技术领域technical field
本发明涉及一种亚稳β钛合金板材及其加工方法，属于钛合金板材制备技术领域，该方法加工的亚稳β钛合金板材微观组织均匀，且该方法流程短，加工成本低，效率高。The invention relates to a metastable β-titanium alloy plate and a processing method thereof, belonging to the technical field of titanium alloy plate preparation. The microstructure of the metastable β-titanium alloy plate processed by the method is uniform, and the process is short, the processing cost is low, and the efficiency is high. .
背景技术Background technique
亚稳β型钛合金是一类具有高强度、强耐蚀、加工性能优异的轻质结构材料，广泛应用于航空航天、舰船、武器装甲、化工、运动装备等领域，其中板材是该类合金最重要的产品，占所有产品的80％左右。Metastable β-type titanium alloy is a kind of lightweight structural material with high strength, strong corrosion resistance and excellent processing performance. It is widely used in aerospace, ships, weapons and armor, chemical industry, sports equipment and other fields. The most important product of alloys, accounting for about 80% of all products.
对于亚稳β型钛合金板材而言，目前的生产方式主要为首先在β相区对铸锭进行多次墩拔的开坯锻造，然后在两相区进行多火次多道次的热轧，最后进行热处理以获得所需性能的板材。由于钛合金铸态组织中β晶粒异常粗大(最大可达厘米级别)，且无法通过热处理细化组织，使得合金铸锭在直接进行轧制时会出现开裂、轧后组织不均匀等缺陷，通常需要经过多次锻造以细化β晶粒。同时由于β晶粒在高温单相区容易长大而造成加工性能恶化、轧后组织不均匀，亚稳β型合金一般选择两相区进行轧制。但由于相变点较低(通常在900℃以下)，该类合金在两相区变形抗力较大、塑性不足，使得合金单一火次和单一道次变形量较低，通常需要经过多火次多道次的轧制才能得到所需要尺寸的板材。复杂的热变形工艺增加亚稳β型钛合金板材的加工成本，从而影响了合金板材的广泛应用。For the metastable β-type titanium alloy plate, the current production method is mainly to carry out billet forging on the ingot in the β-phase region for multiple piers, and then perform multi-fire and multi-pass hot rolling in the two-phase region. , and finally heat-treated to obtain the desired properties of the sheet. Since the β grains in the as-cast structure of titanium alloy are abnormally coarse (up to centimeter level), and the structure cannot be refined by heat treatment, defects such as cracking and uneven structure after rolling will occur when the alloy ingot is directly rolled. Often times forging is required to refine the β grains. At the same time, because the β grains are easy to grow in the high-temperature single-phase region, resulting in deterioration of processability and uneven structure after rolling, metastable β-type alloys are generally selected for rolling in the two-phase region. However, due to the low phase transition point (usually below 900°C), this type of alloy has a large deformation resistance and insufficient plasticity in the two-phase region, so that the deformation of the alloy in a single fire and a single pass is low, and usually requires multiple fires. Multiple passes of rolling are required to obtain the required size of the plate. The complex thermal deformation process increases the processing cost of the metastable β-type titanium alloy sheet, which affects the wide application of the alloy sheet.
发明内容Contents of the invention
本发明的目的是为了克服现有技术的不足，提出一种短流程加工的亚稳β钛合金板材及其加工方法。The purpose of the present invention is to overcome the deficiencies of the prior art, and propose a metastable β titanium alloy plate and a processing method thereof processed in a short process.
本发明的一种短流程加工的亚稳β钛合金板材，该钛合金板材成分中含有0.05～0.2wt％的硼元素，也就是说以该钛合金板材的总质量为100％计算，钛合金板材中硼元素的质量含量为0.05％-0.2％。A metastable β-titanium alloy plate processed by a short process of the present invention, the titanium alloy plate contains 0.05-0.2wt% boron element in its composition, that is to say, the total mass of the titanium alloy plate is 100%, and the titanium alloy plate The mass content of the boron element in the plate is 0.05%-0.2%.
