CN113293325A - Preparation method of high-strength Ti185 alloy - Google Patents
Preparation method of high-strength Ti185 alloy Download PDFInfo
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Abstract
The invention discloses a preparation method of a high-strength Ti185 alloy, which comprises the following steps: firstly, preparing Ti185 alloy spherical powder; secondly, carrying out electron beam selective melting on the Ti185 alloy spherical powder; and thirdly, carrying out solution treatment and aging treatment on the electron beam selective melting formed piece to obtain the high-strength Ti185 alloy, wherein the tensile strength of the high-strength Ti185 alloy is higher than 1298MPa, the tensile yield strength is higher than 1197MPa, and the elongation after fracture is higher than 6%. According to the invention, the Ti185 alloy powder in the selective melting process of the electron beam is preheated, so that the thermal stress in the Ti185 alloy is gradually released, the Ti185 alloy is prevented from Fe element segregation, the solution treatment and the aging treatment are carried out on the selective melting formed part of the electron beam, the precipitation of the nano alpha phase is promoted, the finally prepared Ti185 alloy has excellent mechanical properties, can be made into a high-strength part, and has a wide application range.
Description
Technical Field
The invention belongs to the technical field of alloy material preparation, and particularly relates to a preparation method of a high-strength Ti185 alloy.
Background
The titanium alloy has the characteristics of high specific strength, good corrosion resistance, small thermal expansion coefficient and good fatigue resistance, and has wide application in the industries of aerospace, petrochemical industry, automobiles, biomedical treatment and the like. Taking the boeing 787 dream passenger plane as an example, the titanium alloy used by the boeing 787 dream passenger plane accounts for 15% of the weight of the passenger plane, so far the passenger plane using the largest amount of titanium alloy is the passenger plane, compared with any other passenger plane of the same market grade, the boeing 787 dream passenger plane can save 20% of fuel, and is the most environment-friendly commercial passenger plane with the lowest oil consumption in the world at present.
The Ti-1Al-8V-5Fe (Ti185) alloy belongs to metastable beta titanium alloy, has higher tensile strength and shear strength, and is widely applied to aviation fasteners and parts with higher strength requirements; in addition, the alloy is lower in cost compared with other metastable beta titanium alloys, the Ti185 alloy contains higher content of low-cost Fe, and the cost of the alloy can be reduced by adding higher content of Fe compared with high-cost beta stable elements such as Mo, V, Cr and the like. However, researches show that when the content of Fe exceeding 2.5 wt% is added into the titanium alloy, the segregation of Fe element can be generated in the alloy smelting preparation process to form beta-spots, so that the mechanical property of the alloy is obviously reduced. In general, such component segregation is prevented by means of multiple melting, hot deformation, heat treatment, and the like in the alloy preparation process, which increases the preparation process and cost.
Disclosure of Invention
The technical problem to be solved by the present invention is to provide a method for preparing a high strength Ti185 alloy, aiming at the above-mentioned deficiencies of the prior art. According to the method, the Ti185 alloy spherical powder of each sheet layer in the selective melting process of the electron beam is preheated, so that the internal thermal stress of the Ti185 alloy is gradually released, the internal structure of the Ti185 alloy tends to be uniform, the Fe element segregation in the Ti185 alloy is avoided, meanwhile, the solution treatment and the aging treatment are carried out on the selective melting forming piece of the electron beam, the precipitation of a nano alpha phase is promoted, the micron and nano alpha are distributed in the beta crystal grain partially, a multi-scale microstructure is formed, and the strength and the plasticity of the Ti185 alloy are comprehensively improved.
