CN111940538B - Cold rolling method for TC27 titanium alloy pipe - Google Patents

Cold rolling method for TC27 titanium alloy pipe Download PDF

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CN111940538B
CN111940538B CN202010727597.5A CN202010727597A CN111940538B CN 111940538 B CN111940538 B CN 111940538B CN 202010727597 A CN202010727597 A CN 202010727597A CN 111940538 B CN111940538 B CN 111940538B
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cold rolling
titanium alloy
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tube blank
tube
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CN111940538A (en
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齐立春
张业勤
张明杰
黄旭
黄利军
沙爱学
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AECC Beijing Institute of Aeronautical Materials
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/78—Control of tube rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon

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Abstract

The invention discloses a cold rolling method of TC27 titanium alloy pipes, which comprises the steps of smelting TC27 titanium alloy ingots, carrying out homogenization annealing, cogging the ingots, forging, hot rolling and perforating, and pretreating the pipes before cold rolling; the pretreatment process comprises the following steps: heating the electric furnace to (T)β+20)℃～(Tβ+40) DEG C, and then loading the tube blank into the tube blank at the temperature, wherein the heat preservation time is calculated according to 0.8 min/mm-1.0 min/mm by taking the wall thickness of the tube blank as a base number, and the cooling speed is ensured to be more than or equal to 30 ℃/s; the method has simple process parameter setting, convenient operation and controllable process flow, can improve the cold rolling deformation and reduce the cold rolling pass after pretreatment before cold rolling, and can ensure that the room temperature tensile strength of the pipe is more than or equal to 1150MPa, the yield strength is more than or equal to 1050MPa, the elongation delta is more than or equal to 10 percent, the section shrinkage phi is more than or equal to 20 percent, and the fracture toughness of the pipe is more than or equal to 3.5 percent of NaCl aqueous solution at room temperature through aging treatment after cold rolling
Figure DDA0002600528300000011

Description

Cold rolling method for TC27 titanium alloy pipe
Technical Field
The invention belongs to the technical field of titanium alloy preparation, relates to a pretreatment method of a TC27 titanium alloy pipe before cold rolling, and particularly relates to a pretreatment method of a TC27 titanium alloy pipe before cold rolling, which has high strength, high toughness and marine environment corrosion resistance.
Background
With the increasing shortage of available resources on land, ocean space and resources have become an important area of world military and economic competition that is increasingly intense. At present, exploration, development and utilization of offshore resources are rapidly developing to deep sea areas, and deep sea space and oil and gas resources become strategic spaces and bases for human survival, development of social places and continuous Thai prosperity in coastal countries. The development of deep sea oil and gas resources cannot be completed by the improvement of an ocean engineering equipment system, and the deep sea oil and gas resource development equipment is greatly different from land oil and gas resource development equipment due to the influence of various complex factors such as water depth, environmental conditions, geological conditions, oil reservoir characteristics and the like. The ocean engineering equipment is huge, particularly the deep sea environment is very severe, the mining difficulty is large, the risk is high, the requirements of seawater corrosion, surge, ocean current environment, ocean vortex-induced vibration, deep water pressure and the like on the materials for the ocean engineering equipment are extremely severe, and the materials with high strength, good corrosion resistance, no magnetism and the like and excellent comprehensive performance are required. Ocean engineering equipment materials are developing towards the trends and directions of high strength, high toughness, light weight, good welding performance and the like. The titanium alloy has the advantages of low density, high specific strength, good corrosion resistance, high impact resistance, seawater scouring resistance, no magnetism, no cold brittleness, high sound transmission coefficient, good forming, casting and welding properties and the like. Therefore, titanium alloy is increasingly applied to ocean engineering equipment, is known as 'ocean metal', and has become one of the main civil fields.
In the exploration and exploitation of offshore oil and gas resources, titanium alloys were first adopted in the united states and russia to manufacture oceanographic engineering equipment. In the early 70 s of the last century in the united states, titanium alloys were used in their oil fields to make offshore oil platform legs, while tubular and plate heat exchangers, etc. were made of titanium. At present, titanium alloy is widely used abroad to manufacture offshore oil platform pillars, drill rods, feeler levers, flexible shafts of screw drilling tools, drilling vertical pipes, oil production pipes, joints, lifting drilling tool devices, drilling boosters, sampling rooms, underwater safety valves and other ocean engineering equipment. Among them, titanium alloys commonly used in the U.S. for manufacturing ocean engineering equipment include medium-strength and high-strength titanium alloys, mainly including gr.5, gr.6, gr.7, gr.9, gr.11, gr.12, gr.18, gr.19, gr.23, gr.28, gr.29, and titanium alloys commonly used in russia mainly include OT3, BT5-1, PT7M, PT3B, BT6, etc. Titanium alloy drill pipes provided by RMI of the United states for Conoco Norway Inc. have been successfully applied to tens of oil wells, saving system cost by 40%. Compared with the traditional steel drill rod, the vertical depth of the titanium alloy drill rod can reach 9200 m, while the vertical depth of the steel drill rod is 6100 m, the use of the titanium alloy drill rod can reduce the pulling force of the rod by 30 percent, and obviously reduce the torque by 30 to 40 percent.
