CN114645180B - A dual-phase reinforced aluminum alloy and its preparation method - Google Patents
A dual-phase reinforced aluminum alloy and its preparation method Download PDFInfo
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Abstract
Description
技术领域technical field
本发明属于金属材料领域，具体涉及一种双相颗粒强化铝合金及其制备方法。The invention belongs to the field of metal materials, and in particular relates to a two-phase particle reinforced aluminum alloy and a preparation method thereof.
背景技术Background technique
多相复合强化铝合金由于其高温力学性能优良、耐磨性好和热膨胀系数低，制备工艺简单，增强体成本低廉，成为高端铝材料的研究重点。陶瓷相本身具有耐高温、耐磨损、高强度和硬度等优良性能，但因其自身脆性大，作为增强体时往往存在与基体界面润湿性差、界面结合强度低等问题，在提高了铝材料硬度和强度的同时，也不可避免地降低了材料的塑性和韧性，这限制了铝合金在高端领域的应用范围。Multiphase composite strengthened aluminum alloy has become the research focus of high-end aluminum materials due to its excellent high-temperature mechanical properties, good wear resistance, low thermal expansion coefficient, simple preparation process, and low cost of reinforcement. The ceramic phase itself has excellent properties such as high temperature resistance, wear resistance, high strength and hardness, but because of its high brittleness, it often has problems such as poor wettability with the matrix interface and low interface bonding strength when used as a reinforcement. The hardness and strength of the material also inevitably reduce the plasticity and toughness of the material, which limits the application range of aluminum alloys in high-end fields.
高熵合金作为一种独具创新性的合金体系，是由5种及5种以上元素组成，按照等摩尔比或大约等摩尔比组成的合金，众多学者研究发现高熵合金具有许多相比传统合金较为理想的性质，如高韧性、耐高温性、良好的抗腐蚀性和耐磨性等，因此在材料学领域上备受重视。研究发现高熵合金与铝基体的热膨胀系数相近，且金属与金属之间具有的天然界面结合特性，使得高熵合金与铝基体的界面润湿性与界面相容性良好。在不降低材料的强度和硬度的同时，加入高熵合金，与硬质陶瓷颗粒协同作用，可显著改善增强体与基体间的界面结合，提高材料的塑韧性、耐磨性及弹性模量等性能。As a unique and innovative alloy system, high-entropy alloys are alloys composed of 5 or more elements in equimolar ratios or approximately equimolar ratios. Many scholars have found that high-entropy alloys have many advantages compared to traditional The ideal properties of alloys, such as high toughness, high temperature resistance, good corrosion resistance and wear resistance, have attracted much attention in the field of materials science. The study found that the thermal expansion coefficient of the high-entropy alloy and the aluminum matrix is similar, and the natural interfacial bonding characteristics between metals make the interfacial wettability and interfacial compatibility between the high-entropy alloy and the aluminum matrix good. While not reducing the strength and hardness of the material, adding high-entropy alloys and synergizing with hard ceramic particles can significantly improve the interface bonding between the reinforcement and the matrix, and improve the plasticity, toughness, wear resistance and elastic modulus of the material, etc. performance.
目前，已有关于双相或多相混杂增强铝合金材料的报道，但是关于高熵合金和陶瓷组合作为复合增强相制备双相增强铝合金还未有报道，为继续提升铝合金材料的性能和扩大铝合金的高端应用范围，有必要开发新的针对铝合金强化和性能提升的新体系、新方法，制备更高性能的高强韧铝合金，对航天航空、交通运输等领域具有重要意义。At present, there have been reports on dual-phase or multi-phase hybrid reinforced aluminum alloy materials, but there is no report on the combination of high-entropy alloys and ceramics as composite reinforcement phases to prepare dual-phase reinforced aluminum alloys. In order to continue to improve the performance and To expand the range of high-end applications of aluminum alloys, it is necessary to develop new systems and methods for aluminum alloy strengthening and performance improvement, and to prepare higher-performance high-strength and tough aluminum alloys, which is of great significance to aerospace, transportation and other fields.