In order to solve the technical problems, the invention adopts the technical scheme that: the preparation method of the high-strength Ti185 alloy is characterized in that the Ti185 alloy consists of the following components in percentage by mass: 0.8 to 1.5 percent of Al, 7.5 to 8.5 percent of V, 4.0 to 6.0 percent of Fe, 0.1 to 0.2 percent of O, and the balance of titanium and inevitable impurities;
the preparation method comprises the following steps:
the method comprises the following steps: burdening according to the design components of a target product Ti185 alloy, mixing the burdening, pressing into an electrode block, and then manufacturing into an electrode rod in a vacuum consumable electrode furnace;
step two: loading the electrode rod obtained in the step one into plasma rotating electrode atomization powder making equipment, starting the equipment under a vacuum condition, and carrying out atomization powder making on the electrode rod to obtain atomized powder;
step three: sieving the atomized powder obtained in the step two to obtain Ti185 alloy spherical powder;
step four: drawing a three-dimensional model of a target product Ti185 alloy, then carrying out layering treatment, cutting the model into equal-thickness slices along the height direction of the model to obtain slicing data, and designing the internal scanning mode and scanning path of each slice to obtain slicing scanning data;
step five: guiding the layer cutting data and the layer cutting scanning data obtained in the fourth step into powder bed type electron beam additive manufacturing forming equipment, loading the Ti185 alloy spherical powder obtained in the third step into a powder box of the powder bed type electron beam additive manufacturing equipment, leveling a forming bottom plate and preheating the forming bottom plate, wherein the preheating temperature of the forming bottom plate is 680-750 ℃;
step six: laying the Ti185 alloy spherical powder loaded into the powder box in the step five on the preheated forming bottom plate to form a powder layer, and then preheating the powder layer, wherein the preheating temperature of the powder layer is 680-750 ℃, and the laying thickness of the Ti185 alloy spherical powder is the same as that of each layer in the step four;
step seven: according to the layer cutting data and the layer cutting scanning data introduced into the powder bed type electron beam additive manufacturing forming equipment in the step five, the preheated powder layer is subjected to melting scanning by adopting an electron beam to form a single-layer solid sheet layer, then the forming bottom plate is lowered, and the lowering height of the forming bottom plate is the same as the thickness of each sheet layer in the step four;
step eight: repeating the powder laying process, the preheating process, the melting scanning process and the forming bottom plate descending process in the step six until all the single-layer solid sheet layers are stacked layer by layer to form an electron beam selective melting forming piece, taking out the electron beam selective melting forming piece when the temperature of the forming bottom plate is lower than 100 ℃, and removing residual powder on the surface of the electron beam selective melting forming piece by using high-pressure gas;
step nine: carrying out solid solution treatment on the electron beam selective melting formed piece obtained in the step eight for 0.5-1.5 h at the temperature of 600-730 ℃, then carrying out water quenching, carrying out aging treatment for 3-5 h at the temperature of 400-500 ℃, and finally carrying out air cooling to room temperature to obtain the high-strength Ti185 alloy; the tensile strength of the high-strength Ti185 alloy is higher than 1298MPa, the tensile yield strength is higher than 1197MPa, and the elongation after fracture is higher than 6%.
The method adopts a plasma rotating electrode atomization powder preparation mode, so that the electrode rod undergoes a process of centrifugally solidifying molten liquid drops into powder, the prepared atomized powder has high sphericity and fine particle size, and the spherical powder is easy to disperse, thereby being beneficial to improving the tissue uniformity of the Ti185 alloy; the Ti185 alloy is prepared by adopting an electron beam selective melting forming method, the spherical powder of the Ti185 alloy and a forming bottom plate are preheated, the preheating temperature is controlled to be 680-750 ℃, each layer of the prepared Ti185 alloy is subjected to repeated heat treatment, the internal thermal stress of the Ti185 alloy is gradually released, the internal structure of the Ti185 alloy tends to be uniform, meanwhile, the spherical powder of the Ti185 alloy is preheated and then melted for scanning, the preheating is favorable for the adhesion of elements in the Ti185 alloy, the movement caused by the impact of electron beams is avoided, the binding force between layers of the Ti185 alloy is improved, the component segregation of the prepared Ti185 alloy is also favorably avoided, particularly the beta spot defect caused by the segregation of Fe element is avoided, and the strength of the Ti185 alloy is influenced; according to the invention, through carrying out solution treatment and aging treatment on the Ti185 alloy, the precipitation of a nano alpha phase is promoted, so that micro and nano alpha are distributed in a beta grain part to form a multi-scale microstructure, and further the mechanical property of the Ti185 alloy is improved, and meanwhile, 0.1-0.2% of O element added into the Ti185 alloy can play a role in solution strengthening, the fracture toughness of the Ti185 alloy is improved, and the strength of the Ti185 alloy is further improved.