本发明的一种亚稳β钛合金板材的制备方法，该方法的步骤包括：A kind of preparation method of metastable β titanium alloy sheet material of the present invention, the step of this method comprises:
(1)熔炼铸锭(1) Smelting ingot
将原材料通过分层布料或混料的方式进行混合，压制为电极，利用氩弧焊接将电极进行连接，利用真空自耗电弧熔炼炉进行2～3次熔炼，得到钛合金铸锭。The raw materials are mixed by layered distribution or mixing, pressed into electrodes, connected by argon arc welding, and smelted 2 to 3 times in a vacuum consumable arc melting furnace to obtain titanium alloy ingots.
(2)板材轧制(2) Plate rolling
将步骤(1)得到的钛合金铸锭进行扒皮，然后切取板坯。将板坯进行保温处理，然后利用热轧设备在一火次下经过3～5个道次轧制，得到中间板材。然后利用马弗炉对板材进行20min～1h的固溶处理，冷却方式为水淬(WQ)或者空冷(AC)，得到组织均匀的钛合金板材。The titanium alloy ingot obtained in step (1) is peeled off, and then a slab is cut. Carry out heat preservation treatment on the slab, and then use hot rolling equipment to go through 3 to 5 passes of rolling under one fire to obtain the intermediate plate. Then, the plate is subjected to solution treatment for 20 minutes to 1 hour in a muffle furnace, and the cooling method is water quenching (WQ) or air cooling (AC), so as to obtain a titanium alloy plate with a uniform structure.
所述的步骤(1)中的原材料包括制备亚稳β钛合金的原料和含硼中间合金或硼粉。The raw materials in the step (1) include raw materials for preparing metastable β titanium alloy and boron-containing master alloy or boron powder.
所述含硼中间合金为AlTiB或FeB，其中AlTiB中Al元素的质量分数不超过10％，FeB中硼元素的质量分数不低于18％。当亚稳β钛合金成分中含有Fe元素时，优选FeB；当亚稳态β钛合金成分中含Al元素时，优选AlTiB；当亚稳β钛合金成分中既不含有Al元素也不含有Fe元素时，选择硼粉。The boron-containing master alloy is AlTiB or FeB, wherein the mass fraction of Al in AlTiB is not more than 10%, and the mass fraction of boron in FeB is not lower than 18%. When the metastable β titanium alloy contains Fe element, FeB is preferred; when the metastable β titanium alloy contains Al element, AlTiB is preferred; when the metastable β titanium alloy contains neither Al nor Fe Elements, choose boron powder.
所述的步骤(1)中钛合金铸锭中硼的质量分数为0.05～0.2wt.％(质量分数)。The mass fraction of boron in the titanium alloy ingot in the step (1) is 0.05-0.2wt.% (mass fraction).
所述的步骤(2)中板坯的保温处理时间根据板坯厚度确定，具体为1.0～2.0min/mm；保温处理温度为Tβ～Tβ+100℃，Tβ为钛合金相变温度。The heat preservation treatment time of the slab in the step (2) is determined according to the thickness of the slab, specifically 1.0 to 2.0 min/mm; the heat preservation treatment temperature is Tβ to Tβ +100°C, and Tβ is the phase transition temperature of the titanium alloy .
所述的步骤(2)中轧制每道次变形量不低于10％，轧制总变形量不低于50％；固溶处理温度为Tβ～Tβ+50℃,Tβ为钛合金相变温度。In the step (2), the rolling deformation per pass is not less than 10%, and the total rolling deformation is not less than 50%; the solution treatment temperature is Tβ ~ Tβ + 50°C, and Tβ is titanium Alloy transformation temperature.