The titanium alloy mainly used by ocean engineering equipment in China is Ti31, Ti75, Ti80, TC4 and the like with medium strength level, and is mainly applied to ships, and the amount of the used titanium alloy is very small. Therefore, the titanium alloy material and the application technology commonly used in China at present can not meet the development requirements of offshore oil and gas resource exploration and exploitation equipment, the difference from foreign countries is large, the technical level is lagged behind, so that the oil extraction system, the oil storage system, the petroleum primary processing equipment and the like of ocean engineering equipment completely depend on import, the import rate of the ocean engineering equipment reaches 70% -90%, and the development of ocean engineering in China is severely restricted.
The TC27 titanium alloy (the component is disclosed in Chinese patent CN101503771B) is a titanium alloy which is independently developed in China and has a series of advantages of high specific strength, good fracture toughness, strong stress corrosion resistance and the like, belongs to a high-strength grade titanium alloy, has the tensile strength of more than 1100MPa, and is particularly suitable for replacing traditional high-strength steel to manufacture a drill rod, so that the effect of reducing the weight of the drill rod is realized, and the purposes of reducing the pulling force of the drill rod and reducing the torque are achieved.
The method generally adopted by the publicly reported titanium alloy seamless tube mainly comprises the steps of extruding a pierced billet, then carrying out multi-pass cold rolling or cold drawing, carrying out cross rolling and piercing on the pierced billet, and then carrying out multi-pass cold rolling, and is generally directed at the titanium alloy with medium strength (the yield strength is 700 MPa-800 MPa), because the alloy hardness is low after the pierced billet is manufactured by thermal deformation, the deformation resistance is low, the cold rolling difficulty is low, and pretreatment is not needed before cold rolling or only air cooling treatment after common annealing is needed. Aiming at high strength and high toughness (yield strength is more than 1050MPa, fracture toughness)
Figure BDA0002600528290000021
Figure BDA0002600528290000022
) Titanium alloy tube material ofThe published report of pretreatment before the cold rolling process.
The TC27 titanium alloy has high strength and large deformation resistance, and the Rockwell hardness HRC value of the titanium alloy after ordinary annealing can only be controlled between 37 and 40, so that cold rolling deformation cannot be carried out.
Based on the requirements, a pretreatment process before cold rolling of the novel high-strength, high-toughness and marine environment corrosion-resistant TC27 titanium alloy which is independently developed in China needs to be designed.
Disclosure of Invention
The purpose of the invention is: a cold rolling method for a TC27 titanium alloy pipe is designed to adapt to a cold rolling treatment process of a TC27 titanium alloy.
In order to solve the technical problem, the technical scheme of the invention is as follows:
a TC27 titanium alloy pipe cold rolling method is used for preprocessing a pipe blank before cold rolling, and the preprocessing technology is as follows:
heating the electric furnace to (T)β+20)℃～(Tβ+40) DEG C, and then the tube blank is put into the tube blank at the temperature, the heat preservation time is calculated according to 0.8 min/mm-1.0 min/mm by taking the wall thickness of the tube blank as the base number, and the cooling speed is ensured to be more than or equal to 30 ℃/s.