The preparation method of the high-strength Ti185 alloy is characterized in that the manufacturing process of the electrode rod in the first step is as follows: putting the electrode block into a vacuum self-consuming furnace for vacuum sintering, grinding, chamfering, welding, smelting and forging, wherein the vacuum degree in the vacuum self-consuming furnace is less than 1 multiplied by 10-3Pa. According to the invention, the electrode block is subjected to vacuum sintering, polishing, chamfering, welding, smelting and forging processing, so that the electrode block is subjected to preliminary alloying and component homogenization, harmful volatile substances and gases are eliminated, and the uniform distribution of components in subsequent atomized powder is facilitated; the influence of impurity gas on the purity of the Ti185 alloy is reduced by controlling the vacuum degree in the processing process, and meanwhile, the sintering and smelting temperatures can be reduced under the vacuum condition, so that the manufacturing cost is saved.
The preparation method of the high-strength Ti185 alloy is characterized in that the plasma rotating electrode atomization in the step twoVacuum degree in powder making equipment is less than 1 x 10-3Pa. According to the invention, by controlling the vacuum degree in the plasma rotary electrode atomization powder making equipment, the influence of other impurity gases on the components in the Ti185 alloy is effectively avoided, so that the finally prepared Ti185 alloy spherical powder has low impurity content, and meanwhile, by controlling the vacuum degree instead of using inert protective gas, the alloy performance is ensured and the production cost is reduced.
The preparation method of the high-strength Ti185 alloy is characterized in that the particle size of the Ti185 alloy spherical powder in the step three is 40-150 mu m. The Ti185 alloy spherical powder with the particle size has better fluidity, is beneficial to spreading the Ti185 alloy spherical powder on a forming bottom plate, improves the uniformity of laying a powder layer, further improves the uniformity of each component in the Ti185 alloy, avoids the occurrence of composition segregation phenomenon, and is beneficial to improving the melting speed in the selective melting process of electron beams.
The preparation method of the high-strength Ti185 alloy is characterized in that drawing software of the three-dimensional model in the fourth step is Magics, and the thickness of the sheet layer in the fourth step is 0.05-0.1 mm. The thickness of the lamella is the powder spreading thickness, and the thickness of the lamella is set to be 0.05 mm-0.1 mm so as to adapt to the melting capability of the electron beam to the Ti185 alloy spherical powder.
The preparation method of the high-strength Ti185 alloy is characterized in that in the fifth step, the operating environment humidity of the powder bed type electron beam additive manufacturing forming equipment is not higher than 40%. According to the invention, the humidity of the environment where the powder bed electron beam additive manufacturing forming equipment is located is controlled, so that moisture in the environment is prevented from entering Ti185 alloy powder, and the influence on the finally prepared alloy performance is further avoided.
The preparation method of the high-strength Ti185 alloy is characterized in that the process parameters of the melting scanning in the sixth step are as follows: the distance between the scanning lines is 0.1mm, the scanning current is 9 mA-15 mA, and the scanning speed is 2000 mm/s-3300 mm/s. The Ti185 alloy is prepared by performing electron beam selective melting on the Ti185 alloy spherical powder by adopting the forming parameters, so that the dimensional accuracy and the melting quality of each sheet layer in the forming process are effectively controlled, the prepared Ti185 alloy forming piece is uniform in inside and complete in shape, and the strength of the Ti185 alloy is favorably improved; meanwhile, on the premise of meeting the melting requirement, the invention properly adopts smaller scanning current, creates good conditions for the solidification of the Ti185 alloy, effectively inhibits the occurrence of crystallization segregation, ensures that the internal structure of the prepared Ti185 alloy is uniform, and further improves the strength of the Ti185 alloy.
The preparation method of the high-strength Ti185 alloy is characterized in that in the eighth step, the density of the selective electron beam melting formed part is not lower than 4.68g/cm3. The Ti185 alloy spherical powder adopted by the invention has high component uniformity, and the uniformity of each component in the Ti185 alloy is further improved through the selective electron beam melting process of preheating and then scanning melting, so that the density of the prepared selective electron beam melting formed part is high, and the density and the mechanical property of the selective electron beam melting formed part are further improved.