有益效果Beneficial effect
与现有的技术相比，本发明具有以下的优势：目前通常的亚稳β型钛合金热轧板材的加工通常包括在高温下(1000～1200℃)对合金铸锭进行多次墩拔的开坯锻造，然后在低于相变点的温度下进行多火次多道次的热轧。而本发明通过向合金中加入0.05～0.2wt.％的硼元素，使得合金铸锭可以省却开坯锻造过程，直接在相变温度以上进行轧制，同时经过单一火次和3～5道次轧制即可得到合金中间板材，然后在相变温度以上进行短时固溶处理，获得合金板材。本发明相比现有技术可显著缩短板材的加工流程，降低加工成本。同时，相对传统工艺在相变点以下轧制，本发明的轧制温度和固溶处理温度在相变点以上，选择范围较宽，使得生产上易于操作。本发明通过向合金中添加微量的硼元素，在不影响其力学性能的前提下，有效缩短合金板材的加工流程。Compared with the existing technology, the present invention has the following advantages: the processing of the usual metastable β-type titanium alloy hot-rolled plate usually includes the process of repeatedly piering the alloy ingot at high temperature (1000-1200 ° C). Open billet forging, and then hot rolling with multiple fires and multiple passes at a temperature lower than the transformation point. However, in the present invention, by adding 0.05-0.2wt.% boron element to the alloy, the alloy ingot can save the billet forging process, and directly roll above the phase transition temperature, and at the same time go through a single fire and 3-5 passes. The alloy intermediate plate can be obtained by rolling, and then a short-term solution treatment is performed above the phase transformation temperature to obtain an alloy plate. Compared with the prior art, the invention can significantly shorten the processing flow of the plate and reduce the processing cost. At the same time, compared with the traditional process of rolling below the phase transition point, the rolling temperature and solution treatment temperature of the present invention are above the phase transition point, and the selection range is wide, making the production easy to operate. The invention effectively shortens the processing flow of the alloy plate by adding a trace amount of boron element to the alloy without affecting its mechanical properties.
附图说明Description of drawings
图1为制备亚稳态β型钛合金热轧板材的传统加工工艺流程；Fig. 1 is the traditional process flow of preparing metastable β-type titanium alloy hot-rolled plate;
图2为本发明中制备亚稳态β型钛合金热轧板材的短流程加工工艺流程；比图1可知，本发明的工艺流程明显少于传统工艺，加工成本低，效率高。Fig. 2 is the short-flow processing process flow for preparing the metastable β-type titanium alloy hot-rolled plate in the present invention; as can be seen from Fig. 1, the process flow of the present invention is obviously less than the traditional process, and the processing cost is low and the efficiency is high.
图3a为实施例1中总变形量为50％的直接轧制2A2F10B合金板材经850℃/1h/WQ固溶处理后纵截面的显微组织；Fig. 3 a is the microstructure of the longitudinal section of the directly rolled 2A2F10B alloy sheet with a total deformation of 50% in Example 1 after solution treatment at 850°C/1h/WQ;
图3b为实施例1中总变形量为50％的直接轧制2A2F合金板材经850℃/1h/WQ固溶处理后纵截面的显微组织；Fig. 3b is the microstructure of the longitudinal section of the directly rolled 2A2F alloy plate with a total deformation of 50% in Example 1 after solution treatment at 850°C/1h/WQ;
图4a为实施例2中总变形量为70％的直接轧制2A2F10B合金板材经850℃/1h/WQ固溶处理后纵截面的显微组织；Fig. 4a is the microstructure of the longitudinal section of the directly rolled 2A2F10B alloy sheet with a total deformation of 70% in Example 2 after solution treatment at 850°C/1h/WQ;
图4b为实施例2中总变形量为70％的直接轧制2A2F合金板材经850℃/1h/WQ固溶处理后纵截面的显微组织；Fig. 4b is the microstructure of the longitudinal section of the directly rolled 2A2F alloy plate with a total deformation of 70% in Example 2 after solution treatment at 850°C/1h/WQ;
图5a为实施例3中总变形量为85％的直接轧制2A2F10B合金板材经850℃/1h/WQ固溶处理后纵截面的显微组织；Fig. 5a is the microstructure of the longitudinal section of the directly rolled 2A2F10B alloy plate with a total deformation of 85% in Example 3 after solution treatment at 850°C/1h/WQ;
图5b为实施例3中总变形量为85％的直接轧制2A2F合金板材经850℃/1h/WQ固溶处理后纵截面的显微组织。Figure 5b is the microstructure of the longitudinal section of the directly rolled 2A2F alloy plate with a total deformation of 85% in Example 3 after solution treatment at 850°C/1h/WQ.
具体实施方式Detailed ways
以下通过实施例和附图阐述本发明具体实施方式。The specific implementation manner of the present invention is set forth below through embodiment and accompanying drawing.
