segregation along the gravity direction takes place because of the difference in cooling rate inside the master alloy.By comparison,the microstructures of the alloy droplets are homogeneous.The variations of thermodynamical parameters with droplet size are analyzed.As droplet diameter decreases,its Nusselt and Reynolds numbers rise from 3 to 8 and from 5 to 137,respectively,its undercooling and cooling rate increase from 50 to 216 K and from 1.23 x 103 to 5.53 x 105 K.s-1 respectively.This causes the corresponding microstructural transition.A small amount of primary Nb(Fe,A1)2 phase transforms from dendrite to equiaxed grain,the lamellar eutectic is replaced by the fragmented eutectic.The relationship between eutectic interlamellar spacing and undercooling satisfies an exponential equation,indicating that the eutectic is refined by three times.Consequently,mainly owing to the eutectic refinement,the microhardness of the alloy increases by 10％ with the increase of undercooling according to the Hall-Petch behavior in terms of both eutectic grain size and interlamellar spacing.Compared with the microstructure of the alloy undercooled to the same level under electromagnetic levitation in our recent work,the microstructure in drop tube is more refined due to the larger cooling rate,contributing to the microhardness of the alloy increasing by 2％-6％.%采用落管无容器处理技术实现了Fe67.5Al22.sNb9.7三元合金在微重力条件下的快速凝固,获得了直径为40-1000 μm的合金液滴.实验中合金液滴的过冷度范围为50-216 K,冷却速率随着液滴直径的减小由1.23×103 K.S-1增大到5.53×105 K·s-1.研究发现,Fe67.sAl22.sNb9.7合金液滴的凝固组织均由Nb(Fe,Al)2相和(QFe)相组成,且随着液滴直径的减小,初生Nb(Fe,Al)2相由树枝晶转变为等轴晶,共晶组织发生了约3倍的细化且生长特征由层片共晶向碎断共晶转变;硬质初生Nb(Fe,Al)2相的析出有效提高了合金的显微硬度.与电磁悬浮条件下同过冷合金的凝固组织对比发现,落管条件下的合金液滴凝固组织更细化,使得合金显微硬度提高了2％一6％.

摘要： 本文首次采用深过冷加水淬的方法,成功地制备了样品直径为16mm,高为15mm,组织中颗粒平均尺寸约为120nm左右的Fe76B12Si12合金超细晶材料.其磁损耗P4001T和P10001T分别为普通硅钢片的40％和65％.系统研究了组织类型及Fe2B(Si)相尺度对该合金软磁性能的影响,发现该合金的最佳软磁性能位于FeB(Si)相完全粒化的非规则共晶组织区,并且当其Fe2B(Si)相尺寸细化至0.36～0.50μm以下时,其软磁性能随着相尺寸的减小而大幅度改善.对以上结果产生的原因进行了讨论.

摘要： 该文利用过冷度的遗传性，提出将合金熔体深过冷与传统定向凝固相结合的深过冷定向凝固（ＳＤＳ）技术，并在自制的实验装置上，对ＳＤＳ技术进行了探索性研究，实现了Ｃｕ－５．０ｗｔ℅Ｎｉ合金的深过冷和深过冷定向凝固。结果表明：（１）ＳＤＳ技术获得的定向生长组织与ＬＭＣ法相当，且一次枝晶间距约为３０μｍ，二次分枝被抑制，一次枝晶主干挺直、细密，与试样轴向偏差约为５．８°；（２）建立了描述ＳＤＳ过程过冷度与凝固速率之间的数学模型，即Ｔ－Ｔ模型，利用此模型可以解释ＳＤＳ试样上微观组织的演化情况。

摘要： 本文采用嵌入原子法对深过冷条件下Ni3Al合金的熔点和比热进行了分子动力学模拟.熔点的模拟分别采用三明治夹层结构法和NVE系综法,两种方法获得的熔点比较一致.但均略高于实验值,这应该是由于实验中熔点的测量受到普遍存在的表面熔化过程影响的结果.模拟获得的比热在800K到2000K范围内呈现随着温度的升高缓慢线性减小的趋势.

摘要： 本文采用嵌入原子法对深过冷条件下Ni2TiAl合金的焓、比热和密度进行了分子动力学模拟,并根据模拟结果拟合得到比热随温度变化的关系式.同时,模拟结果显示Ni2TiAl合金的比热和密度随着温度的降低而线性增大,焓则随着温度的降低线性减小.

摘要： 在大气熔炼条件下,用熔融玻璃对铜进行净化,使大体积铜在高铝质陶瓷坩埚中获得了228K的过冷度;在一定过冷度范围内,铜自由凝固后的形核点只有一点,X—射线衍射证明此组织为单晶;从理论上对过冷金属熔体中单晶形成的机理进行了研究,实验得到的形成单晶的过冷度范围与理论计算结果相吻合.