Compared with the prior art, the invention has the following advantages:
1. the Ti185 alloy is prepared by adopting an electron beam selective melting forming method, the spherical powder of the Ti185 alloy and a forming bottom plate are preheated, the preheating temperature is controlled to be 680-750 ℃, each layer of the prepared Ti185 alloy is subjected to repeated heat treatment, the internal thermal stress of the Ti185 alloy is gradually released, the internal structure of the Ti185 alloy tends to be uniform, the prepared Ti185 alloy is prevented from generating component segregation, and particularly the defect of beta spot generated by the segregation of Fe element is avoided.
2. According to the invention, through carrying out solution treatment and aging treatment on the Ti185 alloy, the precipitation of a nano alpha phase is promoted, so that micro and nano alpha are distributed in a beta grain part to form a multi-scale microstructure, and further the mechanical property of the Ti185 alloy is improved, and meanwhile, 0.1-0.2% of O element added into the Ti185 alloy can play a role in solution strengthening, the fracture toughness of the Ti185 alloy is improved, and the strength of the Ti185 alloy is further improved.
3. According to the invention, the electrode block is subjected to vacuum sintering, grinding, chamfering, welding, smelting and forging processing, so that the electrode block is subjected to preliminary alloying and component homogenization, harmful volatile substances and gases are eliminated, the components in subsequent atomized powder are uniformly distributed, and the influence of impurity gases on the purity of the Ti185 alloy is reduced by controlling the vacuum degree in the processing process.
4. According to the invention, through the selective melting of electron beams and the solution aging treatment process, the finally prepared Ti185 alloy has no beta spot defect, the tensile strength of the Ti185 alloy is higher than 1298MPa, the tensile yield strength is higher than 1197MPa, the elongation after fracture is higher than 6%, and the Ti185 alloy can be made into a high-strength part and has a wide application range.
The technical solution of the present invention is further described in detail by the accompanying drawings and examples.
Drawings
FIG. 1 is an SEM image of a high strength Ti185 alloy prepared in example 1 of the present invention.
FIG. 2 is a TEM image of a Ti185 alloy prepared in comparative example 3 of the present invention.
Detailed Description
Example 1
The high-strength Ti185 alloy of the embodiment comprises the following components in percentage by mass: al: 1.0%, V: 8.0%, Fe: 5.0%, O: 0.1%, the balance being titanium and unavoidable impurities; the preparation method comprises the following steps:
step one, mixing the components, pressing the mixture into an electrode block, and then putting the electrode block into a vacuum self-consuming furnace to be processed into an electrode rod through vacuum sintering, polishing, chamfering, welding, smelting and forging; wherein the vacuum degree in the vacuum self-consuming furnace is less than 1 x 10-3Pa；
Step two, the electrode bar obtained in the step one is put into plasma rotating electrode atomization powder manufacturing equipment, and the vacuum degree is less than 1 multiplied by 10-3Under the condition of Pa, starting a plasma gun and a rotating motor in plasma rotating electrode atomization powder making equipment to atomize and make powder on an electrode rod to obtain atomized powder;
step three, sieving the atomized powder obtained in the step two to obtain Ti185 alloy spherical powder, wherein the particle size of the Ti185 alloy spherical powder is 40-150 microns;
step four, adopting Magics software to draw a three-dimensional model of a target product Ti185 alloy, wherein the size of the model is 90mm multiplied by 17mm multiplied by 70mm (length multiplied by width multiplied by height), and cutting the three-dimensional model into 0.1mm slices with equal thickness along the height direction, setting the distance of the tracing lines to be 0.1mm, the scanning current to be 15mA, and the scanning speed to be 3300 mm/s;
step five, importing the slice data and slice scanning data obtained in the step four into powder bed type electron beam additive manufacturing forming equipment, wherein the equipment model adopted in the embodiment is a sialon S200 type; loading 20Kg of Ti185 alloy spherical powder obtained in the third step into a powder box of powder bed type electron beam additive manufacturing equipment, leveling a forming bottom plate and preheating the forming bottom plate, wherein the preheating temperature of the forming bottom plate is 720 ℃, the size of the forming bottom plate is 120mm multiplied by 10mm (length multiplied by width multiplied by thickness), and the environmental humidity of the powder bed electron beam additive manufacturing forming equipment is less than or equal to 40%;
step six, laying the Ti185 alloy spherical powder loaded into the powder box in the step five on the preheated forming bottom plate to form a powder layer, wherein the thickness of the powder layer is 0.1mm, and preheating the powder layer on the forming bottom plate at 720 ℃;
seventhly, according to the layer cutting data and the layer cutting scanning data which are led into the powder bed type electron beam additive manufacturing forming equipment in the step five, melting and scanning the preheated powder layer by adopting an electron beam to form a single-layer solid sheet layer, and then lowering the forming bottom plate by 0.1 mm;
step eight, repeating the powder laying process, the preheating process, the melting scanning process and the forming bottom plate descending process in the step six until all the single-layer solid sheet layers are stacked layer by layer to form an electron beam selective melting forming piece, taking out the electron beam selective melting forming piece when the temperature of the forming bottom plate is lower than 100 ℃, removing residual powder on the surface of the electron beam selective melting forming piece by using high-pressure gas, and detecting that the density of the Ti185 alloy forming sample is 4.69g/cm3；
And step nine, carrying out solution treatment on the electron beam selective melting formed piece obtained in the step eight at 675 ℃ for 1h, then carrying out water quenching, carrying out aging treatment at 440 ℃ for 4h, and carrying out air cooling to room temperature to obtain the high-strength Ti185 alloy.