发明内容Contents of the invention
本发明的目的在于提供一种高熵合金强化相与陶瓷颗粒强化相组合强化的铝合金及其制备方法，通过高熵合金强化相与陶瓷颗粒强化相协同作用，并弥散分布在铝基体晶界处，从而实现复合材料硬度、强度和塑性等性能的同步提高。The purpose of the present invention is to provide an aluminum alloy strengthened by the combination of high-entropy alloy strengthening phase and ceramic particle strengthening phase and its preparation method, through the synergistic effect of high-entropy alloy strengthening phase and ceramic particle strengthening phase, and dispersed in the grain boundary of aluminum matrix In order to realize the synchronous improvement of the hardness, strength and plasticity of the composite material.
本发明是通过以下技术方案实现的：The present invention is achieved through the following technical solutions:
一种双相增强铝合金，其特征在于，所述的双相增强铝合金的增强相为FeCoNiCrMn高熵合金强化相和Al2O3陶瓷强化相，其中，FeCoNiCrMn高熵合金强化相占所述双相增强铝合金总质量分数的15%，Al2O3陶瓷强化相占双相增强铝合金总质量分数的2％~8％，所述的双相增强铝合金的基体为铝。A dual-phase reinforced aluminum alloy, characterized in that the reinforced phase of the dual-phase reinforced aluminum alloy is a FeCoNiCrMn high-entropy alloy reinforced phase and an Al2O3 ceramic reinforced phase, wherein the FeCoNiCrMn high-entropy alloy reinforced phase accounts for the The dual-phase reinforced aluminum alloy accounts for 15% of the total mass fraction, and the Al 2 O 3 ceramic strengthening phase accounts for 2%-8% of the dual-phase reinforced aluminum alloy's total mass fraction, and the matrix of the dual-phase reinforced aluminum alloy is aluminum.
进一步地，所述FeCoNiCrMn高熵合金强化相在铝基体中为片状形态，所述Al2O3陶瓷强化相为球形。Further, the FeCoNiCrMn high-entropy alloy strengthening phase is in the form of flakes in the aluminum matrix, and the Al 2 O 3 ceramic strengthening phase is spherical.
进一步地，所述铝合金的硬度为109.3~128.5HV，屈服强度为291.5~319.2MPa，延伸率为41.2~46.7％。Further, the hardness of the aluminum alloy is 109.3-128.5 HV, the yield strength is 291.5-319.2 MPa, and the elongation is 41.2-46.7%.
所述双相增强铝合金的制备方法，其特征在于，包括以下步骤：The preparation method of the dual-phase reinforced aluminum alloy is characterized in that it comprises the following steps:
(1) 配料：按15%、2％~8％的质量百分比称取FeCoNiCrMn高熵合金强化相粉末、Al2O3陶瓷粉末，以及纯铝粉；(1) Ingredients: Weigh FeCoNiCrMn high-entropy alloy strengthening phase powder, Al 2 O 3 ceramic powder, and pure aluminum powder according to the mass percentage of 15%, 2%~8%;
(2)双相增强铝合金粉末制备：将称量好的粉末混合后，在氩气保护下采用行星式球磨机进行机械合金化，并干燥，制得平均粒径为5μm的双相增强铝合金粉末；(2) Preparation of dual-phase reinforced aluminum alloy powder: After mixing the weighed powders, mechanical alloying was carried out using a planetary ball mill under the protection of argon, and dried to obtain a dual-phase reinforced aluminum alloy with an average particle size of 5 μm powder;
(3)制备压坯：将制得的双相增强铝合金粉末放置于模具中，静压成型，静压力为500MPa，静压时间为10s，得到生坯；(3) Preparing compact: place the prepared dual-phase reinforced aluminum alloy powder in a mold, and perform static pressure molding with a static pressure of 500 MPa and a static pressure time of 10s to obtain a green body;
(5)微波烧结：将生坯放置于微波加热炉内在氩气保护下烧结，烧结温度为460~500℃，保温1~3h，然后随炉冷却到200℃以下即完成烧结，制得双相增强铝合金。(5) Microwave sintering: the green body is placed in a microwave heating furnace and sintered under the protection of argon. The sintering temperature is 460~500°C, kept for 1~3h, and then cooled to below 200°C with the furnace to complete the sintering, and the biphase is obtained. Reinforced aluminum alloy.
进一步地，所述的FeCoNiCrMn高熵合金强化相由纯度大于99.9%的铁、钴、镍、铬、锰粉末按照等摩尔比配制，在氩气保护下采用行星式球磨机机械合金化的方法制备成粒度范围5~15μm、形状为不规则片状的高熵合金粉末。Further, the FeCoNiCrMn high-entropy alloy strengthening phase is prepared from iron, cobalt, nickel, chromium, and manganese powders with a purity greater than 99.9% in an equimolar ratio, and is prepared by mechanical alloying with a planetary ball mill under the protection of argon. High-entropy alloy powder with particle size ranging from 5 to 15 μm and irregular flake shape.
