技术领域Technical field
本发明涉及钛合金熔炼技术领域，尤其涉及一种Ti-Mo-Ni-Y稀土钛合金板材的制备方法。The invention relates to the technical field of titanium alloy smelting, and in particular to a method for preparing a Ti-Mo-Ni-Y rare earth titanium alloy plate.
背景技术Background technique
作为氯碱工业用传统钛合金来讲，除了要求其拥有优异的耐腐蚀性外，其强度依然是非常重要的指标，而随着工业化发展，钛合金的强度水平难以满足日益增长的苛刻的工业服役标准，导致钛合金在其工业化应用时使用周期较短，限制了钛合金的长期应用，因此大批量生产高强高耐蚀钛合金是一项极具意义的工作。As a traditional titanium alloy used in the chlor-alkali industry, in addition to its excellent corrosion resistance, its strength is still a very important indicator. With the development of industrialization, the strength level of titanium alloys is difficult to meet the increasingly demanding industrial service. Standards result in a short service life of titanium alloys in industrial applications, limiting the long-term application of titanium alloys. Therefore, mass production of high-strength and high-corrosion-resistant titanium alloys is a very meaningful task.
在实际电子束冷床熔炼钛合金扁锭的过程中，稀土元素的加入可以改善钛合金的晶体结构，减小晶粒尺寸，提高钛合金的强度和硬度，稀土元素还可以与钛合金形成固溶体，增加钛合金的强度。但由于稀土元素的易挥发性，导致了其在熔炼过程难以控制产品成分的均匀性，同时由于稀土氧化物的熔点过高，不适宜作为原材料进行电子束冷床熔炼，因此在熔炼过程控制稀土元素的挥发以及扁锭的均匀性，对高品质高强高耐蚀钛合金制备具有重大意义。In the actual process of electron beam cooling bed melting of titanium alloy flat ingots, the addition of rare earth elements can improve the crystal structure of the titanium alloy, reduce the grain size, and increase the strength and hardness of the titanium alloy. Rare earth elements can also form a solid solution with the titanium alloy. , increase the strength of titanium alloy. However, due to the volatility of rare earth elements, it is difficult to control the uniformity of product components during the smelting process. At the same time, because the melting point of rare earth oxides is too high, they are not suitable as raw materials for electron beam cooling bed melting. Therefore, rare earth elements must be controlled during the smelting process. The volatilization of elements and the uniformity of flat ingots are of great significance to the preparation of high-quality, high-strength and high-corrosion-resistant titanium alloys.
发明内容Contents of the invention
本发明的目的在于提供一种Ti-Mo-Ni-Y稀土钛合金板材的制备方法，具体包括以下步骤：The object of the present invention is to provide a method for preparing a Ti-Mo-Ni-Y rare earth titanium alloy plate, which specifically includes the following steps:
(1)将所需要的Ti-Mo-Ni-Y钛合金的成分设定为熔炼名义成分，并对海绵钛、Ti-15Mo中间合金、镍屑和纯Y粒进行计算并精确称重。(1) Set the required composition of Ti-Mo-Ni-Y titanium alloy as the nominal melting composition, and calculate and accurately weigh sponge titanium, Ti-15Mo master alloy, nickel scraps and pure Y particles.
(2)将纯Y粒和镍屑用纯钛箔包裹成合金料包，再将Ti-15Mo中间合金和海绵钛混合均匀后干燥。(2) Wrap pure Y particles and nickel shavings with pure titanium foil to form an alloy package, then mix the Ti-15Mo master alloy and sponge titanium evenly and dry.
(3)干燥后的Ti-15Mo中间合金和海绵钛混合物分为3等份，分3次加入，合金料包分为两等份，分两次加入，具体为：先加入混合均匀的Ti-15Mo中间合金和海绵钛，再沿四等分的中心位置加入合金料包形成合金料包层，再加入Ti-15Mo中间合金和海绵钛，继续沿四等分中心位置加入合金料包，最后加入剩余的Ti-15Mo中间合金和海绵钛，压制成柱状料块。(3) The dried Ti-15Mo master alloy and titanium sponge mixture is divided into 3 equal parts and added in three times. The alloy package is divided into two equal parts and added in two times. The details are as follows: first add the uniformly mixed Ti- 15Mo master alloy and sponge titanium, then add the alloy package along the center of the four equal parts to form an alloy cladding, then add Ti-15Mo master alloy and sponge titanium, continue to add the alloy package along the center of the four equal parts, and finally add The remaining Ti-15Mo master alloy and titanium sponge are pressed into columnar blocks.