The cold rolling method of the TC27 titanium alloy pipe comprises the following steps:
step one, smelting a TC27 titanium alloy ingot;
step two, heating the electric furnace to 1100-1200 ℃, loading the ingot obtained in the step one after the temperature is reached, preserving the heat for 18-24 h, carrying out component homogenizing annealing, and then air-cooling to room temperature;
thirdly, according to the method of 'high-low-high' on the phase transformation point and below the phase transformation point, ingot casting cogging and forging change are carried out by adopting a process of combining repeated upsetting and drawing out, the deformation of each firing time on the phase transformation point is controlled to be 45-55 percent, the deformation of each firing time below the phase transformation point is controlled to be 35-45 percent, the single reduction amount is controlled to be 120-160 mm/time during drawing out, and the TC27 titanium alloy bar subjected to forging change in the two-phase region is cut into a fixed-length bar;
step four, heating the electric furnace to (T)β+30)℃～(Tβ+60) deg.c, and filling in the third step after reaching the temperatureThe heat preservation time of the obtained fixed length bar is calculated according to the diameter of the fixed length bar as a base number and 0.8 min/mm-1.0 min/mm, and then the hot rolling and the perforation are carried out, and the air cooling is carried out to the room temperature, so as to obtain a tube blank;
step five, heating the electric furnace to (T)β+20)℃～(Tβ+40) DEG C, and after the temperature is reached, loading the tube blank obtained in the fourth step, wherein the heat preservation time is calculated according to 0.8 min/mm-1.0 min/mm by taking the wall thickness of the tube blank as a base number, the cooling speed is more than or equal to 30 ℃/s, the structure in the tube blank is ensured to be a single supercooled beta phase, and the Rockwell hardness HRC value of the tube blank is controlled to be between 30 and 35;
the tube blank obtained in the sixth step and the fifth step is subjected to cold rolling deformation for 2-3 passes by adopting a cold rolling process for reducing the diameter and the wall at the same time to obtain a tube blank;
and step seven, heating the vacuum electric furnace to 580-630 ℃, loading the tube blank obtained in the step six after the temperature is reached, preserving the heat for 6-10 h, and then cooling the tube blank to room temperature in air.
And in the sixth step, during cold rolling deformation, the cold rolling reduction rate of each pass is controlled to be between 5% and 15%, the wall reduction amount is controlled to be between 10% and 25%, and the elongation coefficient is controlled to be between 1.5 and 2.5.
Preferably, ingot casting cogging and forge changing are carried out 6-10 times in the third step.
Preferably, the pipe blank in the fifth step is cooled in a water cooling or oil cooling mode after heat preservation.
Preferably, cutting the head and the tail of the pretreated pipe blank, and removing oxide skin defects on the inner surface and the outer surface;
preferably, in the sixth step, after the 1 st pass of cold rolling, the fifth step is repeated once, and then the 2 nd pass of cold rolling deformation is performed.
In the first step, a 3-ton TC27 titanium alloy ingot is smelted by a three-time vacuum consumable method, the TC27 titanium alloy ingot is a 3-ton ingot with the diameter phi of more than or equal to 600mm, and the ingot is cut into two parts according to the length after being scalped and head and tail cut.
Preferably, the cast ingot in the second step needs to be coated with a special high-temperature anti-oxidation coating for the TC27 titanium alloy or a copper sheath when being subjected to homogenizing annealing.
The TC27 titanium alloy comprises the following alloy components in percentage by weight: 5.0 to 6.5 percent of Al, 3.5 to 5.0 percent of Mo, 5.0 to 6.5 percent of V, 1.5 to 2.5 percent of Nb, 0.5 to 1.5 percent of Fe, and the balance of Ti and inevitable impurities, wherein the nominal chemical composition of the ingot is Ti-5.5Al-4Mo-6V-2Nb-1 Fe.
Preferably, ingot cogging is directly performed after ingot homogenization in the second step.
And fifthly, removing the defects of oxide skins on the inner surface and the outer surface by adopting an internal twisting and polishing mode after the pipe blank is pretreated.
The invention has the beneficial effects that:
aiming at novel high-strength, high-toughness and marine environment corrosion-resistant TC27 titanium alloy independently developed in China, pretreatment before cold rolling of a titanium alloy pipe is carried out, the method provided by the invention is simple in process parameter setting, convenient to operate and controllable in process flow, cold rolling deformation can be improved after the pipe is pretreated before cold rolling, cold rolling passes are reduced, after cold rolling, aging treatment can be carried out to ensure that the tensile strength of the pipe at room temperature is more than or equal to 1150MPa, the yield strength is more than or equal to 1050MPa, the elongation delta is more than or equal to 10%, the reduction of area psi is more than or equal to 20%, the impact power aku is more than or equal to 30J, and when Kt is 1, R is 0.06, N is 107Fatigue limit of time σDMore than or equal to 890MPa, and the fracture toughness of 3.5 percent NaCl aqueous solution under room temperature environment
Figure BDA0002600528290000051
Figure BDA0002600528290000052
The strength, toughness, service life and marine environment corrosion resistance of the TC27 titanium alloy are obviously improved.
