CN110592425A - High-impact-toughness titanium alloy and method for preparing seamless pipe by using titanium alloy - Google Patents
High-impact-toughness titanium alloy and method for preparing seamless pipe by using titanium alloy Download PDFInfo
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- 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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D3/00—Straightening or restoring form of metal rods, metal tubes, metal profiles, or specific articles made therefrom, whether or not in combination with sheet metal parts
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
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- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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Abstract
The invention discloses a high impact toughness titanium alloy, which comprises 4.0-9.0% of Al, 0.5-5.0% of Mo, 1-5% of Zr, 1-5% of Nb, 0.2-2.0% of Fe and the balance of Ti and impurities.
Description
Technical Field
The invention relates to the field of manufacturing of aluminum alloy materials and seamless pipes, in particular to a high-impact-toughness titanium alloy and a method for preparing a seamless pipe by using the titanium alloy.
Background
The titanium and the titanium alloy have small density, high specific strength, excellent corrosion resistance, good medium-high temperature mechanical property, excellent anti-fatigue and creep property and huge application potential in the petrochemical industry. The titanium alloy pipe has good corrosion resistance, particularly seawater corrosion resistance and biological corrosion resistance, and is widely applied to the petrochemical industry. SY/T6896.3-2016 technical Specification No. 3 for Special pipes in the oil and gas industry: the requirements of titanium alloy oil pipe on the manufacturing process of the titanium alloy oil pipe are as follows: the titanium alloy oil pipe is manufactured by adopting a seamless titanium alloy pipe. The low-cost preparation technology of the titanium alloy seamless pipe for the petrochemical industry is always a research hotspot of all countries in the world.
The oil well pipe is subjected to various actions such as underground stress, pulling, twisting and the like, the internal pressure of dozens of megapascals is born, and the stress condition is complex. Generally, the impact energy of a P110 steel oil pipe reaches about 200J, while the impact energy of a P110 steel grade titanium alloy is usually 30-50J, under the condition, an oil field user thinks that the titanium alloy has better corrosion resistance, but the impact toughness is further improved so as to improve the safety and reliability of a pipe column. The domestic research unit improves the commonly used titanium alloy such as TC4, but the impact toughness is not improved. At present, the development mode of the titanium alloy oil pipe in China basically adopts the existing titanium alloy to carry out performance assessment as the main mode, and rarely carries out new material development. Therefore, the titanium alloy oil pipe is slowly applied in China, and the titanium alloy seamless pipe with certain length and wall thickness and excellent mechanical property has certain difficulty in processing because of large room temperature deformation resistance of the titanium alloy.
Therefore, it is necessary to find a titanium alloy with high impact toughness and a method for preparing seamless pipes by using the titanium alloy so as to meet the use requirements of the petrochemical industry.
Disclosure of Invention
In order to overcome the defects in the prior art, the invention provides a high-impact-toughness titanium alloy and a method for preparing a seamless pipe by using the titanium alloy.
In order to achieve the purpose, the invention adopts the specific scheme that:
a high impact toughness titanium alloy, its chemical composition requires to be Al4.0-9.0%, Mo0.5-5.0%, Zr 1-5%, Nb 1-5%, Fe 0.2-2.0%, the rest is Ti and inevitable impurity; wherein the content of impurities satisfies N is less than or equal to 0.05%, C is less than or equal to 0.1%, H is less than or equal to 0.015%, and O is less than or equal to 0.15%.