(4)在电子束冷床熔炼炉的进料室内对料块均匀排布，进料为连续过程，且随着时间的延长，进料的速度与熔炼速度成正比例；其中进料的速度y与熔炼速度x满足公式y＝kx，0.000834≤k≤0.00167；熔炼得到成分均匀的Ti-Mo-Ni-Y稀土钛合金扁锭；(4) The material blocks are evenly arranged in the feeding chamber of the electron beam cooling bed melting furnace. The feeding is a continuous process, and as time goes by, the feeding speed is proportional to the melting speed; where the feeding speed y and the melting speed x satisfy the formula y=kx, 0.000834≤k≤0.00167; the Ti-Mo-Ni-Y rare earth titanium alloy flat ingot with uniform composition is obtained by melting;
(5)将铸态合金锭铣面后进行无锻直轧成板材。(5) The cast alloy ingot is face-milled and then directly rolled into a plate without forging.
优选的，本发明步骤(1)中原料经过清洗干燥，其中海绵钛为0A级海绵钛，纯度高于99.8％。Preferably, in step (1) of the present invention, the raw materials are washed and dried, and the titanium sponge is 0A grade titanium sponge with a purity higher than 99.8%.
优选的，本发明步骤(2)中干燥的条件为：100～200℃干燥2～3h。Preferably, the drying conditions in step (2) of the present invention are: drying at 100-200°C for 2-3 hours.
优选的，本发明步骤(3)中混合均匀的Ti-15Mo中间合金和海绵钛分三次加入，第一次加入的质量百分比为25～40％，第二次加入的质量百分比为25～40％，剩余的第三次加入。Preferably, in step (3) of the present invention, the uniformly mixed Ti-15Mo master alloy and titanium sponge are added in three times, the mass percentage of the first addition is 25 to 40%, and the mass percentage of the second addition is 25 to 40%. , the remaining third addition.
优选的，本发明所述步骤(4)中熔炼真空度需达到1.0×10-3～1.0×10-8Pa，熔炼速度为600～800kg/h，熔炼温度为1800～2100℃。Preferably, in step (4) of the present invention, the melting vacuum degree needs to reach 1.0×10-3 ~ 1.0×10-8 Pa, the melting speed is 600 ~ 800kg/h, and the melting temperature is 1800 ~ 2100°C.
优选的，本发明所述步骤(5)中无锻直轧一火开轧温度为930～940℃，轧制5道次，压下率75～85％，确保破碎铸锭粗大树枝晶，二火轧制温度为840～850℃，轧制7道次，压下率88～88％，总轧制12道次，总变形量为97％。Preferably, in step (5) of the present invention, the first-fire rolling temperature of the no-forging direct rolling is 930-940°C, 5 rolling passes, and the reduction rate is 75-85% to ensure that the coarse dendrites of the ingot are broken. The fire rolling temperature is 840~850℃, rolling is 7 passes, the reduction rate is 88~88%, the total rolling is 12 passes, and the total deformation is 97%.
发明人发现EB炉熔炼过程为半连铸过程，从非稳态到稳态的过程，随着熔炼时间的延长，熔体不断流入结晶器，熔池变深，此时调控进料室的速度，可以使得前一批海绵钛块完全凝固的同时减少熔池深度，避免缺陷的形成，获得高品质均匀的产品。The inventor found that the EB furnace smelting process is a semi-continuous casting process, from an unsteady state to a steady state. As the smelting time prolongs, the melt continues to flow into the crystallizer and the molten pool becomes deeper. At this time, the speed of the feed chamber is adjusted. , which can completely solidify the previous batch of titanium sponge blocks while reducing the depth of the molten pool, avoiding the formation of defects, and obtaining high-quality and uniform products.
相比于现有技术，本发明的有益效果是：Compared with the existing technology, the beneficial effects of the present invention are:
(1)本发明采用电子束冷床炉(EB炉)一次熔炼获得的扁锭，而传统真空自耗电弧炉(VAR炉)需要熔炼3～4次，并且EB炉熔炼可以充分去除高低密度夹杂，缩短工艺流程，降低熔炼成本，并且能够获得大规格扁锭。(1) The present invention uses an electron beam cooling bed furnace (EB furnace) to obtain flat ingots from one melting, while the traditional vacuum consumable electric arc furnace (VAR furnace) requires 3 to 4 times of melting, and the EB furnace melting can fully remove the high and low High-density inclusions shorten the process flow, reduce smelting costs, and enable large-size flat ingots to be obtained.