The TC27 titanium alloy in the invention has high strength and large deformation resistance, and can not be subjected to cold rolling deformation after ordinary annealing. Therefore, the invention aims at the characteristics of the TC27 titanium alloy, carries out pretreatment before cold rolling, and controls the heat preservation temperature of the pretreatment before cold rolling to be (T)β+20)～(TβAnd +40), simultaneously cooling at a speed of more than or equal to 30 ℃/s to ensure that the structure in the tube blank is a single supercooled beta phase, controlling the Rockwell hardness HRC value of the tube blank to be between 30 and 35, and finally obtaining the high-strength and high-toughness titanium alloy tube through 2-3 passes of reducing and wall-reducing cold rolling processes.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention more apparent, the technical solutions of the present invention will be clearly and completely described below with reference to the embodiments of the present invention. It is to be understood that the embodiments described are only a few embodiments of the present invention, and not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Features of various aspects of embodiments of the invention will be described in detail below. In the following detailed description, numerous specific details are set forth in order to provide a thorough understanding of the present invention. It will be apparent, however, to one skilled in the art that the present invention may be practiced without these specific details. The following description of the embodiments is merely intended to better understand the present invention by illustrating examples thereof. The present invention is not limited to any particular arrangement or method provided below, but rather covers all product structures, any modifications, alterations, etc. of the method covered without departing from the spirit of the invention.
In the following description, well-known structures and techniques are not shown to avoid unnecessarily obscuring the present invention. The steps of the invention are specifically described by adopting a three-time vacuum consumable method to smelt a 3-ton TC27 titanium alloy ingot with the diameter phi of more than or equal to 600mm, and taking the finally obtained drill rod with the diameter of 127mm, the wall thickness of 9.6mm and the length of more than or equal to 10m as an example.
Example 1:
step one, smelting a 3-ton TC27 titanium alloy cast ingot by adopting a three-time vacuum consumable method, wherein the weight percentage of each alloy comprises 5.5% of Al, 3.5% of Mo, 5.5% of V, 2.0% of Nb, 0.5% of Fe and the balance of Ti and inevitable impurities, the 3-ton TC27 titanium alloy cast ingot is 610mm in diameter phi, the cast ingot is sawed into two parts according to the length after being scalped and head and tail cut, and each section is 580mm multiplied by 1100mm in size after being sawed, and the step two is carried out;
and step two, heating the electric furnace to 1100 ℃, loading the ingot obtained in the step two after the temperature is reached, preheating the ingot to 200 ℃ before loading, and uniformly spraying TC27 titanium alloy special high-temperature anti-oxidation coating on the surface of the ingot so as to reduce the thickness of an oxidation layer formed in the high-temperature heat preservation process. And 2 cast ingots are filled into each furnace, the temperature is preserved for 24 hours after the temperature of the furnace is increased again, the components are subjected to homogenization annealing, and then the furnace is cooled to room temperature in air.
And step three, according to the method of 'high-low-high' at the phase transformation point and below the phase transformation point, ingot casting cogging and forging change are carried out for 10 times by adopting a process of combining repeated upsetting and drawing out, the deformation of each time of heating at the phase transformation point is controlled to be 50%, the deformation of each time of heating at the phase transformation point is controlled to be 40%, the single reduction amount is controlled to be 160 mm/time during drawing out, and the TC27 titanium alloy bar subjected to forging change in the two-phase region is cut to length according to phi 150mm multiplied by 2500 mm. The phase change point T of the TC27 titanium alloy batch is measured by adopting a metallographic methodβ870 ℃;
step four, heating the electric furnace to 900 ℃, loading the electric furnace into the fixed-length bar obtained in the step three after the temperature is reached, keeping the temperature for 1.0min/mm, hot-rolling and perforating by adopting phi 150mm perforator equipment and a tool and a die thereof until the diameter is 160mm and the wall thickness is 18mm, and air-cooling to room temperature to obtain a tube blank;
step five, heating the electric furnace to 900 ℃, loading the heated pipe blank into the pipe blank obtained in the step four, wherein the heat preservation time is calculated according to 1.0min/mm, cooling the pipe blank in a water cooling mode after heat preservation, ensuring that the cooling speed is more than or equal to 30 ℃/s, ensuring that the structure in the pipe blank is a single supercooled beta phase, controlling the Rockwell hardness HRC value of the pipe blank to be 30-35, cutting the head and the tail of the pretreated pipe blank, and removing the defects of oxide skins and the like on the inner surface and the outer surface in an internal twisting and polishing mode;
and sixthly, the tube blank obtained in the fifth step is subjected to a cold rolling process of reducing the diameter and reducing the wall at the same time, a cold rolling tube mill with the diameter of 120mm and a tool die are subjected to cold rolling deformation of 3 times, the fifth step is repeated after the cold rolling of the 1 st time, and then the cold rolling deformation of the 2 nd time is carried out. The reduction rate of each cold rolling is controlled to be about 10 percent, the wall reduction amount is controlled to be about 15 percent, and the elongation coefficient is controlled to be about 2.0. Finally obtaining a tube blank with the diameter of 127mm, the wall thickness of 9.6mm and the length of more than or equal to 10 m;
and step seven, heating the vacuum electric furnace to 600 ℃, filling the pipe blank obtained in the step six after reaching the temperature, preserving the heat for 8 hours, and then cooling the pipe blank to the room temperature in air.
