CN117867308B - High-strength TA18 seamless titanium alloy and production method of large-caliber thin tube thereof - Google Patents
High-strength TA18 seamless titanium alloy and production method of large-caliber thin tube thereof Download PDFInfo
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- CN117867308B CN117867308B CN202410269196.8A CN202410269196A CN117867308B CN 117867308 B CN117867308 B CN 117867308B CN 202410269196 A CN202410269196 A CN 202410269196A CN 117867308 B CN117867308 B CN 117867308B
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 46
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 23
- 238000005096 rolling process Methods 0.000 claims abstract description 61
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims abstract description 48
- 229910052786 argon Inorganic materials 0.000 claims abstract description 24
- 238000005098 hot rolling Methods 0.000 claims abstract description 20
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 18
- 239000000956 alloy Substances 0.000 claims abstract description 18
- 238000003466 welding Methods 0.000 claims abstract description 16
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 15
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 15
- 238000000034 method Methods 0.000 claims abstract description 14
- 238000005516 engineering process Methods 0.000 claims abstract description 12
- 239000002245 particle Substances 0.000 claims abstract description 11
- 238000003723 Smelting Methods 0.000 claims abstract description 10
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 10
- 238000003825 pressing Methods 0.000 claims abstract description 9
- 235000010627 Phaseolus vulgaris Nutrition 0.000 claims abstract description 8
- 244000046052 Phaseolus vulgaris Species 0.000 claims abstract description 8
- 238000002156 mixing Methods 0.000 claims abstract description 8
- 239000000843 powder Substances 0.000 claims abstract description 8
- 238000010438 heat treatment Methods 0.000 claims description 59
- 238000004321 preservation Methods 0.000 claims description 42
- 238000005242 forging Methods 0.000 claims description 33
- 238000000137 annealing Methods 0.000 claims description 32
- 206010040844 Skin exfoliation Diseases 0.000 claims description 21
- 238000005097 cold rolling Methods 0.000 claims description 21
- 230000009467 reduction Effects 0.000 claims description 16
- 238000001816 cooling Methods 0.000 claims description 14
- 238000005496 tempering Methods 0.000 claims description 8
- 238000005520 cutting process Methods 0.000 claims description 7
- 238000005238 degreasing Methods 0.000 claims description 7
- 238000005554 pickling Methods 0.000 claims description 7
- 238000005498 polishing Methods 0.000 claims description 7
- 238000010079 rubber tapping Methods 0.000 claims description 7
- 238000005070 sampling Methods 0.000 claims description 7
- 239000010936 titanium Substances 0.000 claims description 3
- 239000000463 material Substances 0.000 abstract description 10
- 230000007547 defect Effects 0.000 abstract description 7
- 238000012545 processing Methods 0.000 abstract description 3
- 238000005204 segregation Methods 0.000 abstract description 3
- 239000013078 crystal Substances 0.000 abstract description 2
- 239000000835 fiber Substances 0.000 abstract description 2
- 238000012360 testing method Methods 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 235000017166 Bambusa arundinacea Nutrition 0.000 description 1
- 235000017491 Bambusa tulda Nutrition 0.000 description 1
- 244000082204 Phyllostachys viridis Species 0.000 description 1
- 235000015334 Phyllostachys viridis Nutrition 0.000 description 1
- 230000004075 alteration Effects 0.000 description 1
- 239000011425 bamboo Substances 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
Classifications
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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
- B21B19/00—Tube-rolling by rollers arranged outside the work and having their axes not perpendicular to the axis of the work
- B21B19/02—Tube-rolling by rollers arranged outside the work and having their axes not perpendicular to the axis of the work the axes of the rollers being arranged essentially diagonally to the axis of the work, e.g. "cross" tube-rolling ; Diescher mills, Stiefel disc piercers or Stiefel rotary piercers
- B21B19/04—Rolling basic material of solid, i.e. non-hollow, structure; Piercing, e.g. rotary piercing mills
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/04—Shaping in the rough solely by forging or pressing
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- 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
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
-
- 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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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
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- Crystallography & Structural Chemistry (AREA)
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Abstract
The invention belongs to the technical field of material processing, and particularly discloses a high-strength TA18 seamless titanium alloy and a production method of a large-caliber thin tube thereof, which comprises the following steps: uniformly mixing OA grade titanium sponge with 3-13mm particles, an alloy bag with 55% V of intermediate alloy and 45% Al, and aluminum beans with 99.90% purity, pressing into electrode blocks by a powder press, welding a plurality of electrode blocks into a bundle of bars by an argon arc welding technology, and smelting for three times by a vacuum consumable-furnace arc method to form cast ingots; the invention makes the components of the cast ingot uniform through three times of smelting, eliminates the defects of segregation, inclusion and air holes through multiple times of upsetting deformation, refines the fiber crystal grains, thereby obtaining the tissue with low defects and high strength, and can reduce the production cost and improve the production efficiency through the hot rolling process of a 850 hot rolling mill and a continuous rolling unit, thereby producing the TA18 seamless titanium alloy large-caliber thin tube with the strength and the plasticity of the finished product meeting the technical requirements.
Description
Technical Field
The invention relates to the technical field of material processing, in particular to a high-strength TA18 seamless titanium alloy and a production method of a large-caliber thin tube thereof.