Through detection, the tensile strength of the high-strength Ti185 alloy prepared in the embodiment is 1298MPa, the tensile yield strength is 1197MPa, and the elongation after fracture is 12.5%.
Fig. 1 is a scanning electron microscope image of the high-strength Ti185 alloy prepared in example 1 of the present invention, and it can be seen from the image that the high-strength Ti185 alloy has micron and nanometer α inside, i.e., the β crystal grains have multi-scale α reinforcing phase inside.
Comparative example 1
This comparative example differs from example 1 in that: in the sixth step of the comparative example, the preheating temperature of the powder layer on the forming bottom plate is 350 ℃, after the preheating is finished, the powder bed type electron beam additive manufacturing forming equipment starts an electron beam, the powder blowing phenomenon occurs, and the forming test is ended.
Comparative example 2
This comparative example differs from example 1 in that: in the sixth step of the comparative example, the preheating temperature of the powder layer on the forming bottom plate is 800 ℃, the phenomenon of peeling occurs in the preheating process of the Ti185 alloy spherical powder in the forming bottom plate, and the forming test is ended.
Comparative example 3
This comparative example differs from example 1 in that: the treatment process for the selective electron beam melting forming part in the ninth step of the comparative example comprises the following steps: solution treatment is carried out for 0.5h at the temperature of 760 ℃, then water quenching is carried out, aging treatment is carried out for 2h at the temperature of 490 ℃, and air cooling is carried out to room temperature, thus obtaining the Ti185 alloy.
The Ti185 alloy prepared by the comparative example is detected to have the tensile strength of 1141MPa and brittle fracture.
FIG. 2 is a TEM image of the Ti185 alloy prepared in comparative example 3 of the present invention, and it can be seen that the Ti185 alloy sample has a brittle phase w inside, and the mechanical properties of the Ti185 alloy prepared in the comparative example are poor.
As can be seen from the comparison of example 1 and comparative example 1, when the preheating temperature of the powder layer is set at 350 ℃, i.e., a lower preheating temperature of the powder layer, the Ti185 alloy spherical powder is not fully melted and adhered in advance, and the powder blowing phenomenon occurs during the scanning process of the electron beam; comparing example 1 and comparative example 2, it can be known that, the preheating temperature of the powder layer is set at 800 ℃, that is, a higher preheating temperature of the powder layer, the spherical powder of Ti185 alloy is prone to uneven heating at high temperature, the surface temperature is too high, the peeling defect occurs, and the quality of the final product is affected, therefore, example 1 sets the preheating temperature of the powder layer at 720 ℃, so that the spherical powder of Ti185 alloy is adhered in the preheating process, the powder blowing phenomenon in the electron beam scanning process is avoided, the peeling defect caused by uneven heating due to too high temperature is avoided, meanwhile, the powder of the preheated powder layer is adhered and then is melted and scanned, which is beneficial to avoiding the powder layer moving caused by the impact of the electron beam, and further, the forming precision and the component uniformity of the melted part in the electron beam selection area are improved.