实施例1Example 1
S1.合金铸锭熔炼：S1. Alloy ingot melting:
按照Ti-2(wt.％)Al-9.2(wt.％)Mo-2(wt.％)Fe-0.1(wt.％)B合金(2A2F10B)成分要求，取相应重量的AlMo55、MoFe50、FeB20、Ti-32Mo中间合金和0级海绵钛，利用分层布料的方式压制电极，然后利用真空自耗电弧熔炼设备进行两次熔炼得到32Kg的合金铸锭，以确保成分均匀。然后将铸锭表面扒皮，并利用化学法测试铸锭化学成分(表1)。通过淬火金相法测定其相变点为815±5℃。According to Ti-2 (wt.%) Al-9.2 (wt.%) Mo-2 (wt.%) Fe-0.1 (wt.%) B alloy (2A2F10B) composition requirements, take the corresponding weight of AlMo55, MoFe50, FeB20 , Ti-32Mo master alloy and 0-grade sponge titanium, use layered cloth to press the electrode, and then use vacuum consumable arc melting equipment to melt twice to obtain a 32Kg alloy ingot to ensure uniform composition. Then the surface of the ingot was peeled off, and the chemical composition of the ingot was tested by chemical method (Table 1). The phase transition point was determined to be 815±5°C by quenching metallographic method.
表1 2A2F10B合金铸锭化学成分(质量含量)Table 1 Chemical composition (mass content) of 2A2F10B alloy ingot
S2.板材轧制：S2. Plate rolling:
从步骤S1得到的铸锭上取115mm(长)×80mm(宽)×20mm(厚)的轧制板坯。将板坯在900℃的加热炉中保温20min，然后送入热轧机中进行4道次单向热轧，各道次变形量分别为20％、10％、10％、10％，空冷至室温后进行表面喷砂处理得到厚度为10mm的热轧中间板材，板材边缘光滑无裂纹。将中间板材在850℃下进行30min固溶处理，并水淬，得到合金板材。观察板材纵截面显微组织，并与相同工艺下制备的Ti-2(wt.％)Al-9.2(wt.％)Mo-2(wt.％)Fe合金(2A2F)板材组织进行对比，如附图3a和附图3b所示可知，采用本发明方法得到的板材组织明显更为均匀。A rolling slab of 115 mm (length)×80 mm (width)×20 mm (thickness) is taken from the ingot obtained in step S1. The slab is kept in a heating furnace at 900°C for 20 minutes, and then sent to a hot rolling mill for 4 passes of unidirectional hot rolling. After room temperature, surface blasting treatment is carried out to obtain a hot-rolled intermediate plate with a thickness of 10mm, and the edge of the plate is smooth without cracks. The intermediate plate was subjected to solution treatment at 850° C. for 30 minutes, and quenched in water to obtain an alloy plate. Observe the microstructure of the longitudinal section of the plate, and compare it with the Ti-2(wt.%)Al-9.2(wt.%)Mo-2(wt.%)Fe alloy (2A2F) plate structure prepared under the same process, as As shown in accompanying drawings 3a and 3b, it can be seen that the plate structure obtained by the method of the present invention is obviously more uniform.
实施例2Example 2
S1.合金铸锭熔炼：S1. Alloy ingot melting:
按照Ti-2(wt％)Al-9.2(wt％)Mo-2(wt％)Fe-0.1(wt％)B合金成分要求，取相应重量的AlMo55、MoFe50、FeB20、Ti-32Mo中间合金和0级海绵钛，利用分层布料的方式压制电极，然后利用真空自耗电弧熔炼设备进行两次熔炼得到32Kg的合金扁形铸锭，以确保成分均匀。然后将铸锭表面扒皮，并利用化学法测试铸锭化学成分(表2)。通过淬火金相法测定其相变点为815±5℃。According to Ti-2 (wt%) Al-9.2 (wt%) Mo-2 (wt%) Fe-0.1 (wt%) B alloy composition requirement, get AlMo55, MoFe50, FeB20, Ti-32Mo master alloy of corresponding weight and Grade 0 titanium sponge, using layered cloth to press the electrode, and then using vacuum consumable arc melting equipment to melt twice to obtain a 32Kg alloy flat ingot to ensure uniform composition. Then the surface of the ingot was peeled off, and the chemical composition of the ingot was tested by chemical method (Table 2). The phase transition point was determined to be 815±5°C by quenching metallographic method.