A method for preparing a seamless pipe by using a high-impact-toughness titanium alloy mainly comprises the following steps:
step one, ingot preparation: weighing an aluminum-niobium intermediate alloy, a molybdenum block, pure sponge zirconium, iron nails and sponge titanium according to the requirements of chemical components, mixing, pressing into an electrode rod, and then putting into a vacuum consumable arc furnace for secondary smelting to obtain a titanium alloy ingot;
step two, preparing a bar blank: cogging and forging the titanium alloy ingot obtained in the step one at 1150 ℃, and forging again at 970-1020 ℃ to obtain a bar blank;
step three, cross piercing: heating the bar blank obtained in the step two in a heating furnace to 950-1200 ℃, and then preserving heat, wherein the heat preservation time is the diameter x (0.5-1.1) min/mm of the bar blank; adopting a molybdenum-based alloy or high alloy top, coating a lubricant on the head, placing the lubricant in the central hole of the heated bar blank, and perforating to obtain a tube blank;
step four, hot rolling and fixed reducing: hot rolling the tube blank obtained in the step three, spraying borax into the tube blank before hot rolling, controlling the deformation to be 50-70%, and then performing fixed diameter reduction to obtain a tube;
step five, heat treatment: placing the pipe obtained in the fourth step into a heat treatment furnace for heat treatment, wherein the heat treatment temperature is 800-980 ℃;
step six, post-treatment: and (4) straightening, sawing, inspecting and warehousing the heat-treated pipe.
Preferably, the requirement of the tube blank produced in the third step is that the outer diameter/wall thickness is 9-12.
Preferably, in the third step, a micro-oxidation atmosphere is kept in the heating furnace in the bar blank heating process, the micro-oxidation atmosphere is a mixed atmosphere of air and natural gas, and the micro-oxidation atmosphere is realized by adjusting the ratio of the air to the natural gas (the ratio of the air to the natural gas can be adjusted according to needs). Maintaining the micro-oxidizing atmosphere in the furnace is beneficial to reducing the possibility of hydrogen absorption of the titanium alloy.
Preferably, in the fourth step, the outer diameter reduction ratio in the diameter reduction process is set to 20 to 30%, and the thickness increase amount is equal to (10% to 15%) wall thickness x after hot rolling.
Preferably, in the sixth step, the pipe is heated to 600-700 ℃ for straightening treatment, and the bending degree of the straightened pipe is less than 1.5 per mill of the total length of the pipe. The pipe prepared by the method is high in strength, and can be straightened only by heating the pipe to 600-700 ℃.
In the third step, the lubricant used for the cross piercing is glass powder lubricant.
Wherein, the hot rolling in the fourth step is carried out by utilizing the residual heat after the cross rolling perforation, and the resources can be saved on the basis of realizing the hot rolling. Spraying borax in the pipe blank before hot rolling, and lubricating the inner wall of the pipe by using the borax to obtain the high-strength seamless pipe.
In the aspect of process adaptability, the surface of the titanium alloy is easy to crack in the heating process and needs to be repeatedly polished, so that the production efficiency is low. The alloy greatly reduces the surface cracking of the alloy and improves the material utilization rate by adding the Fe element. This is because Fe is either substitutionally or interstitially soluble in α -Ti. When Fe is dissolved in the metal interstitials as metal impurity atoms having a relatively small atomic radius, such rapidly diffusing impurities strongly accelerate the diffusion of the matrix material, especially when the temperature is in a certain range below the β -transus temperature. In this temperature range, there are Fe impurity atoms from the high-speed moving impurity-vacancy pairs that are interstitially dissolved in the matrix, which results in a reduction in the matrix diffusion activation energy, promotes diffusion of the matrix material, and increases the effective diffusion capacity of the alloy. When the temperature is close to the phase transition point, dislocation climbing is realized by means of diffusion of vacancies or interstitial atoms, the addition of Fe can generate an impurity-vacancy pair, and meanwhile, the diffusion of the interstitial atoms is enhanced, so that the climbing movement of edge dislocation can be promoted, and the deformation resistance of the titanium alloy is greatly reduced.
Has the advantages that:
1. the invention provides a method for improving the tensile strength and the lasting strength of the alloy by taking Ti as a matrix and Al, Mo, Zr, Nb and Fe as main alloy elements, wherein the Al element is a main strengthening element, so that the tensile strength and the lasting strength of the alloy can be greatly improved; the Mo element is a beta stable element, so that the excellent process plasticity of the alloy is ensured while the room temperature and high temperature performance of the alloy is improved, and the simultaneous addition of two elements is more favorable for improving the comprehensive performance than the addition of only one element; zr is a neutral element, can improve the heat strength of the alloy without influencing the heat stability of the alloy, and refines grains. The Nb element does not greatly contribute to the strength of the titanium alloy, but can greatly improve the thermal stability and the corrosion resistance of the titanium alloy. Fe is a beta stable element, the room temperature strength of the titanium alloy can be greatly improved, the high temperature strength is reduced, the impact toughness and the elongation are not influenced, and the material is ensured to have good processability.