Background
TA18 (Ti-3 Al-2.5V) is a near alpha and beta alloy developed at the end of the year 60 of the U.S. 20 th century, and the material is divided into two types according to the level of mechanical tensile strength, namely high-strength destressing 862MPa and medium-strength complete annealing 620 MPa; the technology of the medium strength in China is relatively mature, and the technology of the large caliber technology with high strength is not perfect; because of the characteristics of high strength, large deformation resistance, large processing forming difficulty and the like (the defects of large outer diameter, thin wall thickness, easy occurrence of polygon, bamboo joints and the like in the rolling process), the mass production of large-caliber thin-wall pipes is limited by a plurality of factors.
At present, a TA18 seamless pipe with high strength of 862MPa is obtained by a cold rolling technology, cracking phenomenon is easy to occur when the pipe is rolled, and high strength and high plasticity of a finished pipe are difficult to meet simultaneously, so that a production method of the TA18 seamless titanium alloy large-caliber thin pipe with high strength is provided.
Disclosure of Invention
The invention aims to provide a production method of a high-strength TA18 seamless titanium alloy large-caliber thin tube, which aims to solve the problems in the prior art.
In order to achieve the above purpose, the present invention provides the following technical solutions: a production method of a high-strength TA18 seamless titanium alloy large-caliber thin tube comprises the following steps:
S1, uniformly mixing OA grade titanium sponge with 3-13mm particles, an alloy bag with 55% V of intermediate alloy and 45% Al, and aluminum beans with 99.90% purity, pressing into electrode blocks by a powder press, welding a plurality of electrode blocks into a bundle of bars by an argon arc welding technology, and smelting the bars into ingots by a vacuum consumable-furnace arc method for three times;
s2, peeling, sampling, flaw detecting and cap opening cutting off on the surface of the ingot to obtain the ingot, wherein the ingot is deformed by tapping and quick clicking at the beginning until a primary coarse grain structure is broken, and the ingot is subjected to multiple upsetting to obtain a square billet;
S3, polishing the surface of the billet, then loading the billet into a stepping heating furnace for heating, wherein the temperature in the furnace is 500 ℃, the heat preservation time is 1h, then continuously heating to 800 ℃, the heat preservation time is 1.5h, then heating to 980 ℃, and the heat preservation time is 2.5h, and performing hot rolling by using a 850 hot rolling mill and a continuous rolling unit 1 to obtain a bar stock;
S4, after the bar stock is subjected to surface peeling treatment, blanking, reducing, oblique rolling and perforating, and perforating from a low-residual alpha+beta two-phase region to a beta single-phase region at a perforation temperature of 920 ℃, so that a primary alpha+beta tissue is obtained, and a TA18 titanium alloy seamless tube blank with good comprehensive performance can be obtained;
S5, cold rolling the pipe blank;
S6, obtaining the TA18 seamless finished pipe, wherein the outer diameter of the TA18 seamless finished pipe is 76mm-108mm, the wall thickness of the TA18 seamless finished pipe is 1.00mm-3.00mm, and the roughness Ra of the inner surface and the outer surface of the TA18 seamless finished pipe is not more than 1.0 mu m.
Preferably, in the step S2, the specific method for obtaining the square billet from the ingot through multiple upsetting comprises the following steps: the 1 st fire cast ingot is put into a heating furnace to be heated to 800 ℃, kept for 3 hours, then continuously heated to 1130 ℃, kept for 3.5 hours, and pier drawing is started; forging, wherein the 2 nd fire tempering temperature is 1070 ℃, the heat preservation time is 2-2.5h, and the final forging temperature is more than 900 ℃; forging 3 fires in a single-phase region, wherein the heating temperature of the single-phase region is 1070-1130 ℃, and forging 3 fires in a two-phase region, and the heating temperature is 930-950 ℃.
Preferably, in the step S5, the cold rolling treatment is performed on the tube blank as follows:
step 1, cold rolling a TA18 titanium alloy seamless tube blank by an annular ring type rolling mill;
Step 2, degreasing and pickling after rolling, annealing under the protection of vacuum argon, cooling along with furnace cooling, and straightening after annealing;
step 3, boring a single side by 0.5mm, wherein the tangible loss is 6% -7%, peeling the outer surface by 0.25mm, and the tangible loss is 2.50% -3.50%;
And step 4, adopting a multi-pass finishing mill to roll into a finished product in multiple passes, wherein two adjacent passes are required to be annealed, the annealing temperature is 580-720 ℃, and the heat preservation time is 2.5h.
Preferably, when the TA18 titanium alloy seamless tube blank is cold rolled by a ring pass rolling mill, the surface shrinkage is 49%, the Q value is 0.4, the Q value represents the ratio of the inner diameter reduction rate to the wall thickness reduction rate, and the rolling speed is 50-60 times/min after being fed for 2 mm.
Preferably, when the annealing is performed by using vacuum argon after rolling, the annealing temperature is 720 ℃, the heat preservation time is 2.5 hours, the vacuum degree is less than or equal to 15Pa, and the argon flow is 3-6mm/min.