By comparing the embodiment 1 with the comparative example 3 and comparing fig. 1 with fig. 2, it can be known that after the solution treatment and the aging treatment in the embodiment 1, the electron beam selective melting formed piece has a multi-scale α -reinforced phase in the Ti185 alloy, and the treatment process in the comparative example 3 obtains a brittle phase w in the Ti185 alloy, so that by adopting the solution treatment and the aging treatment process in the embodiment 1 of the present invention, the multi-scale α -reinforced phase in the Ti185 alloy is effectively promoted, and the mechanical properties of the prepared Ti185 alloy are further improved.
Example 2
The high-strength Ti185 alloy of the embodiment comprises the following components in percentage by mass: al: 0.8%, V: 8.5%, Fe: 6.0%, O: 0.2%, the balance being titanium and unavoidable impurities; the preparation method comprises the following steps:
step one, mixing the components, pressing the mixture into an electrode block, and then putting the electrode block into a vacuum self-consuming furnace to be processed into an electrode rod through vacuum sintering, polishing, chamfering, welding, smelting and forging; wherein the vacuum degree in the vacuum self-consuming furnace is less than 1 x 10-3Pa；
Step two, the electrode bar obtained in the step one is put into plasma rotating electrode atomization powder manufacturing equipment, and the vacuum degree is less than 1 multiplied by 10-3Under the condition of Pa, starting a plasma gun and a rotating motor in plasma rotating electrode atomization powder making equipment to atomize and make powder on an electrode rod to obtain atomized powder;
step three, sieving the atomized powder obtained in the step two to obtain Ti185 alloy spherical powder, wherein the particle size of the Ti185 alloy spherical powder is 40-150 microns;
step four, drawing a three-dimensional model of the Ti185 alloy forming sample by adopting Magics software, wherein the size of the model is 90mm multiplied by 17mm multiplied by 70mm (length multiplied by width multiplied by height), and dividing the three-dimensional model into 0.05mm slices with consistent thickness along the height direction, setting the line drawing distance to be 0.1mm, the scanning current to be 12mA, and the scanning speed to be 2700 mm/s;
introducing the three-dimensional model into powder bed electron beam additive manufacturing forming equipment, wherein the equipment model is a sialon S200 type;
step five, importing the layer cutting data and the layer cutting scanning data obtained in the step four into powder bed type electron beam additive manufacturing forming equipment, wherein the equipment model adopted by the invention is a sialon S200 type; loading 20Kg of Ti185 alloy spherical powder obtained in the third step into a powder box of powder bed type electron beam additive manufacturing equipment, leveling a forming bottom plate and preheating the forming bottom plate, wherein the preheating temperature of the forming bottom plate is 680 ℃, the size of the forming bottom plate is 120mm multiplied by 10mm (length multiplied by width multiplied by thickness), and the environmental humidity of the powder bed electron beam additive manufacturing forming equipment is less than or equal to 40%;
step six, laying the Ti185 alloy spherical powder loaded into the powder box in the step five on the preheated forming bottom plate to form a powder layer, wherein the thickness of the powder layer is 0.05mm, and preheating the powder layer on the forming bottom plate at 680 ℃;
seventhly, according to the layer cutting data and the layer cutting scanning data which are led into the powder bed type electron beam additive manufacturing forming equipment in the step five, melting and scanning the preheated powder layer by adopting an electron beam to form a single-layer solid sheet layer, and then descending the forming bottom plate by 0.05 mm;
step eight, repeating the powder laying process, the preheating process, the melting scanning process and the forming bottom plate descending process in the step six until all the single-layer solid sheet layers are stacked layer by layer to form an electron beam selective melting forming piece, taking out the electron beam selective melting forming piece when the temperature of the forming bottom plate is lower than 100 ℃, removing residual powder on the surface of the electron beam selective melting forming piece by using high-pressure gas,the density of the Ti185 alloy formed sample was detected to be 4.69g/cm3；
And step nine, carrying out solution treatment on the electron beam selective melting formed piece obtained in the step eight at 600 ℃ for 1.5h, then carrying out water quenching, carrying out aging treatment at 500 ℃ for 3h, and carrying out air cooling to room temperature to obtain the high-strength Ti185 alloy.
Through detection, the tensile strength of the high-strength Ti185 alloy prepared in the embodiment is 1316MPa, the tensile yield strength is 1212MPa, and the elongation after fracture is 11.0%.