The properties of the cold rolled drill rods after ageing (600 ℃/8h/AC) are shown in Table 2.
TABLE 2 room temperature tensile properties (600 ℃/8h/AC) after aging of the drill rods of example 1
Figure BDA0002600528290000071
Example 2:
step one, smelting a 3-ton TC27 titanium alloy cast ingot by adopting a three-time vacuum consumable method, wherein the weight percentage of each alloy comprises 5.0% of Al, 4.5% of Mo, 6.5% of V, 1.5% of Nb, 1.0% of Fe and the balance of Ti and inevitable impurities, the 3-ton TC27 titanium alloy cast ingot is 610mm in diameter phi, the cast ingot is sawed into two parts according to the length after being scalped and head and tail cut, and each section is 570mm multiplied by 1150mm in size after being sawed, and the step two is carried out;
and step two, heating the electric furnace to 1200 ℃, and filling the ingot obtained in the step two after the temperature is reached, wherein the ingot is protected by adopting a copper-clad sleeve so as to reduce the thickness of an oxide layer formed in the high-temperature heat preservation process. And 2 ingots are filled into each furnace, the furnace is insulated for 20 hours after reaching the temperature again for component homogenizing annealing, and then the furnace is directly transferred to the step three for ingot casting and cogging on the phase change point.
And step three, according to the method of 'high-low-high' at the phase transformation point and below the phase transformation point, ingot casting cogging and forging change are carried out for 8 times by adopting a process of combining repeated upsetting and drawing out, the deformation of each time of heating at the phase transformation point is controlled to be 55%, the deformation of each time of heating at the phase transformation point is controlled to be 45%, the single reduction amount is controlled to be 140 mm/time during drawing out, and the TC27 titanium alloy bar subjected to forging change in the two-phase region is cut to length according to phi 150mm multiplied by 2500 mm. The phase change point T of the TC27 titanium alloy batch is measured by adopting a metallographic methodβAt 880 ℃;
step four, heating the electric furnace to 920 ℃, putting the electric furnace into the fixed-length bar obtained in the step three after the temperature is reached, keeping the temperature for 0.9min/mm, hot-rolling and perforating by adopting phi 150mm perforator equipment and a tool and a die thereof until the diameter is 160mm and the wall thickness is 18mm, and air-cooling to room temperature to obtain a tube blank;
step five, heating the electric furnace to 920 ℃, putting the heated pipe blank into the pipe blank obtained in the step four, wherein the heat preservation time is calculated according to 0.9min/mm, cooling the pipe blank in a water cooling mode after heat preservation, ensuring that the cooling speed is more than or equal to 30 ℃/s, ensuring that the structure in the pipe blank is a single supercooled beta phase, controlling the Rockwell hardness HRC value of the pipe blank to be 30-35, cutting the head and the tail of the pretreated pipe blank, and removing the defects of oxide skins and the like on the inner surface and the outer surface in an internal twisting and polishing mode;
and sixthly, the tube blank obtained in the fifth step is subjected to a cold rolling process of reducing the diameter and reducing the wall at the same time, a cold rolling tube mill with the diameter of 120mm and a tool die are subjected to cold rolling deformation of 3 times, the fifth step is repeated after the cold rolling of the 1 st time, and then the cold rolling deformation of the 2 nd time is carried out. The reducing rate of each cold rolling is controlled to be about 12 percent, the wall reducing amount is controlled to be about 20 percent, and the elongation coefficient is controlled to be about 2.2. Finally obtaining a tube blank with the diameter of 127mm, the wall thickness of 9.6mm and the length of more than or equal to 10 m;
and step seven, heating the vacuum electric furnace to 580 ℃, filling the tube blank obtained in the step six after the temperature is reached, preserving the heat for 10 hours, and then cooling the tube blank to the room temperature in air.
The properties of the cold rolled drill rods after ageing (580 ℃/10h/AC) are shown in Table 3.