2. The preparation method can realize the mass production of the titanium alloy seamless pipe, and has high efficiency and low cost. And a stable oxide layer is arranged on the surface of the seamless pipe subjected to heat treatment, so that the hardness of the surface of the pipe can be improved while the material is protected, and the wear resistance of the pipe is enhanced. In addition, the oxide layer is an insulating layer, so that the galvanic corrosion problem when the oxide layer is in contact with dissimilar metals can be well solved.
3. The titanium alloy pipe prepared by the invention has high strength, high plasticity, high low-temperature impact toughness and good corrosion resistance, and meets the application requirements of severe working conditions of oil wells and gas wells.
Detailed Description
The high impact toughness titanium alloy prepared by the invention comprises the following chemical components: 4.0 to 9.0 percent of Al, 0.5 to 5.0 percent of Mo, 1 to 5 percent of Zr, 1 to 5 percent of Nb, 0.2 to 2.0 percent of Fe and the balance of Ti. Wherein the content of impurities satisfies N is less than or equal to 0.05%, C is less than or equal to 0.1%, H is less than or equal to 0.015%, and O is less than or equal to 0.15%.
A method for preparing a seamless pipe by using a high-impact-toughness titanium alloy mainly comprises the following steps:
step one, ingot preparation: mixing the aluminum-niobium intermediate alloy, the molybdenum block, the pure sponge zirconium, the iron nail and the sponge titanium according to the chemical component requirements, pressing into an electrode bar, and then putting into a vacuum consumable arc furnace for secondary smelting to obtain a titanium alloy ingot;
step two, preparing a bar blank: cogging and forging a titanium alloy ingot at 1150 ℃, and performing forging change at 970-1020 ℃ to obtain a bar blank;
step three, cross piercing: heating the bar blank in a heating furnace to 950-1200 ℃, and preserving heat after the bar blank is heated to the temperature, wherein the heat preservation time is the diameter x (0.5-1.1) min/mm of the bar blank; adopting a molybdenum-based alloy or high alloy top, coating a lubricant on the head, placing the lubricant in a central hole of a bar blank, and perforating to obtain a tube blank, wherein the outer diameter/wall thickness of the tube blank is 9-12;
step four, hot rolling and fixed reducing: carrying out hot rolling on the tube blank by utilizing the waste heat after the oblique rolling perforation, spraying borax serving as a lubricant into the tube blank before the hot rolling, controlling the deformation to be 50-70%, and then carrying out fixed reducing to obtain a tube, wherein the external diameter reduction proportion in the fixed reducing process is 20-30%, and the wall thickness thickening amount is equal to the wall thickness x (10-15%) after the hot rolling;
step five, heat treatment: placing the pipe in a heat treatment furnace for heat treatment, wherein the heat treatment temperature is 800-980 ℃;
step six, post-treatment: and heating the pipe subjected to heat treatment to 600-700 ℃ for straightening treatment, wherein the bending degree of the straightened pipe is less than 1.5 thousandth of the full length of the pipe, then performing saw cutting, inspection, treatment by adopting a grinding mode on the surface with local defects, and warehousing.
The seamless pipe prepared by the preparation method can be used as a titanium alloy oil well pipe product.
For a further understanding of the present invention, reference will now be made to the following examples and accompanying tables, which, however, should be construed to further illustrate the features and advantages of the present invention and not to limit the scope of the claims thereto.
The following examples use instrumentation conventional in the art. The experimental procedures, in which specific conditions are not noted in the following examples, are generally carried out under conventional conditions or conditions recommended by the manufacturers. In the following examples, various starting materials were used, and unless otherwise specified, conventional commercially available products were used.
