CN116921491A - Preparation method of high-strength titanium alloy pipe - Google Patents
Preparation method of high-strength titanium alloy pipe Download PDFInfo
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- CN116921491A CN116921491A CN202310865788.1A CN202310865788A CN116921491A CN 116921491 A CN116921491 A CN 116921491A CN 202310865788 A CN202310865788 A CN 202310865788A CN 116921491 A CN116921491 A CN 116921491A
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 79
- 238000002360 preparation method Methods 0.000 title claims abstract description 18
- 238000005242 forging Methods 0.000 claims abstract description 63
- 238000000034 method Methods 0.000 claims abstract description 19
- 238000005096 rolling process Methods 0.000 claims abstract description 19
- 230000007704 transition Effects 0.000 claims abstract description 19
- 238000000137 annealing Methods 0.000 claims abstract description 13
- 238000010438 heat treatment Methods 0.000 claims description 30
- 238000005097 cold rolling Methods 0.000 claims description 22
- 238000004519 manufacturing process Methods 0.000 claims description 13
- 238000004080 punching Methods 0.000 claims description 9
- 238000010304 firing Methods 0.000 claims description 8
- 238000005266 casting Methods 0.000 claims description 3
- 230000008569 process Effects 0.000 abstract description 6
- 239000000047 product Substances 0.000 description 14
- 230000007547 defect Effects 0.000 description 12
- 239000000463 material Substances 0.000 description 8
- 239000002994 raw material Substances 0.000 description 6
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 5
- 239000010936 titanium Substances 0.000 description 5
- 238000003754 machining Methods 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 238000000265 homogenisation Methods 0.000 description 3
- 238000012986 modification Methods 0.000 description 3
- 230000004048 modification Effects 0.000 description 3
- 238000007670 refining Methods 0.000 description 3
- 238000006467 substitution reaction Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 238000003672 processing method Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- 238000011282 treatment Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 101100001673 Emericella variicolor andH gene Proteins 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- 239000003513 alkali Substances 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 125000004435 hydrogen atom Chemical class [H]* 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 239000010955 niobium Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 238000013021 overheating Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000004321 preservation Methods 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000009987 spinning Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000005406 washing Methods 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Classifications
-
- 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
-
- 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
- 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
- B21C37/30—Finishing tubes, e.g. sizing, burnishing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
Abstract
The invention discloses a preparation method of a high-strength titanium alloy pipe, which comprises the following steps: 1. homogenizing the cast ingot at the temperature of 250-350 ℃ above the phase transition point; 2. cogging and forging at 250-350 ℃ above the phase transition point and 200-250 ℃ above the phase transition point; 3. performing 3-fire homogenizing forging at the temperature of between 40 and 80 ℃ below the phase transition point; 4. upsetting and hole making are carried out at the temperature of between 50 and 30 ℃ below the phase transition point; 5. intermediate rolling and annealing; sixth,: and rolling the finished product for multiple times to obtain the titanium alloy pipe with good dimensional accuracy. The titanium alloy seamless pipe prepared by the process has fine tissue and uniform wall thickness, and has better straightness and surface smoothness.
Description
Technical Field
The invention belongs to the technical field of processing of titanium alloy pipes, and particularly relates to a preparation method of a high-strength titanium alloy pipe.
Background
Titanium and titanium alloy have the characteristics of high specific strength, low density, high temperature resistance, oxidation resistance, corrosion resistance, no magnetism, good welding performance and the like, and become one of important structural materials in the fields of aerospace, weapons, ships and the like. Along with the increasing wide application of titanium and titanium alloy in army civil products, the requirements on titanium and titanium alloy products are not only limited to bar materials, forgings, plates, wires and other varieties, but also the requirements on high-precision and high-performance pipes are more and more urgent, and higher requirements are put forward on the processing technology of the pipes.
At present, a processing method generally adopted by titanium and titanium alloy pipes is to prepare a pipe blank by utilizing titanium alloy cast ingots through cogging, forging, perforating and punching, and then form pipe products through hot rolling, hot extrusion and other modes, but the straightness and wall thickness uniformity of the hot processed pipes are poor, shaping and straightening processes are often required to be added, the surface of the hot formed pipes is seriously oxidized, a large number of defects exist, and the hot formed pipes are required to be subjected to subsequent acid-alkali washing, polishing and other processing treatments, so that the problems of long production period, low material utilization rate, high use cost and the like are caused. In addition, the high-strength titanium alloy with strength exceeding 1200MPa is added with more beta stabilizing elements (such as Cr, fe and the like) to improve alloying so as to obtain higher strength and reduce material cost, but the addition of the higher beta stabilizing elements is easy to generate component segregation in the process of smelting cast ingot, and the component segregation phenomenon is difficult to eliminate through subsequent cogging forging, so that the structure of a product is uneven.
The Chinese patent with publication number of CN112275830A discloses a grain refining processing method of a titanium alloy tube blank for spinning, the ingot cogging forging temperature of the method is 150-200 ℃ above the transformation point and 50-120 ℃ above the transformation point, the homogenization requirements of cogging forging can be met for alpha-type titanium alloy, alpha+beta-type titanium alloy and the like with higher transformation point temperature, but the high-alloying high-strength beta-type titanium alloy with generally lower transformation point (about 800 ℃) is obviously lower in the cogging forging temperature, the good effect of tissue homogenization during ingot cogging forging is difficult to achieve, in addition, the problems of poor tube surface quality, limited tube length and the like exist in the preparation of tubes by adopting a hot rolling method on a ring rolling machine. In order to overcome the technical defects, it is necessary to invent a preparation method for the titanium alloy pipe with uniform structure, good surface quality and high wall thickness precision.
Disclosure of Invention
The purpose of the invention is that: aiming at the defects of the prior art, a preparation method of the high-strength titanium alloy pipe is provided.
In order to solve the technical problem, the invention adopts the following technical scheme: a preparation method of a high-strength titanium alloy pipe. The method comprises the following steps:
step 1: casting the titanium alloy ingot at a heating temperature of a titanium alloy phase transition point T β Of (T) β +250)℃～(T β Heating and preserving heat at +350) DEG C, and then forging for 1 time to obtain a first bar; the 1-fire forging comprises 1-2 upsetting and drawing steps, wherein the total upsetting ratio of each upsetting is E, and the length of each drawing step is H 1 。
Step 2: the first bar in the step 1 is heated to be the titanium alloy phase transition point T β Of (T) β +200)℃～(T β Heating and preserving heat at +250) DEG C, and then forging for 1 time to obtain a second bar; the 1-fire forging comprises 1-2 upsetting and drawing steps, wherein the total upsetting ratio of each upsetting is E, and the length of each drawing step is H 2 。
Step 3: the second bar in the step 2 is heated to be the titanium alloy phase transition point T β Of (T) β -40)℃～(T β Forging for 3 times under the condition of +80) DEG C to obtain a third bar; the forging each time comprises upsetting and drawing 1-2 times, the total upsetting ratio of each upsetting is E, and the length of the last forging and drawing is H 3 。
Step 4: the third bar in step 3 is heated at a heating temperature (T β -50)℃～(T β Upsetting for 1 time at the temperature of-30) ℃, and then forming holes to obtain a tube blank with the outer diameter of R and the inner diameter of R; the total upsetting ratio of the upsetting is E. Upsetting and punching were completed within 1 firing.
Step 5: and (3) carrying out multi-pass intermediate rolling on the tube blank in the step (4), and carrying out annealing once after each pass of intermediate rolling to obtain an intermediate tube.
Step 6: and (5) rolling the intermediate pipe in the step (5) into a finished product for multiple passes to obtain the pipe.
The heating and heat preserving time in the step 1 is not less than 25 hours, and the length H of the drawing is long 1 The ratio to the maximum cross-sectional thickness of the first bar is not greater than 2.45.
The total upsetting ratio E in step 1, step 2, step 3 and step 4 satisfies the formula (1):
wherein the total upsetting ratio E of each upsetting is completed by n times of single upsetting deformation, delta i The thickness deformation of the section for the ith upsetting is more than or equal to 1 and less than or equal to n.
The total upsetting ratio E in step 1 is calculated according to formula (1), wherein n=5 to 12, preferably 8 to 10; delta i =1.03 to 1.15, preferably 1.09 to 1.11. Length H of the extension 1 The ratio to the maximum cross-sectional thickness of the first bar is not greater than 2.45.
The total upsetting ratio E in step 2 is calculated according to formula (1), wherein n=5 to 12, preferably 7 to 10; delta i =1.05 to 1.16, preferably 1.08 to 1.12. The length of each drawing is H 2 ＝H 1 ×λ 1 Wherein lambda is 1 Is a proportionality coefficient and lambda 1 ＝0.95～1.15。
The heating temperature of the 3-fire forging in the step 3 is sequentially T 1 、T 2 、T 3 Wherein T is 1 ＜T β ，T 2 ＞T β ，T 3 ＜T β And T is 1 -T 3 Not less than 8 ℃; the total upsetting ratio E is calculated according to formula (1), wherein n=4 to 10, preferably 6 to 8; delta i =1.12 to 1.33, preferably 1.18 to 1.25. Length H of the last fire time extension 3 ＝H 2 ×λ 2 Wherein lambda is 2 Is a proportionality coefficient and lambda 2 The value is 1.20 to 1.65; .
The total upsetting ratio E in step 4 is calculated according to formula (1), wherein n=2 to 5, preferably 3 to 4; delta i =1.25 to 1.55, preferably 1.35 to 1.45. The outer diameter R and the inner diameter R of the tube blank satisfy the following conditions: r=r×α, where α is a scaling factor and α=0.25 to 0.55.
In the step 5, the intermediate rolling is multi-pass cold rolling, wherein the number of rolling passes is 2-6, and the external diameter thinning rate of each pass is 5-15%; the heating temperature of the intermediate annealing is 550-750 ℃.
And (3) rolling the finished product in the step (6) into multi-pass cold rolling, wherein the number of rolling passes is 2-4, and the external diameter thinning rate of each pass is 3-12%.
Preferably, the upsetting and punching in step 3 are completed within 1 fire.
Preferably, the third bar material can be separated according to practical situations before upsetting in the step 4, and the ratio of the length to the diameter of the bar material after separation is not more than 2.3.
Compared with the prior art, the invention has the following advantages:
(1) Firstly, unlike the currently commonly used titanium alloy cogging forging process, the invention has the advantages that the titanium alloy ingot is cast in a higher single-phase zone (T β +250)℃～(T β The heating and heat preservation treatment is carried out for a long time at +350), and the main technical effect is to further homogenize the components and the structure of the titanium alloy cast ingot and provide a structure foundation for homogenization and grain refining of subsequent forging deformation.
(2) Second, the present invention employs higher (T β +250)℃～(T β +350) DEG C sum (T β +200)℃～(T β +250) DEG C, and the total upsetting ratio, the deformation amount of upsetting each time and other deformation parameters are comprehensively controlled during forging, so that coarse and uneven structures caused by overheating are avoided, and the ingot tissues are fully crushed.
(3) Thirdly, the invention performs ' low, high and low ' alternate forging deformation of 3 fires at an ' alpha+beta two-phase region, a ' beta single-phase region and an ' alpha+beta two-phase region ' near the phase transition point, wherein the 1 st firing forging deformation is performed at the ' alpha+beta two-phase region, so as to refine and spheroidize an alpha structure and provide recrystallization energy for the next high-temperature deformation; the forging deformation of the 2 nd time is carried out at a lower temperature in a beta single-phase region, the recrystallization of the 1 st time can be utilized to lead the structure to be homogenized and grown, and the forging deformation is further crushed and refined into beta grain structure at the temperature; the 3 rd hot forging deformation is also performed in the alpha+beta two-phase region, but the heating temperature is lower than the 1 st hot forging deformation temperature, and the stage adopts larger upsetting and drawing deformation amount to refine and homogenize the structure.
(4) Finally, upsetting and blank making are carried out at a lower temperature in an alpha+beta two-phase region, blank making is completed on the premise of retaining the refining and homogenizing structure of the previous stage, then a method of combining multi-pass intermediate cold rolling, intermediate annealing and multi-pass finished product cold rolling is adopted, and parameters such as the number of cold rolling passes, annealing temperature, the outer diameter thinning rate of each pass and the like are controlled, so that the tubular product with uniform structure, good surface quality and high dimensional precision is finally obtained. The invention has good process controllability and mass production stability.
Drawings
In order to more clearly illustrate the technical solution of the implementation of the present invention, the following description will briefly explain the drawings that need to be used in the examples of the present invention. It is evident that the drawings described below are only some embodiments of the invention and that other drawings may be obtained from these drawings without inventive effort for a person skilled in the art.
FIG. 1 shows a process flow for carrying out the invention.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention more clear, the technical solutions of the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings in the embodiments of the present invention. It will be apparent that the described embodiments are some, but not all, embodiments of the invention. All other embodiments obtained by those skilled in the art based on the embodiments of the present invention without making any inventive effort are intended to fall within the scope of the present invention.
Features of various aspects of embodiments of the invention are described in detail below. In the following detailed description, numerous specific details are set forth in order to provide a thorough understanding of the 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 for a better understanding of the invention by showing examples of the invention. The present invention is not limited to any particular arrangement and method provided below, but covers any modifications, substitutions, etc. of all product constructions, methods, and the like covered without departing from the spirit of the invention.
In the drawings and the following description, well-known structures and techniques have not been shown in detail in order not to unnecessarily obscure the present invention. The following is a detailed description of embodiments of the invention, taken in conjunction with the accompanying drawings, using a TB8 titanium alloy ingot as a raw material. The TB8 titanium alloy comprises the following main chemical components in percentage by mass: 14.0 to 16.0 percent of molybdenum, 2.4 to 3.2 percent of niobium, 2.5 to 3.5 percent of aluminum and 3.5 to 4.5 percent of silicon, and impurity elements are controlled as follows: less than or equal to 0.4 percent of iron, less than or equal to 0.05 percent of carbon, less than or equal to 0.05 percent of nitrogen, less than or equal to 0.015 percent of hydrogen, less than or equal to 0.17 percent of oxygen, less than or equal to 0.01 percent of other elements singly and less than or equal to 0.04 percent of the sum, and the balance of titanium.
The preparation method for producing qualified TB8 titanium alloy pipe by taking TB8 titanium alloy cast ingot as raw material comprises the following steps:
step 1: casting the titanium alloy ingot at a heating temperature of a titanium alloy phase transition point T β Of (T) β +250)℃～(T β Heating and preserving heat at +350) deg.C for at least 25 hr, upsetting and drawing to forge for 1-2 times, upsetting to obtain the upsetting ratio En＝5～12，δ i =1.03 to 1.15, length per draw is H 1 The ratio of the maximum cross-sectional thickness of the bar to the bar is not more than 2.45, and the first bar is obtained.
Step 2: the first bar in the step 1 is heated to be the titanium alloy phase transition point T β Of (T) β +200)℃～(T β Heating at +250) deg.C, forging for 1-2 times, and upsetting to obtain the final productn＝5～12，δ i =1.05 to 1.16, length per draw is H 2 And H is 2 ＝H 1 ×λ 1 ，λ 1 =0.95 to 1.15, yielding a second bar.
Step 3: the second bar in the step 2 is heated to be the titanium alloy phase transition point T β Of (T) β -40)℃～(T β And (80) C, 3 times of forging is carried out under the condition of +80). Wherein, the 1 st forging is performed at the heating temperature T 1 (T 1 ＜T β ) The upsetting and drawing are carried out for 1 to 2 times under the condition that the total upsetting ratio E of each upsetting is completed by a plurality of upsetting deformations, andn＝4～10，δ i =1.12 to 1.33; forging at heating temperature T 2 (T 2＞ T β ) Upsetting and drawing for 1-2 times, wherein the total upsetting ratio E of each upsetting is completed by multiple upsetting deformations, and +.>n＝4～10，δ i =1.12 to 1.33; forging at heating temperature T3 rd time 3 (T 3 ＜T β And T is 1 -T 3 The upsetting and drawing are carried out for 1 to 2 times at the temperature of more than or equal to 8 ℃, the total upsetting ratio E of each upsetting is completed by multiple upsetting deformations, and +.>n＝4～10，δ i =1.12 to 1.33, the length of the drawn length is H 3 And (2) andH 3 ＝H 2 ×λ 2 ，λ 2 =1.20 to 1.65, yielding a third bar.
Step 4: the third bar in step 3 is heated at a heating temperature (T β -50)℃～(T β Upsetting at-30deg.C for 1 fire time, with a total upsetting ratio of E, andn＝2～5，δ i after that, a tube blank having an outer diameter R and an inner diameter R is obtained by hole forming, and r=r×α, α=0.25 to 0.55. Upsetting and punching were completed within 1 firing.
Step 5: performing multi-pass intermediate cold rolling on the tube blank in the step 4, wherein the number of rolling passes is 2-6, and the outer diameter thinning rate of each pass is 5-15%; and (3) carrying out primary annealing after each pass of intermediate cold rolling, wherein the heating temperature of the annealing is 550-750 ℃, and obtaining the intermediate pipe.
Step 6: and (3) performing multi-pass finished product cold rolling on the intermediate pipe in the step (5), wherein the number of rolling passes is 2-4, and the external diameter thinning rate of each pass is 3-12%, so as to obtain the pipe.
Step 7: and (3) checking the structure, the surface quality, the straightness and the wall thickness of the pipe in the step (6), wherein the pipe is uniform in structure, has no defects such as cracks, folds and the like, and is high in straightness and wall thickness precision. The preparation process of the TB8 titanium alloy pipe obtained by the specific embodiment of the invention is stable and controllable, and the structure is fine and uniform.
The present invention will be described in further detail with reference to examples. The invention is illustrated by four examples which are provided for further details and are not intended to be limiting.
Example 1: preparation of TB8 titanium alloy pipe with external diameter of 145mm and internal diameter of 110mm
In the embodiment, a cast ingot of TB8 titanium alloy with the length of 150mm and the diameter of 180mm is adopted, a riser and surface defects of the cast ingot are cut off by machining, and chamfer angles are formed at two ends of the cast ingot, and the phase transition point (T β ) Is T β ＝815℃。
The method for preparing the high-strength titanium alloy pipe takes the TB8 titanium alloy cast ingot as a raw material blank, and the method for producing the qualified TB8 titanium alloy pipe comprises the following steps:
step 1: heating and preserving the temperature of TB8 titanium alloy cast ingot at 1165 ℃ for 25 hours, then forging by upsetting and pulling, wherein the total upsetting ratio of upsetting is completed by 6 times of single upsetting deformation, and the thickness deformation of the section of each upsetting is delta respectively 1 ＝1.05，δ 2 ＝1.1，δ 3 ＝1.06，δ 4 ＝1.1，δ 5 ＝1.08，δ 6 =1.07, total upsetting ratio of 1.26, length of drawn length of 155mm, resulting in a first bar.
Step 2: forging the first bar in the step 1 at 1050 ℃ in a upsetting and pulling way, wherein the total upsetting ratio of upsetting is finished by 7 times of single upsetting deformation, and the deformation amount of the section thickness of each upsetting is delta respectively 1 ＝1.08，δ 2 ＝1.09，δ 3 ＝1.11，δ 4 ＝1.11，δ 5 ＝1.11，δ 6 ＝1.1，δ 7 =1.12, total upsetting ratio of 1.41, length of elongation of 158mm, yielding a second bar.
Step 3: the second bar in the step 2 is firstly subjected to upsetting-drawing forging at 800 ℃, the total upsetting ratio of upsetting is completed by 5 times of single upsetting deformation, and the deformation amount of the section thickness of each upsetting is delta respectively 1 ＝1.24，δ 2 ＝1.26，δ 3 ＝1.25，δ 4 ＝1.29，δ 5 =1.31, total upsetting ratio of 1.59, length of draw of 149mm; then forging by upsetting and drawing at 875 deg.C, the upsetting total upsetting ratio is completed by 6 times of single upsetting deformation, and the thickness deformation of each upsetting section is delta 1 ＝1.15，δ 2 ＝1.14，δ 3 ＝1.13，δ 4 ＝1.14，δ 5 ＝1.13，δ 6 =1.13, total upsetting ratio of 1.48, length of draw of 149mm; then forging at 790 ℃ with upsetting and drawing, wherein the total upsetting ratio of upsetting is completed by 5 times of single upsetting deformation, and the thickness deformation of the section of each upsetting is delta respectively 1 ＝1.26，δ 2 ＝1.25，δ 3 ＝1.28，δ 4 ＝1.29，δ 5 =1.26, total upsettingThe thickness ratio was 1.81, and the length of the drawn bar was 215mm, to obtain a third bar having a diameter of 150 mm.
Step 4: dividing the third bar in the step 3 to obtain bars with the diameter of 150mm and the length of 100mm, then performing one-time upsetting forging at 785 ℃, wherein the total upsetting ratio of upsetting is completed by 3 times of single upsetting deformation, and the section thickness deformation of each upsetting is delta respectively 1 ＝1.25，δ 2 ＝1.35，δ 3 =1.45, the total upsetting ratio was 1.94, and then a tube blank having an outer diameter of 205mm and an inner diameter of 110mm was punched. Upsetting and punching were completed within 1 firing.
Step 5: and (3) performing 2-pass intermediate cold rolling on the tube blank in the step (4), wherein the external diameter thinning rate of each pass is 8%, and performing intermediate annealing at 550 ℃ after each pass of intermediate cold rolling to obtain an intermediate tube with the external diameter of 170mm and the internal diameter of 110 mm.
Step 6: and (3) performing 3-pass finished product cold rolling on the intermediate pipe in the step (5), wherein the external diameter thinning rate of each pass is 5%, and the pipe with the external diameter of 145mm and the internal diameter of 110mm is obtained.
Step 7: and (3) checking the structure, the surface quality, the straightness and the wall thickness of the pipe in the step (6), wherein the pipe is uniform in structure, has no defects such as cracks, folds and the like, and is high in straightness and wall thickness precision. The preparation process of the TB8 titanium alloy pipe obtained by the specific embodiment of the invention is stable and controllable, and the structure is fine and uniform.
Example 2: preparation of TB8 titanium alloy pipe with external diameter of 160mm and internal diameter of 120mm
In the embodiment, a cast ingot of TB8 titanium alloy with the length of 200mm and the diameter of 250mm is adopted, a riser and surface defects of the cast ingot are cut off by machining, and chamfer angles are formed at two ends of the cast ingot, and the phase transition point (T β ) Is T β ＝815℃。
The method for preparing the high-strength titanium alloy pipe takes the TB8 titanium alloy cast ingot as a raw material blank, and the method for producing the qualified TB8 titanium alloy pipe comprises the following steps:
step 1: heating and preserving heat of TB8 titanium alloy cast ingot at 1160 ℃ for 28 hours, and then forging by upsetting and pullingThe total upsetting ratio of upsetting is completed by 12 times of single upsetting deformation, and the deformation amount of the section thickness of each upsetting is delta respectively 1 ＝1.05，δ 2 ＝1.06，δ 3 ＝1.05，δ 4 ＝1.06，δ 5 ＝1.05，δ 6 ＝1.08，δ 7 ＝1.07，δ 8 ＝1.08，δ 9 ＝1.06，δ 10 ＝1.09，δ 11 ＝1.08，δ 12 =1.07, total upsetting ratio of 1.47, length of elongation of 205mm, resulting in a first bar.
Step 2: forging the first bar in the step 1 at 1065 ℃ in a upsetting-drawing way, wherein the total upsetting ratio of upsetting is completed by 5 times of single upsetting deformation, and the deformation amount of the section thickness of each upsetting is delta respectively 1 ＝1.13，δ 2 ＝1.15，δ 3 ＝1.16，δ 4 ＝1.12，δ 5 =1.12, total upsetting ratio of 1.38, length of elongation of 230mm, yielding a second bar.
Step 3: the second bar in the step 2 is firstly subjected to upsetting-drawing forging at 785 ℃, the total upsetting ratio of upsetting is completed by 10 times of single upsetting deformation, and the thickness deformation of the section of each upsetting is delta respectively 1 ＝1.15，δ 2 ＝1.14，δ 3 ＝1.16，δ 4 ＝1.14，δ 5 ＝1.13，δ 6 ＝1.13，δ 7 ＝1.15，δ 8 ＝1.16，δ 9 ＝1.12，δ 10 =1.17, total upsetting ratio of 1.97, length of draw of 225mm; then forging by upsetting and drawing at 875 deg.C, the upsetting total upsetting ratio is completed by 5 times of single upsetting deformation, and the thickness deformation of each upsetting section is delta 1 ＝1.15，δ 2 ＝1.18，δ 3 ＝1.22，δ 4 ＝1.25，δ 5 =1.16, total upsetting ratio of 1.81, length of draw out of 233mm; then forging by upsetting and drawing at 790 ℃ with the total upsetting ratio of upsetting being completed by 4 times of single upsetting deformation, and the thickness deformation of the section of each upsetting is delta respectively 1 ＝1.31，δ 2 ＝1.28，δ 3 ＝1.27，δ 4 =1.33, total upsetting ratio of 1.56, length of elongation of 285mm, giving a third bar with diameter of 210 mm.
Step 4: forging the third bar in the step 3 at 765 ℃ by one upsetting, wherein the total upsetting ratio of upsetting is completed by 2 times of single upsetting deformation, and the deformation amount of the section thickness of each upsetting is delta respectively 1 ＝1.55，δ 2 =1.33, the total upsetting ratio was 1.43, and then a tube blank having an outer diameter of 250mm and an inner diameter of 120mm was punched. Upsetting and punching were completed within 1 firing.
Step 5: and (3) performing 6-pass intermediate cold rolling on the tube blank in the step (4), wherein the external diameter thinning rate of each pass is 5%, and performing intermediate annealing at 550 ℃ after each pass of intermediate cold rolling to obtain an intermediate tube with the external diameter of 180mm and the internal diameter of 120 mm.
Step 6: and (3) performing 4-pass finished product cold rolling on the intermediate pipe in the step (5), wherein the external diameter thinning rate of each pass is 3%, and the pipe with the external diameter of 160mm and the internal diameter of 120mm is obtained.
Step 7: and (3) checking the structure, the surface quality, the straightness and the wall thickness of the pipe in the step (6), wherein the pipe is uniform in structure, has no defects such as cracks, folds and the like, and is high in straightness and wall thickness precision. The preparation process of the TB8 titanium alloy pipe obtained by the specific embodiment of the invention is stable and controllable, and the structure is fine and uniform.
Example 3: preparation of TB8 titanium alloy pipe with outer diameter of 40mm and inner diameter of 25mm
In the embodiment, a cast ingot of TB8 titanium alloy with the length of 150mm and the diameter of 100mm is adopted, a riser and surface defects of the cast ingot are cut off by machining, and chamfer angles are formed at two ends of the cast ingot, and the phase transition point (T β ) Is T β ＝815℃。
The method for preparing the high-strength titanium alloy pipe takes the TB8 titanium alloy cast ingot as a raw material blank, and the method for producing the qualified TB8 titanium alloy pipe comprises the following steps:
step 1: heating and preserving the temperature of TB8 titanium alloy cast ingot for 26 hours at 1155 ℃, then forging by upsetting and pulling, wherein the total upsetting ratio of upsetting is completed by 10 times of single upsetting deformation, and the deformation of the section thickness of each upsetting is delta respectively 1 ＝1.06，δ 2 ＝1.06，δ 3 ＝1.06，δ 4 ＝1.08，δ 5 ＝1.08，δ 6 ＝1.07，δ 7 ＝1.07，δ 8 ＝1.08，δ 9 ＝1.08，δ 10 =1.08, total upsetting ratio of 1.42, length of draw was 155mm, resulting in a first bar.
Step 2: forging the first bar in the step 1 at 1060 ℃ in a upsetting-drawing way, wherein the total upsetting ratio of upsetting is finished by 8 times of single upsetting deformation, and the deformation amount of the section thickness of each upsetting is delta respectively 1 ＝1.12，δ 2 ＝1.13，δ 3 ＝1.12，δ 4 ＝1.13，δ 5 ＝1.14，δ 6 ＝1.14，δ 7 ＝1.12，δ 8 =1.12, total upsetting ratio of 1.62, length of elongation of 150mm, yielding a second bar.
Step 3: the second bar in the step 2 is firstly subjected to upsetting-drawing forging at 795 ℃, the total upsetting ratio of upsetting is completed by 6 times of single upsetting deformation, and the thickness deformation of the section of each upsetting is delta respectively 1 ＝1.24，δ 2 ＝1.27，δ 3 ＝1.24，δ 4 ＝1.25，δ 5 ＝1.26，δ 6 =1.28, total upsetting ratio of 1.98, length of draw 155mm; then forging by upsetting and drawing at 895 ℃, wherein the total upsetting ratio of upsetting is completed by 6 times of single upsetting deformation, and the deformation amount of the section thickness of each upsetting is delta respectively 1 ＝1.12，δ 2 ＝1.12，δ 3 ＝1.15，δ 4 ＝1.13，δ 5 ＝1.14，δ 6 =1.13, total upsetting ratio of 1.45, length of draw 150mm; then forging by upsetting and drawing at 775 deg.C, the upsetting total upsetting ratio is completed by 4 times of single upsetting deformation, and the deformation of section thickness of each upsetting is delta 1 ＝1.28，δ 2 ＝1.31，δ 3 ＝1.27，δ 4 =1.32, total upsetting ratio of 1.55, length of the drawn length of 225mm, obtaining a third bar with a diameter of 80 mm.
Step 4: dividing the third bar in the step 3 to obtain bars with the diameter of 80mm and the length of 100mm, and then performing one-time upsetting forging at the temperature of 805 ℃ to change the total upsetting ratio of upsetting from 5 times of single upsettingThe deformation of the section thickness of each upsetting is delta 1 ＝1.44，δ 2 ＝1.45，δ 3 ＝1.48，δ 4 ＝1.45，δ 5 =1.46, the total upsetting ratio was 1.43, and then a tube blank having an outer diameter of 95mm and an inner diameter of 25mm was punched. Upsetting and punching were completed within 1 firing.
Step 5: and (3) performing 6-pass intermediate cold rolling on the tube blank in the step (4), wherein the external diameter thinning rate of each pass is 5%, and performing intermediate annealing at 550 ℃ after each pass of intermediate cold rolling to obtain an intermediate tube with the external diameter of 70mm and the internal diameter of 25 mm.
Step 6: and (3) performing 4-pass finished product cold rolling on the intermediate pipe in the step (5), wherein the external diameter thinning rate of each pass is 12%, and the pipe with the external diameter of 40mm and the internal diameter of 25mm is obtained.
Step 7: and (3) checking the structure, the surface quality, the straightness and the wall thickness of the pipe in the step (6), wherein the pipe is uniform in structure, has no defects such as cracks, folds and the like, and is high in straightness and wall thickness precision. The preparation process of the TB8 titanium alloy pipe obtained by the specific embodiment of the invention is stable and controllable, and the structure is fine and uniform.
Example 4: preparing the TB8 titanium alloy pipe with the outer diameter of 250mm and the inner diameter of 220 mm.
In the embodiment, a cast ingot of TB8 titanium alloy with the length of 500mm and the diameter of 320mm is adopted, a riser and surface defects of the cast ingot are cut off by machining, and chamfer angles are formed at two ends of the cast ingot, and the phase transition point (T β ) Is T β ＝815℃。
The method for preparing the high-strength titanium alloy pipe takes the TB8 titanium alloy cast ingot as a raw material blank, and the method for producing the qualified TB8 titanium alloy pipe comprises the following steps:
step 1: heating and preserving the temperature of TB8 titanium alloy cast ingot for 35 hours at 1150 ℃, then forging by upsetting and pulling, wherein the total upsetting ratio of upsetting is completed by 11 times of single upsetting deformation, and the deformation of the thickness of the section of each upsetting is delta respectively 1 ＝1.06，δ 2 ＝1.05，δ 3 ＝1.05，δ 4 ＝1.07，δ 5 ＝1.05，δ 6 ＝1.05，δ 7 ＝1.08，δ 8 ＝1.08，δ 9 ＝1.06，δ 10 ＝1.09，δ 11 =1.08, total upsetting ratio of 1.46, length of elongation of 520mm, resulting in a first bar.
Step 2: forging the first bar in the step 1 at 1075 ℃ by upsetting and pulling, wherein the total upsetting ratio of upsetting is completed by 10 times of single upsetting deformation, and the deformation of the section thickness of each upsetting is delta respectively 1 ＝1.08，δ 2 ＝1.07，δ 3 ＝1.06，δ 4 ＝1.08，δ 5 ＝1.08，δ 6 ＝1.07，δ 7 ＝1.07，δ 8 ＝1.07，δ 9 ＝1.06，δ 10 =1.08, total upsetting ratio of 1.42, length of elongation of 500mm, yielding a second bar.
Step 3: the second bar in the step 2 is firstly subjected to upsetting-drawing forging at 780 ℃, the total upsetting ratio of upsetting is completed by 9 times of single upsetting deformation, and the thickness deformation of the section of each upsetting is delta respectively 1 ＝1.14，δ 2 ＝1.14，δ 3 ＝1.16，δ 4 ＝1.14，δ 5 ＝1.14，δ 6 ＝1.13，δ 7 ＝1.15，δ 8 ＝1.16，δ 9 =1.15, total upsetting ratio of 1.96, length of draw of 510mm; then forging by upsetting and drawing at 895 ℃, wherein the total upsetting ratio of upsetting is completed by 6 times of single upsetting deformation, and the deformation amount of the section thickness of each upsetting is delta respectively 1 ＝1.21，δ 2 ＝1.18，δ 3 ＝1.22，δ 4 ＝1.25，δ 5 ＝1.16，δ 6 =1.18, total upsetting ratio of 1.81, length of draw of 510mm; then forging by upsetting and drawing at 770 deg.C, the upsetting total upsetting ratio is completed by 4 times of single upsetting deformation, and the thickness deformation of each upsetting section is delta 1 ＝1.27，δ 2 ＝1.28，δ 3 ＝1.1.32，δ 4 =1.33, total upsetting ratio of 1.59, length of elongation of 650mm, obtaining a third bar with diameter of 280 mm.
Step 4: separating the third bar material in the step 3 to obtain a bar material with a diameter of 320mm and a length of 280mm, and then performing one step at 7760 DEG CThe upsetting forging is carried out for a plurality of times, the total upsetting ratio of upsetting is completed by 3 times of single upsetting deformation, and the thickness deformation of the section of each upsetting is delta respectively 1 ＝1.55，δ 2 ＝1.33，δ 2 =1.33, the total upsetting ratio was 1.66, and then a tube blank having an outer diameter of 410mm and an inner diameter of 220mm was punched. Upsetting and punching were completed within 1 firing.
Step 5: and (3) performing 4-pass intermediate cold rolling on the tube blank in the step (4), wherein the external diameter thinning rate of each pass is 8%, and performing intermediate annealing at 550 ℃ after each pass of intermediate cold rolling to obtain an intermediate tube with the external diameter of 290mm and the internal diameter of 220 mm.
Step 6: and (3) performing 3-pass finished product cold rolling on the intermediate pipe in the step (5), wherein the external diameter thinning rate of each pass is 5%, and the pipe with the external diameter of 250mm and the internal diameter of 220mm is obtained.
Step 7: and (3) checking the structure, the surface quality, the straightness and the wall thickness of the pipe in the step (6), wherein the pipe is uniform in structure, has no defects such as cracks, folds and the like, and is high in straightness and wall thickness precision. The preparation process of the TB8 titanium alloy pipe obtained by the specific embodiment of the invention is stable and controllable, and the structure is fine and uniform.
Finally, it should be noted that: the above embodiments are only for illustrating the technical solution of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art can easily think about various equivalent modifications or substitutions within the technical scope of the present invention, and these modifications or substitutions should be covered in the scope of the present invention.
Claims (10)
1. The preparation method of the high-strength titanium alloy pipe is characterized by comprising the following steps of:
step 1: casting the titanium alloy ingot at a heating temperature of a titanium alloy phase transition point T β Of (T) β +250)℃～(T β Heating and preserving heat at +350) DEG C, and then forging for 1 time to obtain a first bar; the 1-fire forging comprises 1-2 upsetting and drawing steps, wherein the total upsetting ratio of each upsetting is E, and the length of each drawing step is H 1 。
Step 2: the steps are as follows1, wherein the heating temperature of the first bar is the titanium alloy phase transition point T β Of (T) β +200)℃～(T β Heating and preserving heat at +250) DEG C, and then forging for 1 time to obtain a second bar; the 1-fire forging comprises 1-2 upsetting and drawing steps, wherein the total upsetting ratio of each upsetting is E, and the length of each drawing step is H 2 。
Step 3: the second bar in the step 2 is heated to be the titanium alloy phase transition point T β Of (T) β -40)℃～(T β Heating and preserving heat at +80) DEG C, and forging for 3 times to obtain a third bar; the forging each time comprises upsetting and drawing 1-2 times, the total upsetting ratio of each upsetting is E, and the length of the last forging and drawing is H 3 。
Step 4: the third bar in step 3 is heated at a heating temperature (T β -50)℃～(T β Upsetting for 1 time at the temperature of-30) ℃, and then forming holes to obtain a tube blank with the outer diameter of R and the inner diameter of R; the total upsetting ratio of the upsetting is E. Upsetting and punching were completed within 1 firing.
Step 5: and (3) carrying out intermediate rolling on the tube blank in the step (4), and carrying out primary annealing after each pass of intermediate rolling to obtain an intermediate tube.
Step 6: and (5) rolling the intermediate pipe in the step (5) to obtain the pipe.
2. The method for producing a high-strength titanium alloy pipe according to claim 1, wherein the heating and heat-retaining time in step 1 is not less than 25 hours.
3. The method for producing a high-strength titanium alloy tube according to claim 1, wherein the total upsetting ratio E in step 1, step 2, step 3 and step 4 satisfies the formula (1):
wherein the total upsetting ratio E of each upsetting consists of n times of single upsettingFinishing coarse deformation, delta i The thickness deformation of the section for the ith upsetting is more than or equal to 1 and less than or equal to n.
4. A method of producing a high strength titanium alloy pipe according to claim 3, wherein the total upsetting ratio E in step 1 is calculated according to formula (1), wherein n = 5 to 12; delta i =1.03 to 1.15; length H of the extension 1 The ratio to the maximum cross-sectional thickness of the first bar is not greater than 2.45.
5. A method for producing a high-strength titanium alloy pipe according to claim 3, wherein the total upsetting ratio E in step 2 is calculated according to formula (1), wherein n=5 to 12, δ i =1.05 to 1.16; the length of each drawing is H 2 ＝H 1 ×λ 1 Wherein lambda is 1 Is a proportionality coefficient and lambda 1 ＝0.95～1.15。
6. The method for producing a high-strength titanium alloy pipe according to claim 1, wherein the heating temperature of the 3-fire forging in step 3 is T in this order 1 、T 2 、T 3 Wherein T is 1 ＜T β ，T 2 ＞T β ，T 3 ＜T β And T is 1 -T 3 ≥8℃。
7. A method for producing a high-strength titanium alloy pipe according to claim 3, wherein the total upsetting ratio E in step 3 is calculated according to formula (1), wherein n=4 to 10, δ i =1.12 to 1.33; length H of the last fire time extension 3 ＝H 2 ×λ 2 Wherein lambda is 2 Is a proportionality coefficient and lambda 2 ＝1.20～1.65。
8. A method for producing a high-strength titanium alloy pipe according to claim 3, wherein the total upsetting ratio E in step 4 is calculated according to formula (1), wherein n=2 to 5, δ i =1.25 to 1.55; the outer diameter R and the inner diameter R of the tube blank satisfy the following conditions: r=r×α, where α is a scaling factor and α=0.25 to 0.55.
9. The method for preparing a high-strength titanium alloy pipe according to claim 1, wherein the intermediate rolling in the step 5 is multi-pass cold rolling, wherein the number of rolling passes is 2-6, and the reduction rate of the outer diameter per pass is 5-15%.
10. The method for producing a high-strength titanium alloy pipe according to claim 1, wherein the heating temperature of the annealing in step 5 is 550 ℃ to 750 ℃; and (6) rolling the finished product into multi-pass cold rolling, wherein the number of rolling passes is 2-4, and the external diameter thinning rate of each pass is 3-12%.
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