Preferably, when the multi-pass finishing mill is adopted for multi-pass rolling to a finished product, the surface shrinkage is 43% -48%, the Q value is 0.2-0.4, the rolling speed is 50-60 times/min when the multi-pass finishing mill is used for rolling, and the rolling speed is 2 mm.
A high-strength TA18 seamless titanium alloy comprises the following components in percentage by mass: al2.92%, V2.44%, fe0.077%, si0.06%, zr0.03%, C0.014%, N0.004%, H0.0013%, O0.058%, cu0.02%, ni0.03%, mo0.03%, B0.03% and Y0.01%, the balance being Ti.
Compared with the prior art, the invention has the beneficial effects that: the invention makes the components of the cast ingot uniform through three times of smelting, eliminates the defects of segregation, inclusion and air holes through multiple times of upsetting deformation, refines the fiber crystal grains, thereby obtaining the tissue with low defects and high strength, and can reduce the production cost and improve the production efficiency through the hot rolling process of a 850 hot rolling mill and a continuous rolling unit, thereby producing the TA18 seamless titanium alloy large-caliber thin tube with the strength and the plasticity of the finished product meeting the technical requirements.
Detailed Description
Unless the context clearly indicates otherwise, nouns without quantitative word modifications and nouns modified by "the" include both singular and plural referents.
As used in the specification and claims, the terms "comprising," "including," "having," "can," "containing," and variations thereof, refer to open-ended transitional phrases, terms, or words that require the presence of a specified component/step and allow the presence of other components/steps. However, such description should be construed as also describing the composition or process as "consisting" and "consisting essentially of" the recited components/steps, which allows for the presence of only the specified components/steps and any unavoidable impurities that may result therefrom, and excludes other components/steps.
Numerical values in the specification and claims of the present application should be understood to include numerical values which, when reduced to the same number of significant figures, are identical and numerical values which differ from the stated value by less than the experimental error of conventional measurement technique of the type described in the present application to determine the stated value.
All ranges disclosed herein are inclusive of the endpoints and independently combinable (e.g., ranges of "2 grams to 10 grams" are inclusive of the endpoints, 2 grams and 10 grams, and all intermediate values).
The terms "about" and "approximately" may be used to include any numerical values that may vary without changing the basic function of the value. When used with a range, "about" and "approximately" also disclose a range defined by the absolute values of the two endpoints, e.g., "about 2 to about 4" also discloses a range of "2 to 4". In general, the terms "about" and "approximately" may refer to ± 10% of the indicated number. However, for temperature, the term "about" refers to ±1 ℃.
Unless explicitly stated otherwise, the percentages of elements should be considered as weight percentages of the alloy.
The present disclosure may relate to the temperature of certain method steps. It should be noted that these indicators generally refer to the temperature set by the heat source (e.g., furnace) and not necessarily to the temperature that the heated material must reach.
The invention provides a high-strength TA18 seamless titanium alloy, which comprises the following components in percentage by mass: al2.92%, V2.44%, fe0.077%, si0.06%, zr0.03%, C0.014%, N0.004%, H0.0013%, O0.058%, cu0.02%, ni0.03%, mo0.03%, B0.03% and Y0.01%, the balance being Ti;
A production method of a high-strength TA18 seamless titanium alloy large-caliber thin tube comprises the following steps:
S1, uniformly mixing OA grade titanium sponge with 3-13mm particles, an alloy bag with 55% V of intermediate alloy and 45% Al, and aluminum beans with purity of 99.90%, pressing into electrode blocks by using a 6300 ton powder press, welding a plurality of electrode blocks into a bundle of bar stock by using an argon arc welding technology, and smelting the bars into cast ingots by using a vacuum consumable-furnace arc method for three times;
S2, peeling, sampling, flaw detecting and cap opening cutting are carried out on the surface of the cast ingot, so that the cast ingot with the outer diameter phi 680mm is obtained, the temperature of the titanium alloy bar is from high to low from cogging to finished product temperature, particularly the two heating temperatures and the heating time before the finished product are carried out, and meanwhile, the final forging temperature is controlled; the ingot is deformed by tapping and quick clicking at the beginning until the primary coarse grain structure is broken, and the ingot is subjected to multiple upsetting to obtain square billets with phi 290mmxL more than or equal to 3500 mm; the 1 st fire cast ingot is put into a heating furnace to be heated to 800 ℃, kept for 3 hours, then continuously heated to 1130 ℃, kept for 3.5 hours, and pier drawing is started; forging, wherein the 2 nd fire tempering temperature is 1070 ℃, the heat preservation time is 2-2.5h, and the final forging temperature is more than 900 ℃; forging 3 fires in a single-phase region, wherein the heating temperature of the single-phase region is 1070-1130 ℃, and forging 3 fires in a two-phase region, and the heating temperature is 930-950 ℃;
s3, polishing the surface of the square billet with the diameter of 290mm, then loading the square billet into a stepping heating furnace for heating, wherein the temperature in the furnace is 500 ℃, the heat preservation time is 1h, then continuously heating to 800 ℃, the heat preservation time is 1.5h, then heating to 980 ℃, and the heat preservation time is 2.5h, and performing hot rolling on the square billet with the diameter of 140mm through a 850 hot rolling mill and a continuous rolling unit 1;