Example 1
Step one, ingot preparation: melting aluminum-niobium intermediate alloy, Mo blocks, pure sponge Zr, iron nails and sponge Ti twice through mixing, pressing electrode bars and vacuum self-consumptionThe alloy ingot of (3) has an alloy phase transition point of 973 ℃.
Step two, preparing a bar blank: cogging and forging at 1150 ℃, upsetting and pulling at 3-4 times, and forging at 960 ℃ twice, and then machining to prepare a phi 600 bar blank.
Step three, cross piercing: heating the bar to 950 ℃, then preserving heat for 420min, and then performing cross rolling perforation to prepare a tube blank with phi 630.
Step four, hot rolling and diameter fixing and reducing: and (3) hot rolling the tube blank after cross rolling perforation, spraying borax as a lubricant into the tube before hot rolling, and controlling the deformation amount to be 50-70%. And then, performing fixed reducing, wherein the outer diameter is reduced by 20-30% in the fixed reducing process, the wall thickness is thickened by about 10% of that after hot rolling, and the pipe with the diameter of phi 508 multiplied by 21 is prepared, and the maximum length of the pipe can reach 10 m.
Step five, heat treatment: and (3) placing the pipe in an electric furnace, heating to 820 ℃, keeping the temperature for 60 minutes, discharging from the furnace, and air cooling.
Step six, post-treatment: and heating the heat-treated pipe to 720 ℃, straightening on an automatic straightening machine, and sawing, inspecting and warehousing the pipe, wherein the bending degree of the pipe meets the technical requirement of less than or equal to 1.5 thousandth.
Example 2
Step one, ingot preparation: melting aluminum-niobium intermediate alloy, Mo blocks, pure sponge Zr, iron nails and sponge Ti twice through mixing, pressing electrode bars and vacuum self-consumptionThe alloy ingot of (2) has an alloy phase transition point of 988 ℃.
Step two, preparing a bar blank: cogging and forging at 1150 ℃, upsetting and pulling at 3-4 times, and forging at 960 ℃ twice, and machining to prepare a phi 350 bar blank.
Step three, cross piercing: heating the bar to 1000 ℃, then preserving heat for 200min, and then performing cross rolling perforation to prepare a tube blank with phi 360.
Step four, hot rolling and fixed reducing: and (3) hot rolling the tube blank after cross rolling perforation, spraying borax as a lubricant into the tube before hot rolling, and controlling the deformation amount to be 50-70%. And then, performing fixed reducing, wherein the outer diameter is reduced by 20-30% in the fixed reducing process, the wall thickness is thickened by about 10% of that after hot rolling, and the pipe with the diameter of phi 219 multiplied by 12.7 is prepared, and the length of the pipe can reach more than 20 m.
Step five, heat treatment: the pipe is placed in a natural gas furnace with micro-oxidation atmosphere (mixed atmosphere of air and natural gas) to be heated to 980 ℃, and is taken out of the furnace for air cooling after being kept for 45 minutes.
Step six, post-treatment: and (3) heating the heat-treated pipe to 750 ℃, straightening the pipe on an automatic straightening machine, wherein the bending degree of the pipe meets the technical requirement of less than or equal to 1.5 thousandth, and then sawing, inspecting and warehousing the pipe.
Example 3
Step one, ingot preparation: melting aluminum-niobium intermediate alloy, Mo blocks, pure sponge Zr, iron nails and sponge Ti twice through mixing, pressing electrode bars and vacuum self-consumptionThe alloy ingot of (3) has an alloy phase transition point of 983 ℃.
Step two, preparing a bar blank: cogging and forging at 1150 ℃, upsetting and drawing for 3-4 times, and forging for two times at 950 ℃ and then machining to prepare a phi 350 bar blank.
Step three, cross piercing: heating the bar to 1250 ℃, then preserving heat for 90min, and then carrying out cross rolling perforation to prepare a tube blank of phi 159.