(2)本发明创新性提出A-B-A-B-A的布料方法(A为Ti-15Mo中间合金和海绵钛，B为合金料包)，该方法能够有效的减少Y元素挥发，减少合金损耗，提高合金成分的均匀性。(2) The present invention innovatively proposes the A-B-A-B-A distribution method (A is Ti-15Mo master alloy and titanium sponge, B is alloy material package). This method can effectively reduce the volatilization of Y element, reduce alloy loss, and improve the uniformity of alloy composition. sex.
(3)本发明制备得到的新型Ti-Mo-Ni-Y钛合金扁锭，通过稀土Y元素的微量添加，显著细化了钛合金晶粒，屈服强度提升7.8～14.9％，抗拉强度提升8～24.2％。(3) The new Ti-Mo-Ni-Y titanium alloy flat ingot prepared by the present invention significantly refines the titanium alloy grains through the trace addition of the rare earth Y element, increases the yield strength by 7.8 to 14.9%, and increases the tensile strength. 8～24.2%.
(4)本发明所述进料室的速度与熔炼速度的方程关系，一方面能够避免因为熔速过慢且进料室速度过块而导致产品性能不佳，另一方面能够避免因熔速过快且进料室速度跟不上导致生产速率慢，生产成本高。(4) The equation relationship between the speed of the feed chamber and the melting speed described in the present invention can, on the one hand, avoid poor product performance due to too slow melting speed and excessive feed chamber speed. On the other hand, it can avoid the problem of poor product performance due to excessive melting speed. Too fast and the feed chamber speed cannot keep up, resulting in slow production rate and high production cost.
附图说明Description of the drawings
图1为本发明所述布料方式示意图；Figure 1 is a schematic diagram of the cloth distribution method according to the present invention;
图2为Ti-0.32Mo-0.8Ni-0.01Y合金显微组织图；Figure 2 shows the microstructure of Ti-0.32Mo-0.8Ni-0.01Y alloy;
图3为Ti-0.31Mo-0.82Ni-0.05Y合金显微组织图；Figure 3 shows the microstructure of Ti-0.31Mo-0.82Ni-0.05Y alloy;
图4为Ti-0.23Mo-0.87Ni-0.1Y合金显微组织图；Figure 4 shows the microstructure of Ti-0.23Mo-0.87Ni-0.1Y alloy;
图5为对比例Ti-0.3Mo-0.8Ni合金显微组织图。Figure 5 is a microstructure diagram of the Ti-0.3Mo-0.8Ni alloy of the comparative example.
具体实施方式Detailed ways
下面结合附图和具体实施例对本发明作进一步详细说明，但本发明的保护范围并不限于所述内容。The present invention will be further described in detail below in conjunction with the accompanying drawings and specific embodiments, but the protection scope of the present invention is not limited to the content described.
实施例1Example 1
一种Ti-Mo-Ni-Y稀土钛合金板材的制备方法，具体步骤如下(见图2)：A method for preparing Ti-Mo-Ni-Y rare earth titanium alloy plate. The specific steps are as follows (see Figure 2):
(1)将清洗干燥后的纯度高于99.8％的0A级海绵钛、Ni屑、纯Y粒和Ti-15Mo中间合金进行配料，预计熔炼重量约为9800Kg。(1) Mix the cleaned and dried 0A grade titanium sponge with a purity higher than 99.8%, Ni chips, pure Y particles and Ti-15Mo master alloy. The estimated melting weight is about 9800Kg.
(2)将纯Y粒用纯钛箔包裹成合金料包，再将Ti-15Mo中间合金、镍屑和海绵钛混合均匀后干燥，干燥时间为2h，干燥温度为200℃。(2) Wrap the pure Y particles with pure titanium foil into an alloy package, then mix the Ti-15Mo master alloy, nickel chips and titanium sponge evenly and dry them. The drying time is 2 hours and the drying temperature is 200°C.
(3)干燥后的Ti-15Mo中间合金和海绵钛混合物分为3等份，分3次加入，合金料包分为两等份，分两次加入，具体为：先加入混合均匀的Ti-15Mo中间合金和海绵钛，再沿四等分的中心位置加入合金料包形成合金料包层，再加入Ti-15Mo中间合金和海绵钛，继续沿四等分中心位置加入合金料包，最后加入剩余的Ti-15Mo中间合金和海绵钛，压制成150Kg柱状料块。(3) The dried Ti-15Mo master alloy and titanium sponge mixture is divided into 3 equal parts and added in three times. The alloy package is divided into two equal parts and added in two times. The details are as follows: first add the uniformly mixed Ti- 15Mo master alloy and sponge titanium, then add the alloy package along the center of the four equal parts to form an alloy cladding, then add Ti-15Mo master alloy and sponge titanium, continue to add the alloy package along the center of the four equal parts, and finally add The remaining Ti-15Mo master alloy and titanium sponge are pressed into 150Kg columnar blocks.