S4, after the bar material with the diameter of 140mm is subjected to surface peeling treatment, blanking, reducing, oblique rolling and perforating, and perforating from a low-residual alpha+beta two-phase region to a beta single-phase region at the perforation temperature of 920 ℃, so that a primary alpha+beta tissue is obtained, and a phi 135mmTA titanium alloy seamless tube blank with good comprehensive performance can be obtained;
S5, performing cold rolling treatment on the pipe blank, wherein the specific steps are as follows:
step 1, cold rolling a phi 135 multiplied by 12.00mm titanium alloy seamless tube blank to phi 108.00 multiplied by 7.00mm by an annular ring type LG120 rolling mill, wherein the surface shrinkage is 49%, the Q value is 0.4, the Q value represents the ratio of the inner diameter reduction rate to the wall thickness reduction rate, and the rolling speed is 50-60 times/min when the tube blank is rolled;
step 2, degreasing and pickling after rolling, annealing under the protection of vacuum argon, wherein the annealing temperature is 720 ℃, the heat preservation time is 2.5h, the vacuum degree is less than or equal to 15Pa, the argon flow is 3-6mm/min, cooling along with furnace cooling, and straightening after annealing;
step 3, boring a single side by 0.5mm, wherein the tangible loss is 6% -7%, peeling the outer surface by 0.25mm, and the tangible loss is 2.50% -3.50%;
Step 4, adopting a multi-pass finishing mill LD80 to roll to a finished product in multiple passes, wherein the surface shrinkage is 43% -48%, the Q value is 0.2-0.4, the rolling speed is 50-60 times/min, the adjacent two passes are required to be annealed, the annealing temperature is 580-720 ℃, and the heat preservation time is 2.5h;
During straightening treatment, the deformation of the pipe with the straightening rolling reduction and the reverse bending amount can generate surface residual stress and tensile stress, the yield and the plasticity of the pipe can be reduced, and the stress relief annealing is added after the straightening to eliminate the residual stress and the tensile stress.
During cold rolling, GCr15 is selected as a material of the cold rolling tool and die, and the Rockwell hardness HRC60 of the surface of the cold rolling tool and die after quenching and tempering is not more than Ra0.5 mu m.
The original slideway reducing section of the cold rolling die is adjusted to 12mm.
S6, obtaining the TA18 seamless finished pipe, wherein the outer diameter of the TA18 seamless finished pipe is 76mm-108mm, the wall thickness of the TA18 seamless finished pipe is 1.00mm-3.00mm, and the roughness Ra of the inner surface and the outer surface of the TA18 seamless finished pipe is not more than 1.0 mu m.
In the step S1, the uniform small-particle titanium sponge is used for enabling the components of the cast ingot to be uniform through a three-time vacuum consumable furnace, so that the control of the mechanical properties of the finished product is facilitated.
In the step S2, the titanium alloy cast ingot is firstly subjected to pier pressing deformation in a beta phase region, then is subjected to drawing deformation in an (alpha+beta) two-phase region, defects such as segregation, inclusion, air holes and the like are eliminated through pier drawing deformation, fiberized grains are thinned, a tissue with low defects and high strength is obtained, and the mechanical property of a finished product is effectively ensured.
In the step S3, the square billet is subjected to hot rolling treatment through the cooperation of the 850 hot rolling mill and the continuous rolling unit, and the method has the advantages of high production efficiency and low cost.
In the step S4, the TA18 phase transition point temperature is 940-950 ℃ measured by a metallographic method before perforation is carried out from the low-residual alpha+beta two-phase region to the beta single-phase region.
Example 1
A production method of a high-strength TA18 seamless titanium alloy large-caliber thin tube comprises the following steps:
s1, uniformly mixing an OA grade titanium sponge with 3mm particles, an alloy bag with 55% V of intermediate alloy and 45% Al, and aluminum beans with 99.90% purity, pressing into electrode blocks by using a 6300 ton powder press, welding a plurality of electrode blocks into a bundle of bars by using an argon arc welding technology, and smelting the bars into ingots by using a vacuum consumable-furnace arc method for three times;
S2, peeling, sampling, flaw detecting and cap opening cutting are carried out on the surface of the cast ingot, so that the cast ingot with the outer diameter phi 680mm is obtained, the temperature of the titanium alloy bar is from high to low from cogging to finished product temperature, particularly the two heating temperatures and the heating time before the finished product are carried out, and meanwhile, the final forging temperature is controlled; the ingot is deformed by tapping and quick clicking at the beginning until the primary coarse grain structure is broken, and the ingot is subjected to multiple upsetting to obtain square billets with phi 290mmxL more than or equal to 3500 mm; the 1 st fire cast ingot is put into a heating furnace to be heated to 800 ℃, kept for 3 hours, then continuously heated to 1130 ℃, kept for 3.5 hours, and pier drawing is started; forging, wherein the 2 nd fire tempering temperature is 1070 ℃, the heat preservation time is 2-2.5h, and the final forging temperature is more than 900 ℃; forging 3 fires in a single-phase region, wherein the heating temperature of the single-phase region is 1070-1130 ℃, and forging 3 fires in a two-phase region, and the heating temperature is 930-950 ℃;
s3, polishing the surface of the square billet with the diameter of 290mm, then loading the square billet into a stepping heating furnace for heating, wherein the temperature in the furnace is 500 ℃, the heat preservation time is 1h, then continuously heating to 800 ℃, the heat preservation time is 1.5h, then heating to 980 ℃, and the heat preservation time is 2.5h, and performing hot rolling on the square billet with the diameter of 140mm through a 850 hot rolling mill and a continuous rolling unit 1;