Step four, hot rolling and diameter fixing and reducing: and (3) hot rolling the tube blank after cross rolling perforation, spraying borax as a lubricant into the tube before hot rolling, and controlling the deformation amount to be 50-70%. And then, performing fixed reducing, wherein the outer diameter is reduced by 20-30% in the fixed reducing process, the wall thickness is thickened by about 10% of that after hot rolling, and the pipe with the diameter of 42 multiplied by 4.85 is prepared, and the maximum length of the pipe can reach 20 m.
Step five, heat treatment: and (3) placing the pipe in a protective atmosphere furnace, heating to 850 ℃, keeping the temperature for 45 minutes, discharging from the furnace, and air cooling.
Step six, post-treatment: and heating the heat-treated pipe to 610 ℃, straightening on an automatic straightening machine, and sawing, inspecting and warehousing the pipe, wherein the bending degree of the pipe meets the technical requirement of less than or equal to 1.5 thousandth.
Effects of the embodiment
(1) Compositions of titanium alloy ingots prepared in examples 1 to 3 in terms of mass percent
TABLE 1 composition of titanium alloy ingots in terms of mass% (/ wt%) prepared in examples 1 to 3
(2) Mechanical property test of the titanium alloy seamless pipes prepared in examples 1 to 3
The titanium alloy seamless pipes prepared in examples 1 to 3, certain domestic P110 steel grade G3 alloy oil pipes, certain foreign Q125 steel grade G3 pipes and API relevant standard mechanical property requirements are compared, as shown in Table 2.
Table 2 comparison of titanium alloy seamless tubing prepared in examples 1-3 with prior art oil pipe and API-related standards
As can be seen from Table 2, the tensile strength, elongation and impact energy of the titanium alloy seamless pipe all meet the mechanical properties of API SPEC 5CT to P110 steel grade. And the impact energy of the titanium alloy seamless pipes prepared in the examples 1 to 3 is obviously greater than that of domestic G3 pipes of the same grade.
(3) And the corrosion resistance of the titanium alloy seamless pipes prepared in examples 1 to 3
Selecting a relatively serious corrosion site working condition, carrying out a simulated working condition corrosion evaluation test on the titanium alloy seamless pipe, evaluating the uniform corrosion performance of the titanium alloy seamless pipe under a specific working condition, and detecting the corrosion performance mainly comprises two aspects: on the one hand, the evaluation test was carried out with reference to NACE-MR0175 at a temperature of 160 ℃ and H2S partial pressure of 5MPa and CO2The partial pressure was 11MPa, the NaCl concentration was 100000ppm Cl, elemental sulfur was 3g/L, the SSCB test period was 720 hours, and the corrosion coupon test period was 168 hours, and the test results obtained according to the above test conditions (including the A method test result, the four-point bending method test result, and the 7-day corrosion condition of the corrosion coupon) are shown in Table 3. Another aspect is to test the annual corrosion rate of seamless pipes, the test results of which are shown in table 3.
TABLE 3 Corrosion resistance test results for titanium alloy seamless tubes prepared in examples 1-3
As can be seen from Table 3, the corrosion resistance test results of the titanium alloy seamless pipes prepared in examples 1 to 3 meet the specification of NACE-MR0175 on the corrosion degree, and no obvious corrosion or pitting phenomenon is found on the surface of the seamless pipe. The annual corrosion rate of the seamless pipe is low, so that the titanium alloy seamless pipe has excellent corrosion resistance.
The seamless pipe prepared by the invention can reduce the weight of the pipe column by 40 percent, thereby improving the tensile safety coefficient of the pipe column; meanwhile, the problem of low safety caused by the conventional P110-grade tubular column can be well solved, and a reliable guarantee is provided for the improvement of the petroleum and natural gas exploitation capability in China.
The present invention provides a high impact toughness titanium alloy and a method for manufacturing seamless pipes using the same, which are described in detail above, and the principle and the specific implementation of the present invention are illustrated herein by using specific examples, which are only used to help understanding the method and the core concept of the present invention. It should be noted that any simple modification, equivalent change and modification made to the above embodiments according to the technical essence of the present invention are within the protective scope of the present invention to those skilled in the art.