(4)在电子束冷床熔炼炉的料箱内均匀排布好海绵钛块，对海绵钛块进行熔炼，熔炼速度为600Kg/h，熔炼温度为1900℃，熔炼完的钛合金扁锭尺寸为长8100mm×宽1040mm×厚220mm；进料室的速度y与熔炼速度x满足公式y＝0.00111x。(4) Arrange the titanium sponge blocks evenly in the material box of the electron beam cooling bed melting furnace, and smelt the titanium sponge blocks. The melting speed is 600Kg/h, the melting temperature is 1900°C, and the size of the finished titanium alloy flat ingot is It is 8100mm long × 1040mm wide × 220mm thick; the speed y of the feeding chamber and the melting speed x satisfy the formula y = 0.00111x.
(5)用铣床将钛合金扁锭进行氧化皮铣削，将铣削完的长8000mm×宽1020mm×厚200mm扁锭进行无锻直轧，热轧一火开轧温度为940℃，轧制5道次，压下率75％，确保破碎铸锭粗大树枝晶，二火轧制温度为840℃，轧制7道次，压下率88％，总轧制12道次，总变形量为97％，最终板材厚度为6mm。(5) Use a milling machine to mill the oxide scale of the titanium alloy flat ingot. The milled flat ingot with a length of 8000mm×width of 1020mm×thickness of 200mm is directly rolled without forging. The hot rolling and first-fire rolling temperature is 940℃, and the rolling is performed in 5 passes. times, the reduction rate is 75%, ensuring that the coarse dendrites of the ingot are broken, the secondary rolling temperature is 840°C, the rolling is 7 passes, the reduction rate is 88%, the total rolling is 12 passes, the total deformation is 97% , the final plate thickness is 6mm.
(6)轧制完后待板材冷却至室温从板材心部进行金相和力学性能试样取样。(6) After rolling, wait for the plate to cool to room temperature and take samples of metallographic and mechanical properties from the center of the plate.
实施例2Example 2
一种Ti-Mo-Ni-Y稀土钛合金板材的制备方法，具体步骤如下(见图3)：A method for preparing Ti-Mo-Ni-Y rare earth titanium alloy plate. The specific steps are as follows (see Figure 3):
(1)将清洗干燥后的纯度高于99.8％的0级海绵钛、Ni屑、纯Y粒和Ti-15Mo中间合金进行配料，预计熔炼重量约为9800Kg。(1) Mix the cleaned and dried grade 0 titanium sponge with a purity higher than 99.8%, Ni chips, pure Y particles and Ti-15Mo master alloy. The estimated melting weight is about 9800Kg.
(2)将纯Y粒用纯钛箔包裹成合金料包，再将Ti-15Mo中间合金、镍屑和海绵钛混合均匀后干燥，干燥时间为3h，干燥温度为100℃。(2) Wrap the pure Y particles with pure titanium foil into an alloy package, then mix the Ti-15Mo master alloy, nickel chips and titanium sponge evenly and dry them. The drying time is 3 hours and the drying temperature is 100°C.
(3)干燥后的Ti-15Mo中间合金和海绵钛混合物分为3等份，分3次加入，合金料包分为两等份，分两次加入，具体为：先加入混合均匀的Ti-15Mo中间合金和海绵钛，再沿四等分的中心位置加入合金料包形成合金料包层，再加入Ti-15Mo中间合金和海绵钛，继续沿四等分中心位置加入合金料包，最后加入剩余的Ti-15Mo中间合金和海绵钛，压制成150Kg柱状料块。(3) The dried mixture of Ti-15Mo master alloy and titanium sponge is divided into 3 equal parts and added in 3 times. The alloy package is divided into 2 equal parts and added in two times. The details are as follows: first add the uniformly mixed Ti- 15Mo master alloy and sponge titanium, then add the alloy package along the center of the four equal parts to form an alloy cladding, then add Ti-15Mo master alloy and sponge titanium, continue to add the alloy package along the center of the four equal parts, and finally add The remaining Ti-15Mo master alloy and titanium sponge are pressed into 150Kg columnar blocks.
