本文選題：非晶 + 潤(rùn)濕性��； 參考：《沈陽(yáng)理工大學(xué)》2017年碩士論文

【摘要】：近年來(lái),Ti基非晶合金的非晶形成能力成功提高到了厘米級(jí),Ti基塊體非晶也因其高強(qiáng)度、低密度等特性在工程結(jié)構(gòu)材料中有良好的應(yīng)用前景。但是,室溫下塊體非晶極低的塑性卻限制了它的應(yīng)用。通過(guò)引入增塑相,制備非晶復(fù)合材料可以有效改善塊體非晶的塑性。最近,對(duì)于非晶復(fù)合材料的結(jié)構(gòu)可控制備逐漸受到了科研人員的關(guān)注,這對(duì)開(kāi)發(fā)具有高性能的非晶復(fù)合材料具有重要意義。外加法是一種簡(jiǎn)單并且可控性強(qiáng)的制備復(fù)合材料的方法,而內(nèi)生型非晶復(fù)合材料中的兩相具有十分優(yōu)異的相容性和界面結(jié)合質(zhì)量。本文從基體與第二相的潤(rùn)濕性與固液交互作用出發(fā),研究了層狀復(fù)合Ti32.8Zr30.2Ni5.3Cu9Be22.7非晶和與之具有良好相容性的Ti_(61.5)Zr_(36.4)Cu_(2.1)合金的可行性和復(fù)合后材料的微觀結(jié)構(gòu)組成。研究了Ti32.8Zr30.2Ni5.3Cu9Be22.7非晶與Ti_(61.5)Zr_(36.4)Cu_(2.1)合金的潤(rùn)濕行為,二者具有良好的潤(rùn)濕性。連續(xù)升溫過(guò)程中潤(rùn)濕角分兩次減小,在750、800和850℃保溫時(shí),潤(rùn)濕動(dòng)力學(xué)曲線分為快速減小階段和穩(wěn)態(tài)階段。界面上發(fā)生Ti_(61.5)Zr_(36.4)Cu_(2.1)合金的溶解反應(yīng),固液交界處形成了結(jié)合質(zhì)量很好的原子擴(kuò)散層。非晶合金熔化后,內(nèi)部析出了初級(jí)晶化產(chǎn)物,800℃時(shí)該產(chǎn)物完全消失。因此,制備復(fù)合材料時(shí)需將溫度控制在800℃以上用水淬法制備了液橋樣品來(lái)模擬層狀非晶復(fù)合材料的結(jié)合,研究了層狀非晶復(fù)合材料的結(jié)構(gòu)。結(jié)果表明,在800℃以上制備的復(fù)合材料是由部分Ti_(61.5)Zr_(36.4)Cu_(2.1)合金溶解進(jìn)入非晶層中形成的非晶復(fù)合材料層與剩余Ti_(61.5)Zr_(36.4)Cu_(2.1)合金層組成的�；赥i32.8Zr30.2Ni5.3Cu9Be22.7與Ti_(61.5)Zr_(36.4)Cu_(2.1)間良好化學(xué)成分穩(wěn)定性,非晶復(fù)合材料層由Ti32.8Zr30.2Ni5.3Cu9Be22.7非晶基體與β-Ti(Zr,Cu)枝晶相組成。一定冷速條件下,Ti32.8Zr30.2Ni5.3Cu9Be22.7熔體對(duì)Ti_(61.5)Zr_(36.4)Cu_(2.1)有一定的溶解度,非晶熔體中Ti_(61.5)Zr_(36.4)Cu_(2.1)的濃度需超過(guò)溶解度才能在凝固過(guò)程中析出枝晶相。隨保溫時(shí)間延長(zhǎng),基片溶解反應(yīng)逐漸停止,復(fù)合材料層中的枝晶相分布逐漸均勻。統(tǒng)計(jì)液橋樣品基片的溶解深度,由于Ti_(61.5)Zr_(36.4)Cu_(2.1)的密度略小于Ti32.8Zr30.2Ni5.3Cu9Be22.7熔體的密度,液橋樣品下基片受到了重力驅(qū)動(dòng)對(duì)流的作用,所以其溶解深度略大于上基片。選擇了一種溶解深度預(yù)測(cè)模型對(duì)基片溶解深度進(jìn)行擬合,并且驗(yàn)證了擬合數(shù)值的正確性。根據(jù)該模型的擬合值可以了解不同溫度下復(fù)合材料層中均勻分布的枝晶相的體積分?jǐn)?shù),從而控制復(fù)合材料層的性能。另外,還可以利用該模型設(shè)計(jì)層狀材料層間厚度比,達(dá)到控制層狀復(fù)合材料整體性能的目的。
[Abstract]:In recent years, the amorphous formation ability of Ti based amorphous alloys has been successfully raised to centimeter level. The amorphous Ti based bulk has a good application prospect in engineering structure materials because of its high strength and low density. However, the low amorphous plasticity at room temperature limits its application. By introducing plasticized phase, the preparation of amorphous composites can be made. The plasticity of the bulk amorphous is effectively improved. Recently, the control of the structure of amorphous composites has gradually attracted the attention of the researchers, which is of great significance for the development of high performance Amorphous Composites. In this paper, the feasibility of the laminated composite Ti32.8Zr30.2Ni5.3Cu9Be22.7 amorphous and Ti_ (61.5) Zr_ (36.4) Cu_ (2.1) and the microstructure of the composite after the wettability and solid liquid interaction of the matrix and the second phase are