表2 2A2F10B合金铸锭化学成分(质量含量)Table 2 Chemical composition (mass content) of 2A2F10B alloy ingot
S2.板材轧制：S2. Plate rolling:
从步骤S1所示的铸锭上取115mm(长)×80mm(宽)×20mm(厚)的轧制板坯。将板坯在900℃的加热炉中保温20min，然后送入热轧机中进行4道次单向热轧，各道次变形量分别为25％、20％、15％、10％，空冷至室温后进行表面喷砂处理得到厚度为6mm的热轧中间板材，板材边缘光滑无裂纹。将中间板材在850℃下进行30min固溶处理，并水淬得到合金板材。观察板材纵截面显微组织，并与相同工艺下制备的Ti-2(wt％)Al-9.2(wt％)Mo-2(wt％)Fe合金板材纵截面组织进行对比，如附图4a和附图4b所示可知，采用本发明方法得到的板材显微组织中晶粒均匀细小，而2A2F合金板材组织中晶粒尺寸则较大，组织均匀性也差于2A2F10B合金。A rolled slab of 115 mm (length)×80 mm (width)×20 mm (thickness) is taken from the ingot shown in step S1. The slab was kept in a heating furnace at 900°C for 20 minutes, and then sent to a hot rolling mill for 4 passes of unidirectional hot rolling. The deformation of each pass was 25%, 20%, 15%, and 10%, and air cooled to After room temperature, surface blasting treatment is carried out to obtain a hot-rolled intermediate plate with a thickness of 6mm, and the edge of the plate is smooth without cracks. The intermediate plate was subjected to solution treatment at 850° C. for 30 minutes, and water quenched to obtain an alloy plate. Observe the longitudinal section microstructure of the plate, and compare it with the Ti-2(wt%)Al-9.2(wt%)Mo-2(wt%)Fe alloy plate longitudinal section prepared under the same process, as shown in Figure 4a and As shown in Figure 4b, it can be seen that the microstructure of the plate obtained by the method of the present invention has uniform and fine grains, while the grain size of the plate microstructure of the 2A2F alloy is larger, and the microstructure uniformity is also worse than that of the 2A2F10B alloy.
实施例3Example 3
S1.合金铸锭熔炼：S1. Alloy ingot melting:
按照Ti-2(wt％)Al-9.2(wt％)Mo-2(wt％)Fe-0.1(wt％)B合金成分要求，取相应重量的AlMo55、MoFe50、FeB20、Ti-32Mo中间合金和0级海绵钛，利用分层布料的方式压制电极，然后利用真空自耗电弧熔炼设备进行两次熔炼得到32Kg的合金扁形铸锭，以确保成分均匀。然后将铸锭表面扒皮，并利用化学法测试铸锭化学成分(表3)。通过淬火金相法测定其相变点为815±5℃。According to Ti-2 (wt%) Al-9.2 (wt%) Mo-2 (wt%) Fe-0.1 (wt%) B alloy composition requirement, get AlMo55, MoFe50, FeB20, Ti-32Mo master alloy of corresponding weight and Grade 0 titanium sponge, using layered cloth to press the electrode, and then using vacuum consumable arc melting equipment to melt twice to obtain a 32Kg alloy flat ingot to ensure uniform composition. Then the surface of the ingot was peeled off, and the chemical composition of the ingot was tested by chemical method (Table 3). The phase transition point was determined to be 815±5°C by quenching metallographic method.