TABLE 3 room temperature tensile properties (580 deg.C/10 h/AC) after aging of the drill rods of example 2
Figure BDA0002600528290000081
Example 3:
step one, smelting a 3-ton TC27 titanium alloy cast ingot by adopting a three-time vacuum consumable method, wherein the weight percentage of each alloy comprises 6.0 percent of Al, 5.0 percent of Mo, 5.0 percent of V, 2.5 percent of Nb, 1.5 percent of Fe, and the balance of Ti and inevitable impurities, the specification of the 3-ton TC27 titanium alloy cast ingot is that the diameter phi is 610mm, the cast ingot is sawed into two parts according to the length after being scalped and head and tail cut, and the size of each part is phi 585mm multiplied by 1160mm after being sawed, and then transferring to step two;
and step two, heating the electric furnace to 1150 ℃, loading the ingot obtained in the step two after the temperature is reached, preheating the ingot to 200 ℃ before loading, and uniformly spraying TC27 titanium alloy special high-temperature anti-oxidation coating on the surface of the ingot so as to reduce the thickness of an oxidation layer formed in the high-temperature heat preservation process. 4 ingots are loaded in each furnace, the furnace is insulated for 20 hours after reaching the temperature again for component homogenizing annealing, and then the furnace is directly transferred to the step three for ingot casting and cogging on the phase change point.
And step three, according to the method of 'high-low-high' at the phase transformation point and below the phase transformation point, adopting a process of combining repeated upsetting and drawing out to perform ingot cogging and forging alteration for 9 times, controlling the deformation of each time of heating at the phase transformation point to be 45%, controlling the deformation of each time of heating below the phase transformation point to be 35%, controlling the single reduction amount to be 120 mm/time during drawing out, and cutting the TC27 titanium alloy bar subjected to forging alteration in the two-phase region to a fixed length according to phi 150mm multiplied by 2500 mm. The phase change point T of the TC27 titanium alloy batch is measured by adopting a metallographic methodβ865 ℃ is adopted;
step four, heating the electric furnace to 915 ℃, putting the heated electric furnace into the fixed-length bar obtained in the step three after the temperature is reached, keeping the temperature for 0.8min/mm, hot-rolling and perforating by adopting phi 150mm perforator equipment and a tool and die thereof until the diameter is 160mm and the wall thickness is 18mm, and air-cooling to room temperature to obtain a tube blank;
fifthly, heating the electric furnace to 890 ℃, loading the pipe blank obtained in the fourth step after the temperature is reached, calculating the heat preservation time according to 0.9min/mm, cooling the pipe blank in an oil cooling mode after heat preservation, ensuring that the cooling speed is more than or equal to 30 ℃/s, ensuring that the structure in the pipe blank is a single supercooled beta phase, controlling the Rockwell hardness HRC value of the pipe blank to be between 30 and 35, cutting the head and the tail of the pretreated pipe blank, and removing the defects of oxide skins and the like on the inner surface and the outer surface in an internal twisting and polishing mode;
and sixthly, the tube blank obtained in the fifth step is subjected to a cold rolling process of reducing the diameter and reducing the wall at the same time, a cold rolling tube mill with the diameter of 120mm and a tool die are subjected to cold rolling deformation of 2 passes, the fifth step is repeated after the cold rolling of the 1 st pass, and then the cold rolling deformation of the 2 nd pass is carried out. The reducing rate of each cold rolling is controlled to be about 15 percent, the wall reducing amount is controlled to be about 25 percent, and the elongation coefficient is controlled to be about 2.5. Finally obtaining a tube blank with the diameter of 127mm, the wall thickness of 9.6mm and the length of more than or equal to 10 m;
and step seven, heating the vacuum electric furnace to 630 ℃, filling the tube blank obtained in the step six after the temperature is reached, preserving the heat for 9 hours, and then cooling the tube blank to the room temperature in air.
The properties of the cold rolled drill rods after ageing (630 ℃/9h/AC) are shown in Table 4.
TABLE 4 room temperature tensile properties (630 ℃/9h/AC) after aging of the drill rods of example 3
Figure BDA0002600528290000101
Example 4:
step one, smelting a 3-ton TC27 titanium alloy cast ingot by adopting a three-time vacuum consumable method, wherein the weight percentage of each alloy comprises 6.5% of Al, 4.0% of Mo, 6.0% of V, 2.0% of Nb, 1.0% of Fe and the balance of Ti and inevitable impurities, the 3-ton TC27 titanium alloy cast ingot is 610mm in diameter phi, the cast ingot is sawed into two parts according to the length after being scalped and head and tail cut, and each section is 580mm multiplied by 1110mm after being sawed, and the step two is carried out;
and step two, heating the electric furnace to 1180 ℃, loading the ingot obtained in the step two after the temperature is reached, preheating the ingot to 200 ℃ before loading, and uniformly spraying TC27 titanium alloy special high-temperature anti-oxidation coating on the surface of the ingot so as to reduce the thickness of an oxidation layer formed in the high-temperature heat preservation process. 3 ingots are loaded into each furnace, the furnace is insulated for 18 hours after reaching the temperature again for component homogenizing annealing, and then the furnace is directly transferred to the step three for ingot casting and cogging on the phase change point.