S4, after the bar material with the diameter of 140mm is subjected to surface peeling treatment, blanking, reducing, oblique rolling and perforating, and perforating from a low-residual alpha+beta two-phase region to a beta single-phase region at the perforation temperature of 920 ℃, so that a primary alpha+beta tissue is obtained, and a phi 135mmTA titanium alloy seamless tube blank with good comprehensive performance can be obtained;
S5, performing cold rolling treatment on the pipe blank, wherein the specific steps are as follows:
Step 1, cold rolling a phi 135 multiplied by 12.00mm titanium alloy seamless tube blank to phi 108.00 multiplied by 7.00mm by an annular ring type LG120 rolling mill, wherein the surface shrinkage is 49%, the Q value is 0.4, the Q value represents the ratio of the inner diameter reduction rate to the wall thickness reduction rate, and the rolling speed is 60 times/min at the time of rolling, wherein the feeding is 2 mm;
Step 2, degreasing and pickling after rolling, annealing under the protection of vacuum argon, wherein the annealing temperature is 720 ℃, the heat preservation time is 2.5h, the vacuum degree is less than or equal to 15Pa, the argon flow is 6mm/min, cooling along with furnace cooling, and straightening after annealing;
step 3, boring a single side by 0.5mm, wherein the tangible loss is 6%, peeling the outer surface by 0.25mm, and the tangible loss is 2.50%;
step 4, adopting a multi-pass finishing mill LD80 to roll to a finished product in multiple passes, wherein the surface shrinkage is 45%, the Q value is 0.3, the rolling speed is 60 times/min, the adjacent two passes are required to be annealed, the annealing temperature is 580-720 ℃, and the heat preservation time is 2.5h;
s6, obtaining the TA18 seamless finished pipe, wherein the outer diameter of the TA18 seamless finished pipe is 76.05mm, the wall thickness of the TA18 seamless finished pipe is 1.02mm, and the roughness Ra of the inner surface and the outer surface of the TA18 seamless finished pipe is not more than 1.0 mu m.
Example 2
A production method of a high-strength TA18 seamless titanium alloy large-caliber thin tube comprises the following steps:
S1, uniformly mixing OA grade titanium sponge with 6mm particles, an alloy bag with 55% V of intermediate alloy and 45% Al, and aluminum beans with 99.90% purity, pressing into electrode blocks by using a 6300 ton powder press, welding a plurality of electrode blocks into a bundle of bar stock by using an argon arc welding technology, and smelting the bars into cast ingots by using a vacuum consumable-furnace arc method for three times;
S2, peeling, sampling, flaw detecting and cap opening cutting are carried out on the surface of the cast ingot, so that the cast ingot with the outer diameter phi 680mm is obtained, the temperature of the titanium alloy bar is from high to low from cogging to finished product temperature, particularly the two heating temperatures and the heating time before the finished product are carried out, and meanwhile, the final forging temperature is controlled; the ingot is deformed by tapping and quick clicking at the beginning until the primary coarse grain structure is broken, and the ingot is subjected to multiple upsetting to obtain square billets with phi 290mmxL more than or equal to 3500 mm; the 1 st fire cast ingot is put into a heating furnace to be heated to 800 ℃, kept for 3 hours, then continuously heated to 1130 ℃, kept for 3.5 hours, and pier drawing is started; forging, wherein the 2 nd fire tempering temperature is 1070 ℃, the heat preservation time is 2-2.5h, and the final forging temperature is more than 900 ℃; forging 3 fires in a single-phase region, wherein the heating temperature of the single-phase region is 1070-1130 ℃, and forging 3 fires in a two-phase region, and the heating temperature is 930-950 ℃;
s3, polishing the surface of the square billet with the diameter of 290mm, then loading the square billet into a stepping heating furnace for heating, wherein the temperature in the furnace is 500 ℃, the heat preservation time is 1h, then continuously heating to 800 ℃, the heat preservation time is 1.5h, then heating to 980 ℃, and the heat preservation time is 2.5h, and performing hot rolling on the square billet with the diameter of 140mm through a 850 hot rolling mill and a continuous rolling unit 1;
S4, after the bar material with the diameter of 140mm is subjected to surface peeling treatment, blanking, reducing, oblique rolling and perforating, and perforating from a low-residual alpha+beta two-phase region to a beta single-phase region at the perforation temperature of 920 ℃, so that a primary alpha+beta tissue is obtained, and a phi 135mmTA titanium alloy seamless tube blank with good comprehensive performance can be obtained;
S5, performing cold rolling treatment on the pipe blank, wherein the specific steps are as follows:
Step 1, cold rolling a phi 135 multiplied by 12.00mm titanium alloy seamless tube blank to phi 108.00 multiplied by 7.00mm by an annular ring type LG120 rolling mill, wherein the surface shrinkage is 49%, the Q value is 0.4, the Q value represents the ratio of the inner diameter reduction rate to the wall thickness reduction rate, and the rolling speed is 60 times/min at the time of rolling, wherein the feeding is 2 mm;
Step 2, degreasing and pickling after rolling, annealing under the protection of vacuum argon, wherein the annealing temperature is 720 ℃, the heat preservation time is 2.5h, the vacuum degree is less than or equal to 15Pa, the argon flow is 6mm/min, cooling along with furnace cooling, and straightening after annealing;
step 3, boring a single side by 0.5mm, wherein the tangible loss is 6%, peeling the outer surface by 0.25mm, and the tangible loss is 2.50%;
step 4, adopting a multi-pass finishing mill LD80 to roll to a finished product in multiple passes, wherein the surface shrinkage is 45%, the Q value is 0.3, the rolling speed is 60 times/min, the adjacent two passes are required to be annealed, the annealing temperature is 580-720 ℃, and the heat preservation time is 2.5h;
S6, obtaining the TA18 seamless finished pipe, wherein the outer diameter of the TA18 seamless finished pipe is 92.03mm, the wall thickness of the TA18 seamless finished pipe is 1.27mm, and the roughness Ra of the inner surface and the outer surface of the TA18 seamless finished pipe is not more than 1.0 mu m.