表32 2A2F10B合金铸锭化学成分(质量含量)Table 32 2A2F10B alloy ingot chemical composition (mass content)
S2.板材轧制：S2. Plate rolling:
从步骤S1所示的铸锭上取115mm(长)×80mm(宽)×20mm(厚)的轧制板坯。将板坯在900℃的加热炉中保温20min，然后送入热轧机中进行4道次单向热轧，各道次变形量分别为40％、20％、15％、10％，空冷至室温后进行表面喷砂处理得到厚度为3mm的热轧中间板材，中间板材边缘光滑，且未出现明显裂纹。将板材在850℃下进行30min固溶处理，并水淬，得到合金板材。观察板材纵截面显微组织，并与相同工艺下制备的Ti-2Al-9.2Mo-2Fe合金板材纵截面显微组织进行对比，如附图5a和附图5b所示。可知，采用本发明方法得到的板材显微组织中晶粒尺寸细小，组织均匀性明显优于2A2F合金板材。从板材上沿着轧制方向取板状拉伸样品，根据GB/T228.1-2010测试其拉伸力学性能，并对比传统板材制备工艺得到的2A2F合金板材的拉伸力学性能，见表4所示，可知本发明方法制备得到的合金拉伸力学性能与传统板材制备工艺得到的相同合金板材相当。A rolled slab of 115 mm (length)×80 mm (width)×20 mm (thickness) is taken from the ingot shown in step S1. The slab was kept in a heating furnace at 900°C for 20 minutes, and then sent to a hot rolling mill for 4 passes of unidirectional hot rolling. The deformation of each pass was 40%, 20%, 15%, and 10%, and air-cooled After room temperature, the surface is sand blasted to obtain a hot-rolled intermediate plate with a thickness of 3 mm. The edge of the intermediate plate is smooth without obvious cracks. The plate was subjected to solution treatment at 850° C. for 30 minutes, and quenched in water to obtain an alloy plate. Observe the microstructure of the longitudinal section of the plate, and compare it with the microstructure of the longitudinal section of the Ti-2Al-9.2Mo-2Fe alloy plate prepared under the same process, as shown in Figure 5a and Figure 5b. It can be seen that the grain size in the microstructure of the plate obtained by the method of the present invention is fine, and the uniformity of the structure is obviously better than that of the 2A2F alloy plate. Take a plate-shaped tensile sample from the plate along the rolling direction, test its tensile mechanical properties according to GB/T228.1-2010, and compare the tensile mechanical properties of the 2A2F alloy plate obtained by the traditional plate preparation process, see Table 4 As shown, it can be seen that the tensile mechanical properties of the alloy prepared by the method of the present invention are equivalent to the same alloy sheet obtained by the traditional sheet preparation process.
表4本发明制备的2A2F10B合金板材与传统板材制备工艺制得的2A2F合金板材的拉伸力学性能The tensile mechanical properties of the 2A2F10B alloy sheet prepared by the present invention and the 2A2F alloy sheet prepared by the traditional sheet preparation process
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| CN201810804536.7ACN108977689B (en) | 2018-07-20 | 2018-07-20 | Metastable beta titanium alloy plate and processing method thereof |
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810804536.7ACN108977689B (en) | 2018-07-20 | 2018-07-20 | Metastable beta titanium alloy plate and processing method thereof |
| Publication Number | Publication Date |
|---|---|
| CN108977689Atrue CN108977689A (en) | 2018-12-11 |
| CN108977689B CN108977689B (en) | 2020-11-06 |
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201810804536.7AActiveCN108977689B (en) | 2018-07-20 | 2018-07-20 | Metastable beta titanium alloy plate and processing method thereof |
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|---|---|
| CN (1) | CN108977689B (en) |
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| CN109930100A (en)* | 2019-03-29 | 2019-06-25 | 中国科学院金属研究所 | A kind of damage tolerance titanium alloy plate rolling and mating heat treatment process |
| CN112662971A (en)* | 2020-10-28 | 2021-04-16 | 西安交通大学 | High-strength TWIP titanium alloy with gradient structure and hot rolling method thereof |
| CN112662971B (en)* | 2020-10-28 | 2022-05-20 | 西安交通大学 | A kind of high-strength TWIP titanium alloy with gradient structure and hot rolling method thereof |
| CN113174551A (en)* | 2021-03-30 | 2021-07-27 | 西安交通大学 | Dual-phase high-strength high-plasticity titanium alloy with heterogeneous laminated structure and preparation method thereof |
| CN116875830A (en)* | 2022-06-21 | 2023-10-13 | 中国科学院金属研究所 | Processing method of high-performance high-precision titanium alloy plate |
| CN115816933A (en)* | 2022-12-09 | 2023-03-21 | 西部金属材料股份有限公司 | Multilayer titanium alloy composite titanium alloy plate |
| CN119456672A (en)* | 2025-01-13 | 2025-02-18 | 江苏翔云钛合金新材料有限公司 | A low-cost preparation method for titanium alloy plate |
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