摘要： 本文通过查阅文献资料,综述了国内外近年来难混溶偏晶合金均质化制备技术的研究现状及存在问题,包括微重力条件下的熔融铸造法、定向凝固法、搅拌铸造法、控制铸造法、快速凝固法、离心熔铸法.指出快速凝固法发展潜力最大,并提出有关研究方向.

摘要： 本文通过查阅文献资料,综述了国内外近年来难混溶偏晶合金均质化制备技术的研究现状及存在问题,包括微重力条件下的熔融铸造法、定向凝固法、搅拌铸造法、控制铸造法、快速凝固法、离心熔铸法.指出快速凝固法发展潜力最大,并提出有关研究方向.

摘要： 本文通过查阅文献资料,综述了国内外近年来难混溶偏晶合金均质化制备技术的研究现状及存在问题,包括微重力条件下的熔融铸造法、定向凝固法、搅拌铸造法、控制铸造法、快速凝固法、离心熔铸法.指出快速凝固法发展潜力最大,并提出有关研究方向.

摘要： 本文通过查阅文献资料,综述了国内外近年来难混溶偏晶合金均质化制备技术的研究现状及存在问题,包括微重力条件下的熔融铸造法、定向凝固法、搅拌铸造法、控制铸造法、快速凝固法、离心熔铸法.指出快速凝固法发展潜力最大,并提出有关研究方向.

摘要： 本发明涉及一种带过冷保护的深冷缓释便携冷源装置及其使用方法。本发明的目的是解决现有便携冷源装置存在无法满足野外无保障场景下的现场制冷和深冷缓释等综合需求的技术问题，提供一种带过冷保护的深冷缓释便携冷源装置及其使用方法。该装置采用氯化铵、氢氧化钡、氯化钠等常温组分，利用化学吸热、相变吸热的复合过程，实现深度蓄冷、缓释制冷的综合效能，是一种可提供长时间深度冷却条件的便携装置，解决了现有技术无法现场制冷、无法深度冷却、无法便携备用的问题；通过机械操作启动，无需低温保障、无需加注介质，解决现有技术保障要求高、用前操作繁杂的问题；还基于化学吸热过程的气体产物设计了隔离结构，形成过冷防护功能。

摘要： 本发明属于道岔钢轨的生产技术领域，具体涉及大过冷度深硬化层道岔钢轨及其制备方法。本发明所要解决的技术问题是提供一种硬度分布均匀，深硬化层的大过冷度深硬化层道岔钢轨及其制备方法。该方法是：将入炉铁水依次进行转炉冶炼→小平台→LF精炼→RH真空处理→浇铸得钢坯→缓冷坑缓冷→奥氏体均匀化→轧制得钢轨→热处理；所述转炉冶炼过程中添加0.2～0.3％的Cr，0.04～0.06％的V，0.75～0.80％的C；所述热处理过程分两段进行冷却。本发明方法制备得到的道岔钢轨的深硬化层更深，硬度分布更均匀，抗接触疲劳性能更优，同时兼顾良好的耐磨性能。

摘要： 本发明涉及一种带过冷保护的深冷缓释便携冷源装置及其使用方法。本发明的目的是解决现有便携冷源装置存在无法满足野外无保障场景下的现场制冷和深冷缓释等综合需求的技术问题，提供一种带过冷保护的深冷缓释便携冷源装置及其使用方法。该装置采用氯化铵、氢氧化钡、氯化钠等常温组分，利用化学吸热、相变吸热的复合过程，实现深度蓄冷、缓释制冷的综合效能，是一种可提供长时间深度冷却条件的便携装置，解决了现有技术无法现场制冷、无法深度冷却、无法便携备用的问题；通过机械操作启动，无需低温保障、无需加注介质，解决现有技术保障要求高、用前操作繁杂的问题；还基于化学吸热过程的气体产物设计了隔离结构，形成过冷防护功能。

摘要： 本发明公开了一种深过冷处理GH605高温合金及其制备方法，该合金制备方法包括如下过程：将原始态GH605合金样品置入石英试管并放入净化剂；将石英试管置于感应炉腔室的高频感应加热线圈内，将腔室内抽真空并充入Ar气体；调节加热温度与红外测温仪位置，使实时测量温度与合金样品温度保持一致，待净化剂充分熔化并包覆合金样品后，将合金样品过热至高于合金样品的液相线温度100K–250K并保温，实时观测合金熔体状态；待发生再辉现象后，判断合金样品的过冷度是否达到过冷度50K以上的要求，若满足要求则让合金样品自然冷却至室温。本发明采用熔体过冷处理，调控凝固及后续相的析出，获得大过冷度且显微硬度相比原始态提升60.4％‑66.7％的合金。