Example 3
The high-strength Ti185 alloy of the embodiment comprises the following components in percentage by mass: al: 1.5%, V: 7.5%, Fe: 4.0%, O: 0.1%, the balance being titanium and unavoidable impurities; the preparation method comprises the following steps:
step one, mixing the components, pressing the mixture into an electrode block, and then putting the electrode block into a vacuum self-consuming furnace to be processed into an electrode rod through vacuum sintering, polishing, chamfering, welding, smelting and forging; wherein the vacuum degree in the vacuum self-consuming furnace is less than 1 x 10-3Pa；
Step two, the electrode bar obtained in the step one is put into plasma rotating electrode atomization powder manufacturing equipment, and the vacuum degree is less than 1 multiplied by 10-3Under the condition of Pa, starting a plasma gun and a rotating motor in plasma rotating electrode atomization powder making equipment to atomize and make powder on an electrode rod to obtain atomized powder;
step three, sieving the atomized powder obtained in the step two to obtain Ti185 alloy spherical powder, wherein the particle size of the Ti185 alloy spherical powder is 40-150 microns;
step four, drawing a three-dimensional model of the Ti185 alloy forming sample by adopting Magics software, wherein the size of the model is 90mm multiplied by 17mm multiplied by 70mm (length multiplied by width multiplied by height), and dividing the three-dimensional model into 0.08 mm-thick lamella along the height direction, setting the line drawing distance to be 0.1mm, the scanning current to be 9mA, and the scanning speed to be 2000 mm/s;
step five, importing the layer cutting data and the layer cutting scanning data obtained in the step four into powder bed type electron beam additive manufacturing forming equipment, wherein the equipment model adopted by the invention is a sialon S200 type; loading 20Kg of Ti185 alloy spherical powder obtained in the third step into a powder box of powder bed type electron beam additive manufacturing equipment, leveling a forming bottom plate and preheating the forming bottom plate, wherein the preheating temperature of the forming bottom plate is 750 ℃, the size of the forming bottom plate is 120mm multiplied by 10mm (length multiplied by width multiplied by thickness), and the environmental humidity of the powder bed electron beam additive manufacturing forming equipment is less than or equal to 40%;
step six, laying the Ti185 alloy spherical powder loaded into the powder box in the step five on the preheated forming bottom plate to form a powder layer, wherein the thickness of the powder layer is 0.08mm, and preheating the powder layer on the forming bottom plate at 750 ℃;
seventhly, according to the layer cutting data and the layer cutting scanning data which are led into the powder bed type electron beam additive manufacturing forming equipment in the step five, melting and scanning the preheated powder layer by adopting an electron beam to form a single-layer solid sheet layer, and then descending the forming bottom plate by 0.08 mm;
step eight, repeating the powder laying process, the preheating process, the melting scanning process and the forming bottom plate descending process in the step six until all the single-layer solid sheet layers are stacked layer by layer to form an electron beam selective melting forming piece, taking out the electron beam selective melting forming piece when the temperature of the forming bottom plate is lower than 100 ℃, removing residual powder on the surface of the electron beam selective melting forming piece by using high-pressure gas, and detecting that the density of the Ti185 alloy forming sample is 4.68g/cm3；
And step nine, carrying out solution treatment on the electron beam selective melting formed piece obtained in the step eight at 730 ℃ for 0.5h, then carrying out water quenching, carrying out aging treatment at 400 ℃ for 5h, and carrying out air cooling to room temperature to obtain the high-strength Ti185 alloy.
Through detection, the tensile strength of the high-strength Ti185 alloy prepared in the embodiment is 1309MPa, the tensile yield strength is 1202MPa, and the elongation after fracture is 6.0%.
The above description is only for the preferred embodiment of the present invention, and is not intended to limit the present invention in any way. Any simple modification, change and equivalent structural changes of the above embodiments according to the technical essence of the invention are still within the protection scope of the technical solution of the invention.