(4)在电子束冷床熔炼炉的料箱内均匀排布好海绵钛块，对海绵钛块进行熔炼，熔炼速度为700Kg/h，熔炼温度为1880℃，熔炼完的钛合金扁锭尺寸为长8120mm×宽1080mm×厚230mm；进料室的速度y与熔炼速度x满足公式y＝0.000834x。(4) Arrange the titanium sponge blocks evenly in the material box of the electron beam cooling bed melting furnace, and smelt the titanium sponge blocks. The melting speed is 700Kg/h, the melting temperature is 1880°C, and the size of the finished titanium alloy flat ingot is It is 8120mm long × 1080mm wide × 230mm thick; the speed y of the feeding chamber and the melting speed x satisfy the formula y = 0.000834x.
(5)用铣床将钛合金扁锭进行氧化皮铣削，将铣削完的长8000mm×宽1020mm×厚200mm扁锭进行无锻直轧，热轧一火开轧温度为935℃，轧制5道次，压下率80％确保破碎铸锭粗大树枝晶，二火轧制温度为845℃，轧制7道次，压下率85％，总轧制12道次，总变形量为97％，最终板材厚度为6mm。(5) Use a milling machine to mill the oxide scale of the titanium alloy flat ingot. The milled flat ingot with a length of 8000mm × a width of 1020mm × a thickness of 200mm is directly rolled without forging. The hot rolling and one-fire rolling temperature is 935°C, and the rolling is performed in 5 passes. times, the reduction rate is 80% to ensure that the coarse dendrites of the ingot are broken, the secondary rolling temperature is 845°C, the rolling is 7 passes, the reduction rate is 85%, the total rolling is 12 passes, and the total deformation is 97%. The final sheet thickness is 6mm.
(6)轧制完后待板材冷却至室温从板材心部进行金相和力学性能试样取样。(6) After rolling, wait for the plate to cool to room temperature and take samples of metallographic and mechanical properties from the center of the plate.
实施例3Example 3
一种Ti-Mo-Ni-Y稀土钛合金板材的制备方法，具体步骤如下(见图4)：A method for preparing Ti-Mo-Ni-Y rare earth titanium alloy plate. The specific steps are as follows (see Figure 4):
(1)将清洗干燥后的纯度高于99.8％的0级海绵钛、Ni屑、纯Y粒和Ti-15Mo中间合金进行配料，预计熔炼重量约为9800Kg。(1) Mix the cleaned and dried grade 0 titanium sponge with a purity higher than 99.8%, Ni chips, pure Y particles and Ti-15Mo master alloy. The estimated melting weight is about 9800Kg.
(2)将纯Y粒用纯钛箔包裹成合金料包，再将Ti-15Mo中间合金、镍屑和海绵钛混合均匀后干燥，干燥时间为2h，干燥温度为150℃。(2) Wrap the pure Y particles with pure titanium foil into an alloy package, then mix the Ti-15Mo master alloy, nickel chips and titanium sponge evenly and dry them. The drying time is 2 hours and the drying temperature is 150°C.
(3)干燥后的Ti-15Mo中间合金和海绵钛混合物分为3等份，分3次加入，合金料包分为两等份，分两次加入，具体为：先加入混合均匀的Ti-15Mo中间合金和海绵钛，再沿四等分的中心位置加入合金料包形成合金料包层，再加入Ti-15Mo中间合金和海绵钛，继续沿四等分中心位置加入合金料包，最后加入剩余的Ti-15Mo中间合金和海绵钛，压制成150Kg柱状料块。(3) The dried Ti-15Mo master alloy and titanium sponge mixture is divided into 3 equal parts and added in three times. The alloy package is divided into two equal parts and added in two times. The details are as follows: first add the uniformly mixed Ti- 15Mo master alloy and sponge titanium, then add the alloy package along the center of the four equal parts to form an alloy cladding, then add Ti-15Mo master alloy and sponge titanium, continue to add the alloy package along the center of the four equal parts, and finally add The remaining Ti-15Mo master alloy and titanium sponge are pressed into 150Kg columnar blocks.
(4)在电子束冷床熔炼炉的料箱内均匀排布好海绵钛块，对海绵钛块进行熔炼，熔炼速度为800Kg/h，熔炼温度为2080℃，熔炼完的钛合金扁锭尺寸为长8135mm×宽1056mm×厚213mm。进料室的速度y与熔炼速度x满足公式y＝0.00167x。(4) Arrange the titanium sponge blocks evenly in the material box of the electron beam cooling bed melting furnace, and smelt the titanium sponge blocks. The melting speed is 800Kg/h, the melting temperature is 2080°C, and the size of the finished titanium alloy flat ingot is It is 8135mm long x 1056mm wide x 213mm thick. The speed y of the feeding chamber and the melting speed x satisfy the formula y=0.00167x.