And step three, according to the method of 'high-low-high' at the phase transformation point and below the phase transformation point, ingot casting cogging and forging change are carried out for 10 times by adopting a process of combining repeated upsetting and drawing out, the deformation of each time of heating at the phase transformation point is controlled to be 50%, the deformation of each time of heating at the phase transformation point is controlled to be 45%, the single reduction amount is controlled to be 140 mm/time during drawing out, and the TC27 titanium alloy bar subjected to forging change in the two-phase region is cut to length according to phi 150mm multiplied by 2500 mm. The phase change point T of the TC27 titanium alloy batch is measured by adopting a metallographic methodβ875 ℃;
step four, heating the electric furnace to 935 ℃, loading the electric furnace into the fixed-length bar obtained in the step three after reaching the temperature, carrying out hot rolling and punching by adopting phi 150mm puncher equipment and a tool and die thereof until the diameter is 160mm and the wall thickness is 18mm, and carrying out air cooling to room temperature to obtain a tube blank, wherein the heat preservation time is calculated according to 0.8 min/mm;
fifthly, heating the electric furnace to 895 ℃, loading the pipe blank obtained in the fourth step after the temperature is reached, calculating the heat preservation time according to 1.0min/mm, cooling the pipe blank in an oil cooling mode after heat preservation, ensuring that the cooling speed is more than or equal to 30 ℃/s, ensuring that the structure in the pipe blank is a single supercooled beta phase, controlling the Rockwell hardness HRC value of the pipe blank to be between 30 and 35, cutting the head and the tail of the pretreated pipe blank, and removing the defects of oxide skins and the like on the inner surface and the outer surface in an internal twisting and polishing mode;
and sixthly, the tube blank obtained in the fifth step is subjected to a cold rolling process of reducing the diameter and reducing the wall at the same time, a cold rolling tube mill with the diameter of 120mm and a tool die are subjected to cold rolling deformation of 3 times, the fifth step is repeated after the cold rolling of the 1 st time, and then the cold rolling deformation of the 2 nd time is carried out. The reducing rate of each cold rolling is controlled to be about 5 percent, the wall reducing amount is controlled to be about 10 percent, and the elongation coefficient is controlled to be about 1.5. Finally obtaining a tube blank with the diameter of 127mm, the wall thickness of 9.6mm and the length of more than or equal to 10 m;
and step seven, heating the vacuum electric furnace to 610 ℃, filling the pipe blank obtained in the step six after reaching the temperature, preserving the heat for 6 hours, and then cooling the pipe blank to the room temperature in air.
The properties of the cold rolled drill rods after ageing (610 ℃/6h/AC) are shown in Table 5.
TABLE 5 room temperature tensile properties (610 deg.C/6 h/AC) after aging of the drill rods of example 4
Figure BDA0002600528290000111
The preparation of multiple batches of TC27 titanium alloy drill rods is completed by adopting the method, and the prepared drill rods have the advantages of good surface quality, high dimensional accuracy, high batch stability and good repeatability. In addition, the invention has simple process parameter setting and convenient operation, the cold rolling deformation of the drill rod can be improved after the pretreatment before the cold rolling, the cold rolling passes are reduced, the room temperature tensile strength of the drill rod can be more than or equal to 1150MPa, the yield strength can be more than or equal to 1050MPa, the elongation delta can be more than or equal to 10 percent, the reduction of area psi can be more than or equal to 20 percent, the impact energy aku can be more than or equal to 30J by the aging treatment after the cold rolling, and when Kt is 1, R is 0.06, N is 107Fatigue limit of time σDMore than or equal to 890MPa, and the fracture toughness of 3.5 percent NaCl aqueous solution under room temperature environment
Figure BDA0002600528290000112
Figure BDA0002600528290000121
The strength, toughness, service life and marine environment corrosion resistance of the TC27 titanium alloy are obviously improved.
Finally, it should be noted that: the above embodiments are only for illustrating the technical solutions of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art can easily conceive various equivalent modifications or substitutions within the technical scope of the present invention, and these modifications or substitutions should be covered within the scope of the present invention.

Claims (9)

1. A cold rolling method of TC27 titanium alloy pipes is characterized in that: the cold rolling method is used for preprocessing a pipe blank before cold rolling, and the preprocessing process comprises the following steps:
heating the electric furnace to (T)β+20)℃～(Tβ+40) DEG C, and then loading the tube blank into the tube blank at the temperature, wherein the heat preservation time is calculated according to 0.8 min/mm-1.0 min/mm by taking the wall thickness of the tube blank as a base number, and the cooling speed is ensured to be more than or equal to 30 ℃/s;
the cold rolling method comprises the following steps:
step one, smelting a TC27 titanium alloy ingot;
step two, heating the electric furnace to 1100-1200 ℃, loading the ingot obtained in the step one after the temperature is reached, preserving the heat for 18-24 h, carrying out component homogenizing annealing, and then air-cooling to room temperature;
thirdly, according to the method of 'high-low-high' on the phase transformation point and below the phase transformation point, ingot casting cogging and forging change are carried out by adopting a process of combining repeated upsetting and drawing out, the deformation of each firing time on the phase transformation point is controlled to be 45-55 percent, the deformation of each firing time below the phase transformation point is controlled to be 35-45 percent, the single reduction amount is controlled to be 120-160 mm/time during drawing out, and the TC27 titanium alloy bar subjected to forging change in the two-phase region is cut into a fixed-length bar;
step (ii) ofFourthly, heating the electric furnace to (T)β+30)℃～(Tβ+60) DEG C, loading the rod material obtained in the third step into the fixed-length rod material at the temperature, calculating the heat preservation time according to 0.8 min/mm-1.0 min/mm by taking the diameter of the fixed-length rod material as a base number, then hot rolling and perforating, and air cooling to the room temperature to obtain a tube blank;
step five, heating the electric furnace to (T)β+20)℃～(Tβ+40) DEG C, and after the temperature is reached, loading the tube blank obtained in the fourth step, wherein the heat preservation time is calculated according to 0.8 min/mm-1.0 min/mm by taking the wall thickness of the tube blank as a base number, the cooling speed is more than or equal to 30 ℃/s, the structure in the tube blank is ensured to be a single supercooled beta phase, and the Rockwell hardness HRC value of the tube blank is controlled to be between 30 and 35;
the tube blank obtained in the sixth step and the fifth step is subjected to cold rolling deformation for 2-3 passes by adopting a cold rolling process for reducing the diameter and the wall at the same time to obtain a tube blank;
and step seven, heating the vacuum electric furnace to 580-630 ℃, loading the tube blank obtained in the step six after the temperature is reached, preserving the heat for 6-10 h, and then cooling the tube blank to room temperature in air.
2. The TC27 titanium alloy tube cold rolling method according to claim 1, wherein: and in the sixth step, during cold rolling deformation, the cold rolling reduction rate of each pass is controlled to be between 5% and 15%, the wall reduction amount is controlled to be between 10% and 25%, and the elongation coefficient is controlled to be between 1.5 and 2.5.
3. The TC27 titanium alloy tube cold rolling method according to claim 1, wherein: and in the third step, 6-10 times of heating ingot casting cogging and forging change are carried out.
4. The TC27 titanium alloy tube cold rolling method according to claim 1, wherein: and step five, cooling the pipe blank by adopting a water cooling or oil cooling mode after heat preservation.
5. The TC27 titanium alloy tube cold rolling method according to claim 1, wherein: and fifthly, cutting the head and the tail of the pretreated pipe blank, and removing the oxide skin defects on the inner surface and the outer surface.
6. The TC27 titanium alloy tube cold rolling method according to claim 1, wherein: in the sixth step, after the 1 st pass of cold rolling, the fifth step is repeated once, and then the 2 nd pass of cold rolling deformation is carried out.
7. The TC27 titanium alloy tube cold rolling method according to claim 1, wherein: the first step is specifically as follows: 3-ton TC27 titanium alloy ingots are smelted by a three-time vacuum consumable method, the TC27 titanium alloy ingots are 3-ton ingots with the diameter phi of more than or equal to 600mm, and the ingots are peeled off, cut head and tail, and then cut into two parts according to the length.
8. The TC27 titanium alloy tube cold rolling method according to claim 1, wherein: and in the second step, the cast ingot needs to be coated with a special high-temperature anti-oxidation coating for TC27 titanium alloy or a copper sheath when being subjected to homogenizing annealing.
9. The TC27 titanium alloy tube cold rolling method according to claim 1, wherein: the TC27 titanium alloy comprises the following alloy components in percentage by weight: 5.0 to 6.5 percent of Al, 3.5 to 5.0 percent of Mo, 5.0 to 6.5 percent of V, 1.5 to 2.5 percent of Nb, 0.5 to 1.5 percent of Fe, and the balance of Ti and inevitable impurities, wherein the nominal chemical composition of the ingot is Ti-5.5Al-4Mo-6V-2Nb-1 Fe.
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