Claims (6)
1. The titanium alloy with high impact toughness is characterized by comprising the following chemical components in percentage by weight: 4.0 to 9.0 percent of Al, 0.5 to 5.0 percent of Mo, 1 to 5 percent of Zr, 1 to 5 percent of Nb, 0.2 to 2.0 percent of Fe, and the balance of Ti and inevitable impurities; wherein the content of impurities satisfies N is less than or equal to 0.05%, C is less than or equal to 0.1%, H is less than or equal to 0.015%, and O is less than or equal to 0.15%.
2. A method for producing a seamless pipe using the high impact toughness titanium alloy of claim 1, which essentially comprises the steps of:
step one, ingot preparation: respectively weighing the aluminum-niobium intermediate alloy, the molybdenum block, the pure sponge zirconium, the iron nail and the sponge titanium according to the chemical composition requirements in claim 1, mixing, pressing into an electrode rod, and then putting into a vacuum consumable arc furnace for secondary smelting to obtain a titanium alloy ingot;
step two, preparing a bar blank, namely cogging and forging the titanium alloy ingot obtained in the step one at 1150 ℃, and performing forge change at 970 ~ 1020 ℃ to obtain the bar blank;
step three, oblique piercing, namely placing the bar blank obtained in the step two in a heating furnace to heat to 950 ~ 1200 ℃ and preserving heat for the time of the diameter x (0.5 ~ 1.1.1) min/mm of the bar blank, then adopting a molybdenum-based alloy or high alloy top head, coating a lubricant on the head, placing the lubricant in a central hole of the bar blank after heat preservation, and piercing to obtain a tube blank;
step four, hot rolling and fixed reducing, namely hot rolling the tube blank obtained in the step three, spraying borax into the tube blank before hot rolling, controlling the deformation to be 50 ~ 70%, and then performing fixed reducing to obtain a tube;
step five, heat treatment, namely placing the pipe obtained in the step four into a heat treatment furnace for heat treatment, wherein the heat treatment temperature is 800 ~ 980 ℃;
step six, post-treatment: and (4) straightening, sawing, inspecting and warehousing the heat-treated pipe.
3. The method for preparing seamless pipe material with high impact toughness titanium alloy as claimed in claim 2, wherein in step three, the requirement of the prepared pipe blank is that the outer diameter/wall thickness is =9 ~ 12.
4. The method for preparing the seamless pipe by using the high impact toughness titanium alloy according to the claim 2, wherein in the third step, the micro-oxidation atmosphere in the heating furnace is kept during the heating process of the bar billet, and the micro-oxidation atmosphere is a mixed atmosphere of air and natural gas.
5. The method for producing a seamless pipe using the high impact toughness titanium alloy as claimed in claim 2, wherein in the fourth step, the outside diameter reduction ratio in the sizing and reducing process is 20 ~ 30%, and the wall thickness thickening = wall thickness x after hot rolling (10% ~ 15%).
6. The method for preparing the seamless pipe by using the high-impact-toughness titanium alloy as claimed in claim 2, wherein in the sixth step, the pipe is heated to 600 ~ 700 ℃ for straightening treatment, and the bending degree of the straightened pipe is less than 1.5 per mill of the full length of the pipe.