进一步地，FeCoNiCrMn高熵合金粉末机械合金化参数为：预球磨4~6h，转速120r/min；再设置球磨时间为72~96h，转速为280~360r/min；球磨罐和研磨球均为钢质，球料比为5:1。Further, the mechanical alloying parameters of FeCoNiCrMn high-entropy alloy powder are: pre-ball milling for 4-6 hours, and the speed is 120r/min; then set the ball milling time for 72-96 hours, and the speed is 280-360r/min; the ball milling pot and the grinding balls are all steel quality, the ratio of ball to material is 5:1.
进一步地，所述的Al2O3陶瓷强化相尺寸为1~3μm，形状为规则的球形的颗粒。Further, the size of the Al 2 O 3 ceramic strengthening phase is 1-3 μm, and the shape is regular spherical particles.
进一步地，步骤（2）中所述双相增强铝合金粉末的机械合金化参数为：球磨时间设置为6~10h，转速为120~160r/min，球磨罐和研磨球均为钢质，球料比为5:1。Further, the mechanical alloying parameters of the dual-phase reinforced aluminum alloy powder in step (2) are as follows: the ball milling time is set to 6-10 hours, the rotation speed is 120-160 r/min, the ball milling pot and the grinding balls are all made of steel, and the ball milling The material ratio is 5:1.
进一步地，步骤（2）所述的双相增强铝合金粉末干燥过程在真空干燥箱内完成，干燥温度为70~75℃。Further, the drying process of the dual-phase reinforced aluminum alloy powder described in step (2) is completed in a vacuum drying oven, and the drying temperature is 70-75°C.
进一步地，步骤（5）中所述微波加热炉内烧结的升温速率为40~55℃/min。Further, the heating rate of the sintering in the microwave heating furnace in step (5) is 40-55° C./min.
本发明的主要优势在于：以具有金属特质的高熵合金和典型陶瓷特质的氧化铝陶瓷组合作为铝合金的复合强化相，两种强化相在增强铝合金时能够保持自身的优势，起到协同强化、混杂增强效应的作用，使材料的性能大幅度提高。The main advantage of the present invention is that the combination of a high-entropy alloy with metallic properties and alumina ceramics with typical ceramic properties is used as the composite strengthening phase of the aluminum alloy, and the two strengthening phases can maintain their own advantages when strengthening the aluminum alloy and play a synergistic The effect of strengthening and mixing reinforcement effect greatly improves the performance of the material.
高熵合金与陶瓷复合强化铝合金的作用机制在于：The mechanism of action of high-entropy alloy and ceramic composite strengthening aluminum alloy is:
（1）添加高熵合金可以平衡Al2O3陶瓷颗粒与Al基体之间变形的不均匀性，提供良好的结合界面，材料受到外力作用时，载荷能够有效地传递到颗粒上，释放了基体上的应力集中，降低了Al基体断裂的可能性，提高了复合材料的力学性能。(1) The addition of high-entropy alloys can balance the inhomogeneity of deformation between the Al 2 O 3 ceramic particles and the Al matrix, and provide a good bonding interface. When the material is subjected to external forces, the load can be effectively transferred to the particles, releasing the matrix. The stress concentration on the Al matrix reduces the possibility of fracture of the Al matrix and improves the mechanical properties of the composite.
（2）由于Al2O3陶瓷颗粒本身具有优异的性能，它的加入提高了材料的抗拉强度、抗压强度和抗弯强度，加之氧化铝陶瓷颗粒质地坚硬，在球磨过程中一定程度上也充当了研磨剂，对晶粒细化、颗粒弥散分布有积极影响。(2) Due to the excellent performance of Al 2 O 3 ceramic particles themselves, its addition improves the tensile strength, compressive strength and flexural strength of the material, and the alumina ceramic particles are hard, and to a certain extent in the ball milling process It also acts as an abrasive and has a positive effect on grain refinement and particle dispersion.
（3）增强相与铝基体润湿性整体较好，界面平整干净，不存在明显反应层，界面结合强度高。(3) The wettability between the reinforcing phase and the aluminum matrix is generally good, the interface is smooth and clean, there is no obvious reaction layer, and the interface bonding strength is high.