摘要： 本发明属于金属材料制备技术领域，提供了金属材料液态深过冷和固态相变双联协控方法及装置。本发明提供的金属材料液态深过冷和固态相变双联协控装置包括加热系统(1)、冷却系统(2)和与所述加热系统连接的抽拉系统(3)；所述加热系统(1)包括样品容器(11)和热源(12)；所述样品容器(11)置于热源(12)内；所述加热系统(1)的样品容器(11)通过抽拉系统(3)进入或脱离所述冷却系统(2)。本发明提供的双联协控装置在加热系统进行深过冷后，通过抽拉系统直接将加热系统的样品容器拉入冷却系统进行冷却得到冷却样品；然后根据实际需要将冷却样品在加热系统和冷却系统中进行往复运动，实现固态相变的调控。本发明的装置可以实现深过冷和固态相变调控的一体操作，操作简单、操作难度小。

摘要： 本发明涉及定向凝固技术领域，尤其涉及一种多模式激发的深过冷定向凝固装置及方法，其包括反应炉、熔炼装置、加料装置、激发装置、抽拉杆和抽拉装置，加料装置用于在热熔过程中向坩埚内添加净化剂；激发装置包括能够填充液态金属的激发室、水冷环层和与激发室连通的液位控制器，液位控制器用于控制激发室内液态金属的液位；抽拉装置能够通过抽拉杆以预定速度范围将坩埚的至少一部分拉入激发室内。本装置通过玻璃净化和循环过热结合的方法实现熔体深过冷，并将熔炼、液态金属/水双重冷却以及抽拉装置巧妙结合，可以选择不同模式激发深过冷熔体定向凝固，从而能够获得具有不同组织及性能特征的深过冷定向凝固铸件，以满足更多研究和应用需求。

摘要： 本发明属于金属材料制备技术领域，提供了金属材料液态深过冷和固态相变双联协控方法及装置。本发明提供的金属材料液态深过冷和固态相变双联协控装置包括加热系统(1)、冷却系统(2)和与所述加热系统连接的抽拉系统(3)；所述加热系统(1)包括样品容器(11)和热源(12)；所述样品容器(11)置于热源(12)内；所述加热系统(1)的样品容器(11)通过抽拉系统(3)进入或脱离所述冷却系统(2)。本发明提供的双联协控装置在加热系统进行深过冷后，通过抽拉系统直接将加热系统的样品容器拉入冷却系统进行冷却得到冷却样品；然后根据实际需要将冷却样品在加热系统和冷却系统中进行往复运动，实现固态相变的调控。本发明的装置可以实现深过冷和固态相变调控的一体操作，操作简单、操作难度小。

摘要： 本发明公开了一种提高钴基高温合金强韧性的磁场深过冷处理方法，包括将锻态GH605合金的样品加热升温至高于样品的液相线温度50 K‑150 K保温，待保温完成后开始降温，并持续观测温度随时间的变化曲线，待发生再辉现象后实现大过冷，重复上述过热循环过程直到过冷度稳定，随后在样品低于再辉温度200‑300 K时保温5‑10 min，然后再次升温，并启动所述超导磁体励磁功能，并保证合金熔体的保温阶段已完全处于稳恒强磁场作用下，保温完成后降温后将石英试管取出，并迅速淬火去磁。本发明采用强磁场下的熔体过冷处理技术，调控凝固过程及后续相的析出，可获得室温压缩强度和断后延伸率相比原始态分别提升近44％和21％的合金。

摘要： 本发明公开了一种深过冷处理GH605高温合金及其制备方法，该合金制备方法包括如下过程：将原始态GH605合金样品置入石英试管并放入净化剂；将石英试管置于感应炉腔室的高频感应加热线圈内，将腔室内抽真空并充入Ar气体；调节加热温度与红外测温仪位置，使实时测量温度与合金样品温度保持一致，待净化剂充分熔化并包覆合金样品后，将合金样品过热至高于合金样品的液相线温度100K–250K并保温，实时观测合金熔体状态；待发生再辉现象后，判断合金样品的过冷度是否达到过冷度50K以上的要求，若满足要求则让合金样品自然冷却至室温。本发明采用熔体过冷处理，调控凝固及后续相的析出，获得大过冷度且显微硬度相比原始态提升60.4％‑66.7％的合金。

摘要： 本发明公开了一种深过冷快速凝固法制备焦绿石结构Bi2Ti2O7陶瓷的方法，包括以下步骤：将铋源和钛源混合后，研磨成粉末状配料，再将其压制成生坯，进行热处理后，得到样品，将样品置于悬浮容器中，并在悬浮容器底部持续通入Ar气，使样品悬浮于Ar气中，然后用CO2激光器将样品加热至熔化，待熔化的样品在Ar气中悬浮稳定后，停止加热，冷却后，即制得焦绿石结构Bi2Ti2O7陶瓷，本发明方法过程简单，无任何副产物，重复性好，制备的焦绿石结构Bi2Ti2O7块体材料纯度高，且制备原料配比的比例范围宽，不限于单一的配比。