studied. The wetting behavior of Ti32.8Zr30.2Ni5.3Cu9Be22.7 amorphous and Ti_ (61.5) Zr_ (36.4) Cu_ (2.1) alloy was investigated, and the two had good wettability. The wetting angle was reduced two times during the continuous heating process. The wetting kinetics curve was divided into a rapid decrease stage and a steady state at 750800 and 850 C. Ti_ (61.5) Zr_ (36.4) Cu_ (2.1) occurred on the interface. The dissolving reaction of the alloy formed a good atomic diffusion layer with good quality at the junction of solid and liquid. After the melting of the amorphous alloy, the primary crystallization product was precipitated, and the product completely disappeared at 800 C. Therefore, the temperature of the composite material was controlled at 800 degrees centigrade, and the liquid bridge sample was prepared by water quenching to simulate the layered amorphous composite. The structure of layered Amorphous Composites is studied. The results show that the composite material prepared at above 800 degrees C is composed of amorphous composite layer formed in the amorphous layer by partial Ti_ (61.5) Zr_ (36.4) Cu_ (2.1) alloy and remaining Ti_ (61.5) Zr_ (36.4) Cu_ (2.1) alloy layer. Based on Ti32.8Zr30.2Ni5.3Cu9Be22.7 and Ti_ (61.5) Z) The stability of chemical composition between r_ (36.4) Cu_ (2.1), amorphous composite layer composed of Ti32.8Zr30.2Ni5.3Cu9Be22.7 amorphous matrix and beta -Ti (Zr, Cu) dendrite. Under certain cold speed conditions, Ti32.8Zr30.2Ni5.3Cu9Be22.7 melts have certain solubility to Ti_ (61.5) Zr_ (36.4) Cu_ (2.1), Ti_ (61.5) Zr_ (2.1) in amorphous melt. The dendrite phase can be precipitated during the solidification process. With the prolongation of the heat preservation time, the dissolution reaction of substrate dissolves gradually and the dendrite phase distribution in the composite layer is evenly distributed. The dissolution depth of the base sheet of the liquid bridge sample is statistically less than the density of Ti_ (61.5) Zr_ (36.4) Cu_ (2.1) less than the density of the melt in the liquid bridge, and the liquid bridge sample The substrate is driven by the action of gravity driven convection, so the dissolution depth is slightly larger than that of the upper substrate. A solution depth prediction model is selected to fit the dissolution depth of the substrate, and the correctness of the fitting value is verified. The volume fraction is used to control the properties of the composite layer. In addition, the model can be used to design the thickness ratio between layers of layered materials to control the overall performance of layered composites.
【學(xué)位授予單位】：沈陽(yáng)理工大學(xué)
【學(xué)位級(jí)別】：碩士
【學(xué)位授予年份】：2017
【分類號(hào)】：TG139.8

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