（4）FeCoNiCrMn高熵合金相与氧化铝陶瓷相强化铝合金，存在多种强化机制，包括细晶强化、颗粒强化、位错强化、界面强化等。FeCoNiCrMn和Al2O3的弹性模量较高，所以复合材料具有较高的弹性模量，颗粒增强铝基复合材料的塑性和韧性潜能得到充分发挥。(4) FeCoNiCrMn high-entropy alloy phase and alumina ceramic phase strengthen aluminum alloys, and there are multiple strengthening mechanisms, including fine-grain strengthening, particle strengthening, dislocation strengthening, and interface strengthening. The elastic modulus of FeCoNiCrMn and Al 2 O 3 is higher, so the composite material has a higher elastic modulus, and the plasticity and toughness potential of the particle reinforced aluminum matrix composite material can be fully exerted.
（5）本发明的制备方法可制得颗粒弥散均匀、微观组织细小的FeCoNiCrMn高熵合金和Al2O3陶瓷强化铝合金，具有良好的硬度、强度以及耐磨性能，能够满足航空航天和交通运输领域的应用。(5) The preparation method of the present invention can produce FeCoNiCrMn high-entropy alloys and Al 2 O 3 ceramic-reinforced aluminum alloys with uniform particle dispersion and fine microstructure, which have good hardness, strength and wear resistance, and can meet aerospace and transportation requirements. Applications in the field of transportation.
同时，本发明所采用微波烧结加热技术，具有快速加热、受热均匀等特点。烧结温度结合了高熵合金、氧化铝和铝基体的热膨胀特性，所采用的烧结温度条件下获得的双相增强铝合金具有较高的致密度，在此温度范围下，很大程度上避免了烧结时出现元素扩散、晶粒长大和颗粒界面剥离等现象，对复合材料的性能具有积极影响。At the same time, the microwave sintering heating technology adopted in the present invention has the characteristics of rapid heating and uniform heating. The sintering temperature combines the thermal expansion characteristics of the high-entropy alloy, alumina, and aluminum matrix. The dual-phase reinforced aluminum alloy obtained under the sintering temperature conditions adopted has a high density. In this temperature range, it is largely avoided Phenomena such as element diffusion, grain growth, and particle interface peeling during sintering have a positive impact on the properties of the composite.
附图说明Description of drawings
图1是实施例1获得的FeCoNiCrMn+Al2O3双相强化铝合金的XRD图。FIG. 1 is an XRD pattern of the FeCoNiCrMn+Al 2 O 3 dual-phase strengthened aluminum alloy obtained in Example 1.
图2是实施例1获得的FeCoNiCrMn+Al2O3双相强化铝合金的SEM图。FIG. 2 is an SEM image of the FeCoNiCrMn+Al 2 O 3 dual-phase strengthened aluminum alloy obtained in Example 1.
图3是实施例2获得的FeCoNiCrMn+Al2O3双相强化铝合金的SEM图。3 is an SEM image of the FeCoNiCrMn+Al 2 O 3 dual-phase strengthened aluminum alloy obtained in Example 2.
图4是实施例3获得的FeCoNiCrMn+Al2O3双相强化铝合金的SEM图。FIG. 4 is a SEM image of the FeCoNiCrMn+Al 2 O 3 dual-phase strengthened aluminum alloy obtained in Example 3.
具体实施方式Detailed ways
为使本领域技术人员更好地理解本发明的技术方案，下面结合附图对本发明做进一步详细描述。应理解，这些实施例只是为了举例说明本发明，而非以任何方式限制本发明的范围；在以下的实施例中，未详细描述的各种过程和方法是本领域中公知的常规方法。In order to enable those skilled in the art to better understand the technical solution of the present invention, the present invention will be further described in detail below in conjunction with the accompanying drawings. It should be understood that these embodiments are only for illustrating the present invention, rather than limiting the scope of the present invention in any way; in the following embodiments, various processes and methods not described in detail are conventional methods well known in the art.