(5)用铣床将钛合金扁锭进行氧化皮铣削，将铣削完的长8000mm×宽1020mm×厚200mm扁锭进行无锻直轧，热轧一火开轧温度为930℃，轧制5道次，压下率85％，确保破碎铸锭粗大树枝晶，二火轧制温度为850℃，轧制7道次，压下率80％，总轧制12道次，总变形量为97％，最终板材厚度为6mm。(5) Use a milling machine to mill the oxide scale of the titanium alloy flat ingot. The milled flat ingot with a length of 8000mm×width of 1020mm×thickness of 200mm is directly rolled without forging. The hot rolling and one-fire rolling temperature is 930℃, and the rolling is performed in 5 passes. times, the reduction rate is 85%, to ensure that the coarse dendrites of the ingot are broken, the secondary rolling temperature is 850°C, the rolling is 7 passes, the reduction rate is 80%, the total rolling is 12 passes, the total deformation is 97% , the final plate thickness is 6mm.
(6)轧制完后待板材冷却至室温从板材心部进行金相和力学性能试样取样。(6) After rolling, wait for the plate to cool to room temperature and take samples of metallographic and mechanical properties from the center of the plate.
对比实施例1Comparative Example 1
本实施例所用原料和步骤与实施例1相同，不同在于：不添加纯Y粒。The raw materials and steps used in this embodiment are the same as those in Example 1, except that pure Y particles are not added.
对比实施例2Comparative Example 2
本实施例所用原料和步骤与实施例1相同，不同在于：将步骤(3)修改为：将合金料包与Ti-15Mo中间合金和海绵钛的混合物混合均匀，压制成柱状料块。The raw materials and steps used in this embodiment are the same as those in Example 1. The difference is that step (3) is modified as follows: mix the alloy package with the mixture of Ti-15Mo master alloy and titanium sponge evenly, and press it into a columnar block.
对比实施例3Comparative Example 3
本实施例所用原料和步骤与实施例1相同，不同在于：步骤(4)中进料室的速度等于熔炼速度。The raw materials and steps used in this embodiment are the same as those in Embodiment 1, except that the speed of the feeding chamber in step (4) is equal to the melting speed.
对比实施例4Comparative Example 4
本实施例所用原料和步骤与实施例1相同，不同在于：步骤(5)中轧制热轧条件为：开轧温度为940℃，轧制12道次，总变形量为97％，最终板材厚度为6mm。The raw materials and steps used in this embodiment are the same as those in Embodiment 1. The difference is that the hot rolling conditions in step (5) are: the rolling temperature is 940°C, the rolling is 12 passes, the total deformation is 97%, and the final plate Thickness is 6mm.
对实施例1～3和对比实施例1～4合金板材进行如下分析：The alloy plates of Examples 1 to 3 and Comparative Examples 1 to 4 were analyzed as follows:
(1)力学性能分析(1) Mechanical property analysis
对实施例1～3和对比实施例1～4合金板材进行拉伸试验；每组拉伸试样取5组，保证实验结果可靠；室温单向拉伸实验采用美国MTS E45万能材料试验机进行，拉升速度为1mm/min，获得力学性能等相关数据，测试结果如表1所示。Tensile tests were conducted on the alloy plates of Examples 1 to 3 and Comparative Examples 1 to 4; 5 sets of tensile specimens were taken from each group to ensure reliable experimental results; the room temperature uniaxial tensile test was conducted using the American MTS E45 universal material testing machine. , the lifting speed is 1mm/min, and relevant data such as mechanical properties are obtained. The test results are shown in Table 1.