Claims (8)
1. The preparation method of the high-strength Ti185 alloy is characterized in that the Ti185 alloy consists of the following components in percentage by mass: 0.8 to 1.5 percent of Al, 7.5 to 8.5 percent of V, 4.0 to 6.0 percent of Fe, 0.1 to 0.2 percent of O, and the balance of titanium and inevitable impurities;
the preparation method comprises the following steps:
the method comprises the following steps: burdening according to the design components of a target product Ti185 alloy, mixing the burdening, pressing into an electrode block, and then manufacturing into an electrode rod in a vacuum consumable electrode furnace;
step two: loading the electrode rod obtained in the step one into plasma rotating electrode atomization powder making equipment, starting the equipment under a vacuum condition, and carrying out atomization powder making on the electrode rod to obtain atomized powder;
step three: sieving the atomized powder obtained in the step two to obtain Ti185 alloy spherical powder;
step four: drawing a three-dimensional model of a target product Ti185 alloy, then carrying out layering treatment, cutting the model into equal-thickness slices along the height direction of the model to obtain slicing data, and designing the internal scanning mode and scanning path of each slice to obtain slicing scanning data;
step five: guiding the layer cutting data and the layer cutting scanning data obtained in the fourth step into powder bed type electron beam additive manufacturing forming equipment, loading the Ti185 alloy spherical powder obtained in the third step into a powder box of the powder bed type electron beam additive manufacturing equipment, leveling a forming bottom plate and preheating the forming bottom plate, wherein the preheating temperature of the forming bottom plate is 680-750 ℃;
step six: laying the Ti185 alloy spherical powder loaded into the powder box in the step five on the preheated forming bottom plate to form a powder layer, and then preheating the powder layer, wherein the preheating temperature of the powder layer is 680-750 ℃, and the laying thickness of the Ti185 alloy spherical powder is the same as that of each layer in the step four;
step seven: according to the layer cutting data and the layer cutting scanning data introduced into the powder bed type electron beam additive manufacturing forming equipment in the step five, the preheated powder layer is subjected to melting scanning by adopting an electron beam to form a single-layer solid sheet layer, then the forming bottom plate is lowered, and the lowering height of the forming bottom plate is the same as the thickness of each sheet layer in the step four;
step eight: repeating the powder laying process, the preheating process, the melting scanning process and the forming bottom plate descending process in the step six until all the single-layer solid sheet layers are stacked layer by layer to form an electron beam selective melting forming piece, taking out the electron beam selective melting forming piece when the temperature of the forming bottom plate is lower than 100 ℃, and removing residual powder on the surface of the electron beam selective melting forming piece by using high-pressure gas;
step nine: carrying out solid solution treatment on the electron beam selective melting formed piece obtained in the step eight for 0.5-1.5 h at the temperature of 600-730 ℃, then carrying out water quenching, carrying out aging treatment for 3-5 h at the temperature of 400-500 ℃, and finally carrying out air cooling to room temperature to obtain the high-strength Ti185 alloy; the tensile strength of the high-strength Ti185 alloy is higher than 1298MPa, the tensile yield strength is higher than 1197MPa, and the elongation after fracture is higher than 6%.
2. The method for preparing a high-strength Ti185 alloy as claimed in claim 1, wherein the electrode rod in the first step is manufactured by the following steps: putting the electrode block into a vacuum self-consuming furnace for vacuum sintering, grinding, chamfering, welding, smelting and forging, wherein the vacuum degree in the vacuum self-consuming furnace is less than 1 multiplied by 10-3Pa。
3. The method of claim 1, wherein the vacuum degree in the plasma rotating electrode atomization powder producing apparatus in the second step is less than 1 x 10-3Pa。
4. The method for preparing a high-strength Ti185 alloy as claimed in claim 1, wherein the particle size of the Ti185 alloy spherical powder in step three is 40 μm-150 μm.
5. The method according to claim 1, wherein the software for drawing the three-dimensional model in step four is Magics, and the thickness of the sheet layer in step four is 0.05mm to 0.1 mm.
6. The method according to claim 1, wherein the operating environment humidity of the powder bed type electron beam additive manufacturing and forming device in the fifth step is not higher than 40%.
7. The method for preparing the high-strength Ti185 alloy according to claim 1, wherein the process parameters of the melting scan in the sixth step are as follows: the distance between the scanning lines is 0.1mm, the scanning current is 9 mA-15 mA, and the scanning speed is 2000 mm/s-3300 mm/s.
8. The method of claim 1, wherein the density of the selectively melted electron beam formed part in step eight is not less than 4.68g/cm3。
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