实施例1：Example 1:
制备一种FeCoNiCrMn高熵合金和Al2O3陶瓷相复合强化的铝合金，其中FeCoNiCrMn高熵合金强化相的加入量占双相增强铝合金总质量分数的15%，Al2O3陶瓷强化相占双相增强铝合金总质量分数的2％，所述的双相增强铝合金的基体为铝。A FeCoNiCrMn high-entropy alloy and Al 2 O 3 ceramic phase composite strengthened aluminum alloy was prepared, in which the FeCoNiCrMn high-entropy alloy strengthening phase accounted for 15% of the total mass fraction of the dual-phase reinforced aluminum alloy, and the Al 2 O 3 ceramic strengthening phase Accounting for 2% of the total mass fraction of the dual-phase reinforced aluminum alloy, the matrix of the dual-phase reinforced aluminum alloy is aluminum.
上述双相强化铝合金的制备过程为：The preparation process of the above-mentioned dual-phase strengthened aluminum alloy is as follows:
步骤1：将纯度大于99.9%的铁、钴、镍、铬和锰粉按等摩尔比混合后装入不锈钢球磨罐，按球粉重量比5：1加入不锈钢球，不锈钢球分15mm、10mm、5mm三个尺寸，按质量比1：3：5称量大中小球。球磨罐中添加无水乙醇的量为混合粉末的60wt.%，以确保粉末在球磨罐中的均匀性，然后将球磨罐抽真空，并在氩气保护下采用行星式球磨机，预球磨5h，转速120r/min；再设置球磨时间为96h，转速为360r/min；球磨罐和研磨球均为钢质，球料比为5:1，机械合金化后制得FeCoNiCrMn高熵合金粉末，平均粒径为5~15μm，形状呈片状。Step 1: Mix iron, cobalt, nickel, chromium and manganese powders with a purity greater than 99.9% in an equimolar ratio and put them into a stainless steel ball mill tank. Add stainless steel balls according to the ball powder weight ratio of 5:1. The stainless steel balls are divided into 15mm, 10mm, There are three sizes of 5mm, and the large, medium and small balls are weighed according to the mass ratio of 1:3:5. The amount of absolute ethanol added in the ball milling tank is 60wt.% of the mixed powder to ensure the uniformity of the powder in the ball milling tank, then the ball milling tank is evacuated, and a planetary ball mill is used under the protection of argon for pre-milling for 5h. The rotation speed is 120r/min; the ball milling time is set to 96h, and the rotation speed is 360r/min; both the ball mill pot and the grinding balls are made of steel, and the ball-to-material ratio is 5:1. The diameter is 5~15μm, and the shape is flake.
步骤2：按15wt.%、2wt.%的质量百分比进行称量步骤1所得的FeCoNiCrMn高熵合金粉末及氧化铝，余量为纯铝。所述氧化铝为粒径为1-3μm的规则的球形颗粒。Step 2: Weigh the FeCoNiCrMn high-entropy alloy powder and alumina obtained in step 1 according to the mass percentages of 15wt.% and 2wt.%, and the balance is pure aluminum. The aluminum oxide is regular spherical particles with a particle diameter of 1-3 μm.
步骤3：高能球磨制备复合粉末：将称好的两种增强体粉末与基体铝粉混合后装入不锈钢球磨罐，按球粉重量比5：1加入不锈钢球，不锈钢球分15mm、10mm、5mm三个尺寸，按质量比1：2：4。球磨罐中添加无水乙醇的量为混合粉末的60 wt.%，以确保粉末在球磨罐中的均匀性，然后将球磨罐抽真空，并在氩气保护下采用行星式球磨机，球磨时间设置为10h，转速为160r/min，球磨罐和研磨球均为钢质，球料比为5:1，机械合金化后制得 (FeCoNiCrMn+Al2O3)p/Al复合粉末，平均粒径为5μm。再采用真空干燥箱进行干燥，设置干燥箱温度为73℃。Step 3: Preparation of composite powder by high-energy ball milling: mix the two kinds of reinforced powder and matrix aluminum powder and put them into a stainless steel ball mill tank, and add stainless steel balls according to the ball powder weight ratio of 5:1, and the stainless steel balls are divided into 15mm, 10mm, and 5mm Three sizes, according to the mass ratio 1:2:4. The amount of absolute ethanol added to the ball milling jar is 60 wt.% of the mixed powder to ensure the uniformity of the powder in the ball milling jar, then the ball milling jar is evacuated, and a planetary ball mill is used under the protection of argon, and the ball milling time is set 10h, rotating speed 160r/min, ball milling pot and balls are made of steel, ball-to-material ratio is 5:1, (FeCoNiCrMn+Al 2 O 3 )p/Al composite powder is obtained after mechanical alloying, average particle size is 5 μm. Then use a vacuum drying oven to dry, and set the temperature of the drying oven to 73°C.
步骤4：制备压坯：将步骤3所得的复合粉末干燥后放置于模具中，静压成型，静压力为450MPa，静压时间为10s，得到生坯；Step 4: Prepare the compact: dry the composite powder obtained in
步骤5：微波烧结：将步骤4所得的生坯放置于微波熔炼炉内，升温速率为45℃/min，升温到490℃，保温2h，加热过程均在氩气保护下进行，待温度缓慢降至200℃以下，制得双相强化铝合金。Step 5: Microwave sintering: Place the green body obtained in Step 4 in a microwave melting furnace at a heating rate of 45°C/min, raise the temperature to 490°C, and keep it warm for 2 hours. The heating process is carried out under the protection of argon, and the temperature drops slowly To below 200 ° C, a dual-phase strengthened aluminum alloy is produced.
检测结果：实施例1制备的FeCoNiCrMn+Al2O3双相强化铝合金的XRD及SEM见图1及图2，从图中可以看出，所得材料的颗粒弥散分布在铝基体晶界处，界面平整干净，不存在明显反应层，孔隙及缺陷较低，通过标准性能测试，结果表明，双相强化铝合金的硬度达到109.3HV，屈服强度为291.5MPa，延伸率为41.2％，实现了材料性能的大幅度提升，具有显著的技术效果。Test results: XRD and SEM of the FeCoNiCrMn+Al 2 O 3 dual-phase strengthened aluminum alloy prepared in Example 1 are shown in Figure 1 and Figure 2. It can be seen from the figure that the particles of the obtained material are dispersedly distributed at the grain boundaries of the aluminum matrix. The interface is smooth and clean, there is no obvious reaction layer, and the porosity and defects are relatively low. Through the standard performance test, the results show that the hardness of the dual-phase strengthened aluminum alloy reaches 109.3HV, the yield strength is 291.5MPa, and the elongation is 41.2%. The performance has been greatly improved and has significant technical effects.
实施例2和实施例3中保持FeCoNiCrMn高熵合金占双相增强铝合金总质量分数的15%，增加Al2O3陶瓷强化相的质量分数，并采用与实施例1相同的工艺过程及参数制备FeCoNiCrMn+Al2O3复合材料。实施例1-3所获得的FeCoNiCrMn+Al2O3复合材料的性能指标如表1所示。In Example 2 and Example 3, keep the FeCoNiCrMn high-entropy alloy accounting for 15% of the total mass fraction of the dual-phase reinforced aluminum alloy, increase the mass fraction of the Al2O3 ceramic strengthening phase, and adopt the same process and parameters as in Example 1 Preparation of FeCoNiCrMn+Al 2 O 3 composite material. Table 1 shows the performance indexes of the FeCoNiCrMn+Al 2 O 3 composite material obtained in Examples 1-3.
表1Table 1
由表1所示的测试数据，表明本发明制备的FeCoNiCrMn+Al2O3复合材料，随着氧化铝陶瓷增强相的增多硬度、屈服强度和延伸率均有所提升。The test data shown in Table 1 shows that the hardness, yield strength and elongation of the FeCoNiCrMn+Al 2 O 3 composite material prepared by the present invention increase with the increase of the alumina ceramic reinforcement phase.
所述实施例为本发明的优选的实施方式，但本发明并不限于上述实施方式，在不背离本发明的实质内容的情况下，本领域技术人员能够做出的任何显而易见的改进、替换或变型均属于本发明的保护范围。The described embodiment is a preferred implementation of the present invention, but the present invention is not limited to the above-mentioned implementation, without departing from the essence of the present invention, any obvious improvement, replacement or modification that those skilled in the art can make Modifications all belong to the protection scope of the present invention.
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Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110438493A (en) * | 2019-09-05 | 2019-11-12 | 山东建筑大学 | A method of preparing CNTs enhancing high-entropy alloy laser deposition composite material |
| CN112549848A (en) * | 2020-11-26 | 2021-03-26 | 江苏珀然股份有限公司 | Wheel hub made of high-entropy alloy reinforced aluminum-based gradient material and manufacturing method thereof |
Family Cites Families (22)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4735656A (en) * | 1986-12-29 | 1988-04-05 | United Technologies Corporation | Abrasive material, especially for turbine blade tips |
| CN100478474C (en) * | 2002-07-31 | 2009-04-15 | 北京有色金属研究总院 | Particle reinforced aluminium-based composite material and workpiece therefrom and its forming process |
| TW200724492A (en) * | 2005-12-16 | 2007-07-01 | Rui-Kai Chen | Bi-liquid phase sintering process for manufacturing of Al2O3 super hard ceramic metal using cryolite and binding alloy |
| CN104388764B (en) * | 2014-11-06 | 2016-05-04 | 华南理工大学 | Aluminum matrix composite that a kind of high-entropy alloy strengthens and preparation method thereof |
| CN104862510B (en) * | 2015-06-03 | 2016-09-07 | 华中科技大学 | A kind of high-entropy alloy particle enhanced aluminum-based composite material and preparation method thereof |
| CN105478724B (en) * | 2015-12-23 | 2017-08-29 | 华南理工大学 | A kind of high-entropy alloy particle enhanced aluminum-based composite material and its stirring casting preparation technology |
| US20170314097A1 (en) * | 2016-05-02 | 2017-11-02 | Korea Advanced Institute Of Science And Technology | High-strength and ultra heat-resistant high entropy alloy (hea) matrix composites and method of preparing the same |
| CN108588501B (en) * | 2018-05-21 | 2020-05-05 | 江苏理工学院 | A kind of aluminum alloy composite material with solid self-lubricating property and preparation method thereof |
| CN108624829B (en) * | 2018-05-21 | 2020-05-05 | 江苏理工学院 | A kind of high elastic aluminum matrix composite material and preparation method thereof |
| CN108660352B (en) * | 2018-05-31 | 2019-08-30 | 太原理工大学 | Preparation method and application of an enhanced AlCoCrFeNi2 high-entropy alloy-based neutron-absorbing material |
| CN109338172A (en) * | 2018-12-11 | 2019-02-15 | 西安工业大学 | A kind of high-entropy alloy reinforced 2024 aluminum matrix composite material and preparation method thereof |
| CN109439951B (en) * | 2018-12-27 | 2020-07-03 | 吉林大学 | A method for strengthening aluminum-silicon alloy based on multiphase hybrid-scale ceramic particle strengthener |
| US12012647B2 (en) * | 2019-06-21 | 2024-06-18 | United States Government Administrator Of Nasa | Additively manufactured oxide dispersion strengthened medium entropy alloys for high temperature applications |
| CN110273078B (en) * | 2019-06-28 | 2021-01-15 | 江苏大学 | Magnetic (FeCoNi)1.5CuBmREn)PAl composite material and preparation method thereof |
| US11840746B2 (en) * | 2019-07-19 | 2023-12-12 | University Of Florida Research Foundation, Inc. | High temperature lightweight Al—Fe—Si based alloys |
| CN110523997B (en) * | 2019-08-19 | 2022-05-20 | 江苏大学 | A kind of high-entropy alloy particle reinforced cryogenically treated aluminum matrix composite material and preparation method thereof |
| US11565318B2 (en) * | 2019-09-03 | 2023-01-31 | Ut-Battelle, Llc | Reactive matrix infiltration of powder preforms |
| CN111394667B (en) * | 2020-03-25 | 2021-09-10 | 江苏大学 | Regulation (FeCoNiCrAlCu)pMethod for interface of/2024A 1 composite material |
| CN111961906B (en) * | 2020-07-29 | 2021-11-05 | 济南大学 | Preparation method of high-strength high-toughness corrosion-resistant nickel-based composite material and obtained product |
| CN112626403A (en) * | 2020-12-07 | 2021-04-09 | 湘潭大学 | TiB2-FeCoNiCrMn aluminum liquid corrosion resistant material |
| CN112899531B (en) * | 2021-01-19 | 2021-11-23 | 江苏大学 | High-entropy alloy particle reinforced aluminum-based composite material and magnetic field auxiliary preparation method |
| CN113789464B (en) * | 2021-08-16 | 2022-08-26 | 东南大学 | Ceramic phase reinforced refractory high-entropy alloy and preparation method thereof |
-
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110438493A (en) * | 2019-09-05 | 2019-11-12 | 山东建筑大学 | A method of preparing CNTs enhancing high-entropy alloy laser deposition composite material |
| CN112549848A (en) * | 2020-11-26 | 2021-03-26 | 江苏珀然股份有限公司 | Wheel hub made of high-entropy alloy reinforced aluminum-based gradient material and manufacturing method thereof |
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