表1实施例1～3和对比实施例1～4钛合金板材力学性能测试结果Table 1 Mechanical property test results of titanium alloy plates of Examples 1 to 3 and Comparative Examples 1 to 4
通过实施例1和对比实施例1相比可以看出屈服强度提升高达14.9％，抗拉强度提升幅度达24.2％，延伸率没有明显下降，原因是本发明加入微量稀土Y元素，Y元素的加入能够有效限制晶粒的长大，如图2～4可以看出，本发明钛合金由非常细小的网篮状α相构成，本发明添加Y元素后α集束明显更加细化，在加入0.1Y后显微组织最为细小，而对比合金1中显微组织由长条状的α相构成，显微组织较为粗大，本发明由于Y元素添加导致钛合金显微组织显著细化，并且会以纳米颗粒Y2O3形式存在于晶界处，阻碍位错运动，从而使本发明所得钛合金屈服强度和抗拉强度提升。Comparing Example 1 with Comparative Example 1, it can be seen that the yield strength is increased by up to 14.9%, the tensile strength is increased by 24.2%, and the elongation does not decrease significantly. The reason is that the present invention adds a trace amount of rare earth Y element. The addition of Y element It can effectively limit the growth of crystal grains. As can be seen from Figures 2 to 4, the titanium alloy of the present invention is composed of very fine basket-like α phases. After the Y element is added in the present invention, the α clusters are significantly more refined. After adding 0.1 Y The rear microstructure is the smallest, while the microstructure in Comparative Alloy 1 is composed of long α phases, and the microstructure is relatively coarse. In the present invention, due to the addition of Y element, the microstructure of the titanium alloy is significantly refined, and the microstructure will be reduced to nanometers. The Y2O3 particles exist at the grain boundaries and hinder dislocation movement, thereby increasing the yield strength and tensile strength of the titanium alloy obtained by the present invention.
通过实施例1和对比实施例2相比可以看出屈服强度提升高达13.5％，抗拉强度提升幅度达21.6％，延伸率有所提升，原因是对比实施例2中将合金料包与Ti-15Mo中间合金和海绵钛的混合物混合均匀时，Y粒会在混匀后静置的时间出现下漏的情况，导致Y粒在柱状料块的底部富集，而中间及上部Y粒很少或者没有，此时，合金的屈服强度和抗拉强度均显著下降。Comparing Example 1 with Comparative Example 2, it can be seen that the yield strength is increased by 13.5%, the tensile strength is increased by 21.6%, and the elongation is improved. The reason is that in Comparative Example 2, the alloy package is mixed with Ti- When the mixture of 15Mo master alloy and titanium sponge is mixed evenly, the Y particles will leak out during the standing time after mixing, causing the Y particles to be enriched at the bottom of the columnar block, while there are very few Y particles in the middle and upper parts or No, at this time, the yield strength and tensile strength of the alloy decrease significantly.
通过实施例1和对比实施例3相比可以看出屈服强度提升3.6％，抗拉强度提升幅度15.8％，延伸率有所提升，原因是对比实施例3中熔炼的速度等于进料的速度，而第一批料进入熔池时还没有完全融化，此时就会导致熔炼的速度比进料的速度慢，以至于熔池中上一批的料还没有完全融化下一批料已经到达熔池，最后导致熔炼出来的铸锭成分不均匀，因此屈服强度与抗拉强度降低。Comparing Example 1 with Comparative Example 3, it can be seen that the yield strength increased by 3.6%, the tensile strength increased by 15.8%, and the elongation increased. The reason is that the smelting speed in Comparative Example 3 is equal to the feeding speed. The first batch of materials has not been completely melted when entering the molten pool, which will cause the melting speed to be slower than the feeding speed, so that the previous batch of materials in the molten pool has not yet completely melted and the next batch of materials has reached the melting point. pool, which ultimately leads to uneven composition of the smelted ingot, thus reducing the yield strength and tensile strength.
通过实施例1和对比实施例4相比可以看出屈服强度提升6.1％，抗拉强度提升幅度2.7％，延伸率有所提升，原因是直接进行一次轧制合金边缘处开裂，导致合金的屈服强度与抗拉强度降低。Comparing Example 1 with Comparative Example 4, it can be seen that the yield strength has increased by 6.1%, the tensile strength has increased by 2.7%, and the elongation has increased. The reason is that the edge of the alloy is directly rolled once, which leads to the yield of the alloy. Strength and tensile strength are reduced.