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| CN111826549A (en) * | 2020-06-04 | 2020-10-27 | 中国船舶重工集团公司第七二五研究所 | High-toughness titanium alloy and method for preparing bar by using same |
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| CN114273429A (en) * | 2021-12-29 | 2022-04-05 | 西部金属材料股份有限公司 | Preparation method of metal pipe difficult to deform |
| CN115029582A (en) * | 2022-07-26 | 2022-09-09 | 中海石油(中国)有限公司 | 860-doped 1086MPa tensile strength titanium alloy drill rod material and preparation method thereof |
| CN115595460A (en) * | 2022-09-29 | 2023-01-13 | 洛阳伍鑫金属材料科技有限公司（Cn） | High-impact-toughness titanium alloy for oil and gas exploitation and preparation method thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2002090607A1 (en) * | 2001-05-07 | 2002-11-14 | Verkhnaya Salda Metallurgical Production Association | Titanium-base alloy |
| CN103146956A (en) * | 2013-03-26 | 2013-06-12 | 武汉武船机电设备有限责任公司 | Titanium alloy pipe and manufacturing method |
| CN105349829A (en) * | 2014-08-21 | 2016-02-24 | 张忠世 | Titanium alloy Ti80 seamless tube and preparation method thereof |
| CN107574335A (en) * | 2017-08-14 | 2018-01-12 | 宝钢特钢有限公司 | A kind of middle strength titanium alloys and preparation method thereof |
| CN109280787A (en) * | 2018-11-30 | 2019-01-29 | 西北有色金属研究院 | A kind of preparation method of petroleum gas industrial titanium alloy seamless tubular goods |
-
2019
- 2019-09-02 CN CN201910824117.4A patent/CN110592425B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2002090607A1 (en) * | 2001-05-07 | 2002-11-14 | Verkhnaya Salda Metallurgical Production Association | Titanium-base alloy |
| CN103146956A (en) * | 2013-03-26 | 2013-06-12 | 武汉武船机电设备有限责任公司 | Titanium alloy pipe and manufacturing method |
| CN105349829A (en) * | 2014-08-21 | 2016-02-24 | 张忠世 | Titanium alloy Ti80 seamless tube and preparation method thereof |
| CN107574335A (en) * | 2017-08-14 | 2018-01-12 | 宝钢特钢有限公司 | A kind of middle strength titanium alloys and preparation method thereof |
| CN109280787A (en) * | 2018-11-30 | 2019-01-29 | 西北有色金属研究院 | A kind of preparation method of petroleum gas industrial titanium alloy seamless tubular goods |
Non-Patent Citations (3)
| Title |
|---|
| （苏）Н.Ф.科什科著、金钦瀚译: "《钢和合金的物理-化学相分析》", 31 December 1982, 国防工业出版社 * |
| 温景林: "《普通高等教育"十二五"规划教材 金属压力加工车间设计 第2版》", 30 September 2011, 冶金工业出版社 * |
| 肖国章: "钛合金油井管的生产加工工艺研发现状", 《钢管》 * |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111330999A (en) * | 2020-02-27 | 2020-06-26 | 中国船舶重工集团公司第七二五研究所 | Medium-strength high-elasticity modulus titanium alloy seamless pipe and preparation method thereof |
| CN111826549A (en) * | 2020-06-04 | 2020-10-27 | 中国船舶重工集团公司第七二五研究所 | High-toughness titanium alloy and method for preparing bar by using same |
| CN112718909A (en) * | 2020-11-23 | 2021-04-30 | 昆明理工大学 | Short-process preparation method of Ti-Al-Nb-Zr-Mo alloy seamless tube |
| CN112718909B (en) * | 2020-11-23 | 2023-09-15 | 昆明理工大学 | Short-flow preparation method of Ti-Al-Nb-Zr-Mo alloy seamless pipe |
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| CN114273429A (en) * | 2021-12-29 | 2022-04-05 | 西部金属材料股份有限公司 | Preparation method of metal pipe difficult to deform |
| CN114273429B (en) * | 2021-12-29 | 2024-04-30 | 西部金属材料股份有限公司 | Preparation method of metal pipe difficult to deform |
| CN115029582A (en) * | 2022-07-26 | 2022-09-09 | 中海石油(中国)有限公司 | 860-doped 1086MPa tensile strength titanium alloy drill rod material and preparation method thereof |
| CN115595460A (en) * | 2022-09-29 | 2023-01-13 | 洛阳伍鑫金属材料科技有限公司（Cn） | High-impact-toughness titanium alloy for oil and gas exploitation and preparation method thereof |
| CN115595460B (en) * | 2022-09-29 | 2024-01-30 | 洛阳伍鑫金属材料科技有限公司 | High impact toughness titanium alloy for oil gas exploitation and preparation method thereof |
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