Example 3
A production method of a high-strength TA18 seamless titanium alloy large-caliber thin tube comprises the following steps:
s1, uniformly mixing OA grade titanium sponge with 10mm particles, an alloy bag with 55% of V and 45% of Al serving as an intermediate alloy and aluminum beans with 99.90% of purity, pressing into electrode blocks by using a 6300 ton powder press, welding a plurality of electrode blocks into a bundle of bars by using an argon arc welding technology, and smelting the bars into ingots by using a vacuum consumable-furnace arc method for three times;
S2, peeling, sampling, flaw detecting and cap opening cutting are carried out on the surface of the cast ingot, so that the cast ingot with the outer diameter phi 680mm is obtained, the temperature of the titanium alloy bar is from high to low from cogging to finished product temperature, particularly the two heating temperatures and the heating time before the finished product are carried out, and meanwhile, the final forging temperature is controlled; the ingot is deformed by tapping and quick clicking at the beginning until the primary coarse grain structure is broken, and the ingot is subjected to multiple upsetting to obtain square billets with phi 290mmxL more than or equal to 3500 mm; the 1 st fire cast ingot is put into a heating furnace to be heated to 800 ℃, kept for 3 hours, then continuously heated to 1130 ℃, kept for 3.5 hours, and pier drawing is started; forging, wherein the 2 nd fire tempering temperature is 1070 ℃, the heat preservation time is 2-2.5h, and the final forging temperature is more than 900 ℃; forging 3 fires in a single-phase region, wherein the heating temperature of the single-phase region is 1070-1130 ℃, and forging 3 fires in a two-phase region, and the heating temperature is 930-950 ℃;
s3, polishing the surface of the square billet with the diameter of 290mm, then loading the square billet into a stepping heating furnace for heating, wherein the temperature in the furnace is 500 ℃, the heat preservation time is 1h, then continuously heating to 800 ℃, the heat preservation time is 1.5h, then heating to 980 ℃, and the heat preservation time is 2.5h, and performing hot rolling on the square billet with the diameter of 140mm through a 850 hot rolling mill and a continuous rolling unit 1;
S4, after the bar material with the diameter of 140mm is subjected to surface peeling treatment, blanking, reducing, oblique rolling and perforating, and perforating from a low-residual alpha+beta two-phase region to a beta single-phase region at the perforation temperature of 920 ℃, so that a primary alpha+beta tissue is obtained, and a phi 135mmTA titanium alloy seamless tube blank with good comprehensive performance can be obtained;
S5, performing cold rolling treatment on the pipe blank, wherein the specific steps are as follows:
Step 1, cold rolling a phi 135 multiplied by 12.00mm titanium alloy seamless tube blank to phi 108.00 multiplied by 7.00mm by an annular ring type LG120 rolling mill, wherein the surface shrinkage is 49%, the Q value is 0.4, the Q value represents the ratio of the inner diameter reduction rate to the wall thickness reduction rate, and the rolling speed is 60 times/min at the time of rolling, wherein the feeding is 2 mm;
Step 2, degreasing and pickling after rolling, annealing under the protection of vacuum argon, wherein the annealing temperature is 720 ℃, the heat preservation time is 2.5h, the vacuum degree is less than or equal to 15Pa, the argon flow is 6mm/min, cooling along with furnace cooling, and straightening after annealing;
step 3, boring a single side by 0.5mm, wherein the tangible loss is 6%, peeling the outer surface by 0.25mm, and the tangible loss is 2.50%;
step 4, adopting a multi-pass finishing mill LD80 to roll to a finished product in multiple passes, wherein the surface shrinkage is 45%, the Q value is 0.3, the rolling speed is 60 times/min, the adjacent two passes are required to be annealed, the annealing temperature is 580-720 ℃, and the heat preservation time is 2.5h;
S6, obtaining the TA18 seamless finished pipe, wherein the outer diameter of the TA18 seamless finished pipe is 102.31mm, the wall thickness of the TA18 seamless finished pipe is 2.24mm, and the roughness Ra of the inner surface and the outer surface of the TA18 seamless finished pipe is not more than 1.0 mu m.
Example 4
A production method of a high-strength TA18 seamless titanium alloy large-caliber thin tube comprises the following steps:
S1, uniformly mixing an OA grade titanium sponge with 13mm particles, an alloy bag with 55% V of intermediate alloy and 45% Al, and aluminum beans with 99.90% purity, pressing into electrode blocks by using a 6300 ton powder press, welding a plurality of electrode blocks into a bundle of bars by using an argon arc welding technology, and smelting the bars into ingots by using a vacuum consumable-furnace arc method for three times;
S2, peeling, sampling, flaw detecting and cap opening cutting are carried out on the surface of the cast ingot, so that the cast ingot with the outer diameter phi 680mm is obtained, the temperature of the titanium alloy bar is from high to low from cogging to finished product temperature, particularly the two heating temperatures and the heating time before the finished product are carried out, and meanwhile, the final forging temperature is controlled; the ingot is deformed by tapping and quick clicking at the beginning until the primary coarse grain structure is broken, and the ingot is subjected to multiple upsetting to obtain square billets with phi 290mmxL more than or equal to 3500 mm; the 1 st fire cast ingot is put into a heating furnace to be heated to 800 ℃, kept for 3 hours, then continuously heated to 1130 ℃, kept for 3.5 hours, and pier drawing is started; forging, wherein the 2 nd fire tempering temperature is 1070 ℃, the heat preservation time is 2-2.5h, and the final forging temperature is more than 900 ℃; forging 3 fires in a single-phase region, wherein the heating temperature of the single-phase region is 1070-1130 ℃, and forging 3 fires in a two-phase region, and the heating temperature is 930-950 ℃;
s3, polishing the surface of the square billet with the diameter of 290mm, then loading the square billet into a stepping heating furnace for heating, wherein the temperature in the furnace is 500 ℃, the heat preservation time is 1h, then continuously heating to 800 ℃, the heat preservation time is 1.5h, then heating to 980 ℃, and the heat preservation time is 2.5h, and performing hot rolling on the square billet with the diameter of 140mm through a 850 hot rolling mill and a continuous rolling unit 1;
S4, after the bar material with the diameter of 140mm is subjected to surface peeling treatment, blanking, reducing, oblique rolling and perforating, and perforating from a low-residual alpha+beta two-phase region to a beta single-phase region at the perforation temperature of 920 ℃, so that a primary alpha+beta tissue is obtained, and a phi 135mmTA titanium alloy seamless tube blank with good comprehensive performance can be obtained;
S5, performing cold rolling treatment on the pipe blank, wherein the specific steps are as follows:
Step 1, cold rolling a phi 135 multiplied by 12.00mm titanium alloy seamless tube blank to phi 108.00 multiplied by 7.00mm by an annular ring type LG120 rolling mill, wherein the surface shrinkage is 49%, the Q value is 0.4, the Q value represents the ratio of the inner diameter reduction rate to the wall thickness reduction rate, and the rolling speed is 60 times/min at the time of rolling, wherein the feeding is 2 mm;
Step 2, degreasing and pickling after rolling, annealing under the protection of vacuum argon, wherein the annealing temperature is 720 ℃, the heat preservation time is 2.5h, the vacuum degree is less than or equal to 15Pa, the argon flow is 6mm/min, cooling along with furnace cooling, and straightening after annealing;
step 3, boring a single side by 0.5mm, wherein the tangible loss is 6%, peeling the outer surface by 0.25mm, and the tangible loss is 2.50%;
step 4, adopting a multi-pass finishing mill LD80 to roll to a finished product in multiple passes, wherein the surface shrinkage is 45%, the Q value is 0.3, the rolling speed is 60 times/min, the adjacent two passes are required to be annealed, the annealing temperature is 580-720 ℃, and the heat preservation time is 2.5h;
S6, obtaining the TA18 seamless finished pipe, wherein the outer diameter of the TA18 seamless finished pipe is 108.00mm, the wall thickness of the TA18 seamless finished pipe is 2.50mm, and the roughness Ra of the inner surface and the outer surface of the TA18 seamless finished pipe is not more than 1.0 mu m.
Examples 1 to 4 were tested in a tensile test according to the GB/T228.1-2010 standard in a room temperature environment, the test results of which are shown in the following table:
From the results of the above table, it can be seen that the tensile strength, the prescribed non-proportional elongation strength and the elongation a 50 of examples 1 to 4 all meet the technical requirements, and that the tensile strength, the prescribed non-proportional elongation strength and the elongation a 50 are all reduced with the reduction of the particle size of the OA grade titanium sponge particles.
In the room temperature environment, metal tube flattening tests were performed on examples 1 to 4 according to GB/T246-2007, and metal tube flaring tests were performed on examples 1 to 4 according to GB/T242-2007, with the following test results:
From the results of the above table, it can be seen that the flattening and flaring inner diameter expansion rates of examples 1-4 meet the technical requirements.
Although embodiments of the present invention have been shown and described, it will be understood by those skilled in the art that various changes, modifications, substitutions and alterations can be made therein without departing from the principles and spirit of the invention, the scope of which is defined in the appended claims and their equivalents.
Claims (6)
1. The production method of the high-strength TA18 seamless titanium alloy large-caliber thin tube is characterized by comprising the following steps of:
S1, uniformly mixing OA grade titanium sponge with 3-13mm particles, an alloy bag with 55% V of intermediate alloy and 45% Al, and aluminum beans with 99.90% purity, pressing into electrode blocks by a powder press, welding a plurality of electrode blocks into a bundle of bars by an argon arc welding technology, and smelting the bars into ingots by a vacuum consumable-furnace arc method for three times;
s2, peeling, sampling, flaw detecting and cap opening cutting off on the surface of the ingot to obtain the ingot, wherein the ingot is deformed by tapping and quick clicking at the beginning until a primary coarse grain structure is broken, and the ingot is subjected to multiple upsetting to obtain a square billet;
S3, polishing the surface of the billet, then loading the billet into a stepping heating furnace for heating, wherein the temperature in the furnace is 500 ℃, the heat preservation time is 1h, then continuously heating to 800 ℃, the heat preservation time is 1.5h, then heating to 980 ℃, and the heat preservation time is 2.5h, and performing hot rolling by using a 850 hot rolling mill and a continuous rolling unit 1 to obtain a bar stock;
S4, after the bar stock is subjected to surface peeling treatment, blanking, reducing, oblique rolling and perforating, wherein the perforating temperature is 920 ℃, so that a primary alpha+beta structure is obtained, and a TA18 titanium alloy seamless tube blank with good comprehensive performance can be obtained;
S5, cold rolling the pipe blank;
S6, obtaining the TA18 seamless finished pipe, wherein the outer diameter of the TA18 seamless finished pipe is 76mm-108mm, the wall thickness is 1.00mm-3.00mm, the roughness Ra of the inner surface and the outer surface is not more than 1.0 mu m,
In the step S2, the concrete method for obtaining square billets through multiple upsetting and pulling of the cast ingot comprises the following steps: the 1 st fire cast ingot is put into a heating furnace to be heated to 800 ℃, kept for 3 hours, then continuously heated to 1130 ℃, kept for 3.5 hours, and pier drawing is started; forging, wherein the 2 nd fire tempering temperature is 1070 ℃, the heat preservation time is 2-2.5h, and the final forging temperature is more than 900 ℃; then forging 3 fires in a single-phase region, wherein the heating temperature of the single-phase region is 1070-1130 ℃, and forging 3 fires in a two-phase region, and the heating temperature is 930-950 ℃;
In the step S5, the cold rolling treatment of the pipe blank specifically includes the following steps:
step 1, cold rolling a TA18 titanium alloy seamless tube blank by an annular ring type rolling mill;
Step 2, degreasing and pickling after rolling, annealing under the protection of vacuum argon, cooling along with furnace cooling, and straightening after annealing;
step 3, boring a single side by 0.5mm, wherein the tangible loss is 6% -7%, peeling the outer surface by 0.25mm, and the tangible loss is 2.50% -3.50%;
And step 4, adopting a multi-pass finishing mill to roll into a finished product in multiple passes, wherein two adjacent passes are required to be annealed, the annealing temperature is 580-720 ℃, and the heat preservation time is 2.5h.
2. The method for producing the high-strength TA18 seamless titanium alloy large-caliber thin tube according to claim 1, which is characterized in that: when the TA18 titanium alloy seamless tube blank is cold rolled by a ring pass rolling mill, the surface shrinkage is 49%, the Q value is 0.4, the Q value represents the ratio of the inner diameter reduction rate to the wall thickness reduction rate, and the rolling speed is 50-60 times/min after being fed by 2mm during rolling.
3. The method for producing the high-strength TA18 seamless titanium alloy large-caliber thin tube according to claim 1, which is characterized in that: in the step 2, when annealing is carried out by using vacuum argon after rolling, the annealing temperature is 720 ℃, the heat preservation time is 2.5h, the vacuum degree is less than or equal to 15Pa, and the argon flow is 3-6mm/min.
4. The method for producing the high-strength TA18 seamless titanium alloy large-caliber thin tube according to claim 1, which is characterized in that: in the step 4, when a multi-pass finishing mill is adopted for multi-pass rolling to obtain a finished product, the surface shrinkage is 43% -48%, the Q value is 0.2-0.4, the finished product is fed for 2mm during rolling, and the rolling speed is 50-60 times/min.
5. The high-strength TA18 seamless titanium alloy large-caliber thin tube is characterized by comprising the following steps of: the high-strength TA18 seamless titanium alloy large-caliber thin pipe is prepared by the production method of the high-strength TA18 seamless titanium alloy large-caliber thin pipe in any one of claims 1-4.
6. The high-strength TA18 seamless titanium alloy heavy caliber thin tube according to claim 5, wherein the tube comprises the following components in percentage by mass: al2.92%, V2.44%, fe0.077%, si0.06%, zr0.03%, C0.014%, N0.004%, H0.0013%, O0.058%, cu0.02%, ni0.03%, mo0.03%, B0.03% and Y0.01%, the balance being Ti.
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