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202311086277.6ACN117089733B (en) | 2023-08-28 | 2023-08-28 | A preparation method of Ti-Mo-Ni-Y rare earth titanium alloy plate |
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202311086277.6ACN117089733B (en) | 2023-08-28 | 2023-08-28 | A preparation method of Ti-Mo-Ni-Y rare earth titanium alloy plate |
| Publication Number | Publication Date |
|---|---|
| CN117089733Atrue CN117089733A (en) | 2023-11-21 |
| CN117089733B CN117089733B (en) | 2025-06-20 |
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202311086277.6AActiveCN117089733B (en) | 2023-08-28 | 2023-08-28 | A preparation method of Ti-Mo-Ni-Y rare earth titanium alloy plate |
| Country | Link |
|---|---|
| CN (1) | CN117089733B (en) |
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4129438A (en)* | 1976-03-23 | 1978-12-12 | Rmi Company | Method of adding trace elements to base metals |
| US20080053577A1 (en)* | 2006-09-06 | 2008-03-06 | Cook Incorporated | Nickel-titanium alloy including a rare earth element |
| WO2017018522A1 (en)* | 2015-07-29 | 2017-02-02 | 新日鐵住金株式会社 | Titanium composite material and titanium material for hot working |
| CN108384966A (en)* | 2018-04-13 | 2018-08-10 | 青海聚能钛业股份有限公司 | A method of utilizing electron-beam cold bed furnace melting TA10 titanium alloys |
| CN113802023A (en)* | 2021-08-11 | 2021-12-17 | 昆明理工大学 | A Ti-Al-based titanium alloy slab smelting method for reducing Al element volatilization |
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4129438A (en)* | 1976-03-23 | 1978-12-12 | Rmi Company | Method of adding trace elements to base metals |
| US20080053577A1 (en)* | 2006-09-06 | 2008-03-06 | Cook Incorporated | Nickel-titanium alloy including a rare earth element |
| WO2017018522A1 (en)* | 2015-07-29 | 2017-02-02 | 新日鐵住金株式会社 | Titanium composite material and titanium material for hot working |
| CN108384966A (en)* | 2018-04-13 | 2018-08-10 | 青海聚能钛业股份有限公司 | A method of utilizing electron-beam cold bed furnace melting TA10 titanium alloys |
| CN113802023A (en)* | 2021-08-11 | 2021-12-17 | 昆明理工大学 | A Ti-Al-based titanium alloy slab smelting method for reducing Al element volatilization |
| Title |
|---|
| 刘千里 等: "电子束冷床熔炼钛及钛合金的研究进展", 热加工工艺, vol. 45, no. 9, 31 May 2016 (2016-05-31), pages 9 - 14* |
| Publication number | Publication date |
|---|---|
| CN117089733B (en) | 2025-06-20 |
| Publication | Publication Date | Title |
|---|---|---|
| CN104294068B (en) | A kind of process that can improve A356 aluminium alloy fine degenerate effect | |
| CN104313411B (en) | A kind of process that can improve A356 Mechanical Properties of Aluminum Alloys | |
| CN112430767B (en) | Large-size hollow ingot casting and ingot casting method | |
| CN111961893B (en) | A kind of high-strength, high-plasticity high-entropy alloy and preparation method thereof | |
| CN104294110B (en) | A kind of process that can improve polynary hypoeutectic al-si alloy mechanical property | |
| CN116855752A (en) | Method for preparing TC4 titanium alloy cast ingot by EB furnace | |
| CN106521267A (en) | Casting method for aluminum alloy precision template | |
| CN114905010A (en) | Nickel-based alloy wire and preparation method thereof | |
| CN106521281A (en) | Modifier and modifying method for low-melting-point impurity element lead in copper and copper alloy | |
| CN114231771A (en) | High-performance aluminum alloy prepared by using recycled aluminum and preparation method | |
| CN118639055A (en) | Nickel-boron-aluminum intermediate alloy for high-temperature alloy and preparation method thereof | |
| CN117089733A (en) | Preparation method of Ti-Mo-Ni-Y rare earth titanium alloy plate | |
| CN108866365A (en) | A kind of high-quality titanium aluminium pre-alloyed powder electrode preparation method | |
| CN111575572A (en) | B-doped TiZrNb multi-principal-element alloy and preparation method thereof | |
| CN106544556A (en) | A kind of heat treatment method of precision aluminium-alloy template | |
| CN115747569A (en) | Novel Ti-Fe-B alloy and preparation method thereof | |
| CN115652142A (en) | A kind of novel titanium alloy and preparation method thereof | |
| WO2023000510A1 (en) | Silicide-reinforced copper-titanium alloy matrix composite material and preparation method therefor | |
| CN114000020A (en) | Ingot for large-size die forging and preparation method thereof | |
| CN106244840A (en) | The method preparing TiC particle enhanced aluminum-based composite material by tabletting pretreatment | |
| JPH04272147A (en) | Production of titanium | |
| CN118957329B (en) | Preparation process of low-carbon high-silicon manganese alloy | |
| CN115961187B (en) | A Bi-containing small deformation aging Al-Mg-Sc alloy and preparation method thereof | |
| EP3951000B1 (en) | Zinc alloy and manufacturing method thereof | |
| CN112795816B (en) | Preparation process of AlTi10 intermediate alloy |
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |