CN117385304A - Low anisotropic powder Ti 2 AlNb alloy fine-grain thin plate and preparation method and application thereof - Google Patents
Low anisotropic powder Ti 2 AlNb alloy fine-grain thin plate and preparation method and application thereof Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 97
- 239000000956 alloy Substances 0.000 title claims abstract description 97
- 239000000843 powder Substances 0.000 title claims abstract description 54
- 238000002360 preparation method Methods 0.000 title claims abstract description 25
- 238000005096 rolling process Methods 0.000 claims abstract description 103
- 238000000034 method Methods 0.000 claims abstract description 18
- 238000005253 cladding Methods 0.000 claims abstract description 12
- 238000004321 preservation Methods 0.000 claims description 36
- 238000005098 hot rolling Methods 0.000 claims description 25
- 238000010304 firing Methods 0.000 claims description 21
- 238000001513 hot isostatic pressing Methods 0.000 claims description 17
- 239000002245 particle Substances 0.000 claims description 10
- 238000004519 manufacturing process Methods 0.000 claims description 6
- 230000008569 process Effects 0.000 claims description 5
- 238000012545 processing Methods 0.000 abstract description 5
- 230000009467 reduction Effects 0.000 description 35
- 238000005498 polishing Methods 0.000 description 14
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 8
- 238000000137 annealing Methods 0.000 description 8
- 238000007599 discharging Methods 0.000 description 8
- 238000011049 filling Methods 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 7
- 238000003466 welding Methods 0.000 description 7
- 229910000831 Steel Inorganic materials 0.000 description 6
- 239000010959 steel Substances 0.000 description 6
- 238000012546 transfer Methods 0.000 description 6
- 238000009849 vacuum degassing Methods 0.000 description 6
- 238000001816 cooling Methods 0.000 description 5
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- 238000012360 testing method Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
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- 229910017604 nitric acid Inorganic materials 0.000 description 2
- RNFJDJUURJAICM-UHFFFAOYSA-N 2,2,4,4,6,6-hexaphenoxy-1,3,5-triaza-2$l^{5},4$l^{5},6$l^{5}-triphosphacyclohexa-1,3,5-triene Chemical compound N=1P(OC=2C=CC=CC=2)(OC=2C=CC=CC=2)=NP(OC=2C=CC=CC=2)(OC=2C=CC=CC=2)=NP=1(OC=1C=CC=CC=1)OC1=CC=CC=C1 RNFJDJUURJAICM-UHFFFAOYSA-N 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
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- 238000009792 diffusion process Methods 0.000 description 1
- 239000003063 flame retardant Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
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- 238000009689 gas atomisation Methods 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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Abstract
The invention relates to the technical field of alloy processing, in particular to low-anisotropy powder Ti 2 An AlNb alloy fine-grain thin plate, a preparation method and application thereof. The method comprises the following steps: (a) Performing first fire rolling along the width direction of the alloy slab, and then performing second fire rolling along the length direction of the alloy slab to obtain a slab A; (b) Rolling the slab A along the width direction at least twice to obtain a slab B; (c) Performing primary fire rolling on the slab B along the length direction, and performing cladding rolling along the length direction; the absolute value of the difference between the deformation ratio in step (b) and the deformation ratio in step (c) is 20% or less. The invention carries out reversing rolling for a plurality of times on the plate blank to lead the transverse and longitudinal deformation to be basically equivalent, and obtains Ti with lower anisotropism by matching with other technological parameters 2 An AlNb alloy fine-grain sheet.
Description
Technical Field
The invention relates to the technical field of alloy processing, in particular to low-anisotropy powder Ti 2 An AlNb alloy fine-grain thin plate, a preparation method and application thereof.
Background
Ti 2 The AlNb alloy has the advantages of low density, small thermal expansion coefficient, good flame retardant property, high specific strength, high fracture toughness, good high-temperature creep resistance and the like, is a structural material which can be used for a long time at 600-750 ℃ or applied at a higher temperature in a short time, particularly has great application potential in the aspect of aerospace structural materials, and has important significance in the aspects of improving thrust ratio of aircrafts, improving fuel efficiency, high-temperature service performance and the like.
Adopts Ti 2 The thin-wall complex member for aerospace formed by the AlNb alloy sheet bears the severe aerodynamic heat and aerodynamic force coupling action in the high-speed flight process, and the member bears the force/heat coupling action in more than one direction when in service in the environment, and often bears the severe force/heat coupling action in multiple directions, so that the material is required to have good high-temperature strength, lower anisotropy, and uniformity and consistency of tissues and performances are required to be ensured as much as possible. Ti prepared by conventional process 2 The AlNb alloy thin plate has larger anisotropism, is easy to generate irregular warpage of a formed part in the processing and forming process, and is difficult to meet the requirement of dimensional accuracy.
In view of this, the present invention has been made.
Disclosure of Invention
It is an object of the present invention to provide a low anisotropic powder Ti 2 Preparation method of AlNb alloy fine-grain thin plate for solving the problem of Ti in the prior art 2 The AlNb alloy thin plate has a technical problem of large anisotropy.
Another of the inventionAims at providing low anisotropic powder Ti 2 An AlNb alloy fine-grain sheet.
It is a further object of the present invention to provide a low anisotropic powder Ti 2 The application of the AlNb alloy fine-grain thin plate in preparing the aerospace thin-wall complex structural member.
In order to achieve the above object of the present invention, the following technical solutions are specifically adopted:
low anisotropic powder Ti 2 The preparation method of the AlNb alloy fine-grain thin plate comprises the following steps:
(a) Along Ti 2 First hot rolling is carried out on the AlNb alloy plate blank in the width direction, and then the plate blank is rolled along the Ti 2 Performing second hot rolling on the AlNb alloy plate blank in the length direction to obtain a plate blank A;
(b) Rolling the slab A along the width direction for at least two times to obtain a slab B;
(c) Performing primary fire rolling on the slab B along the length direction, and performing cladding rolling along the length direction;
the absolute value of the difference between the deformation ratio in the width direction in step (b) and the deformation ratio in the length direction in step (c) is not more than 20%.
In a specific embodiment of the present invention, the temperature of the rolling is 900 to 1080 ℃.
In a specific embodiment of the present invention, in the step (a), the deformation ratio of the first hot rolling in the width direction is 10% to 40%, and the deformation ratio of the second hot rolling in the length direction is 10% to 40%.
In a specific embodiment of the present invention, in each of the hot rolling in the step (a) and the step (b), the rolling pass of one hot is 2 to 6 times.
In a specific embodiment of the present invention, in step (b), the total deformation ratio in the width direction is 50% to 90%; in the step (c), the total deformation rate along the length direction is 50-90%.
In a specific embodiment of the present invention, in step (b), the deformation rate of each firing in the width direction is independently 15% to 60%, preferably 20% to 45%.
In a specific embodiment of the present invention, in the step (c), the deformation rate in the length direction in the first hot rolling is 10% to 50%, preferably 35% to 45%; the deformation rate of the cladding rolling is 15-80%, preferably 40-70%.
In a specific embodiment of the present invention, the Ti 2 The preparation of the AlNb alloy plate blank comprises the following steps: adopts Ti 2 Preparation of Ti from AlNb prealloyed powder by hot isostatic pressing 2 An AlNb alloy slab;
the conditions of the hot isostatic pressing include: the temperature is 980-1200 ℃, the pressure is more than or equal to 100MPa, and the heat preservation time is more than or equal to 1h.
In a specific embodiment of the invention, the prealloyed powder has a particle size of 250 μm or less, such as 50 to 150 μm.
The invention also provides a low anisotropic powder Ti using any one of the above 2 Low anisotropic powder Ti prepared by preparation method of AlNb alloy fine-grain thin plate 2 An AlNb alloy fine-grain sheet.
In a specific embodiment of the present invention, the low anisotropy powder Ti 2 In the AlNb alloy fine-grain thin plate, the structure is a fine equiaxed structure, the size of O phase particles is less than 5 mu m, the aspect ratio of the O phase particles is less than 3: 1,O, the crystallographic orientation of the B2 phase is not preferentially distributed, and the B2 phase has {111} < 110 > texture.
The invention also provides the low anisotropic powder Ti 2 The application of the AlNb alloy fine-grain thin plate in preparing the aerospace thin-wall complex structural member.
Compared with the prior art, the invention has the beneficial effects that:
(1) The invention carries out reversing rolling for a plurality of times on the plate blank to lead the transverse and longitudinal deformation to be basically equivalent, and obtains Ti with lower anisotropism by matching with other technological parameters 2 An AlNb alloy fine-grain thin plate;
(2) The low anisotropic powder Ti prepared by the invention 2 The AlNb alloy fine-grain thin plate has good consistency of structure and performance in different directions, good room temperature strength and plasticity, relatively low high temperature strength and excellent high temperaturePlasticity is favorable to Ti 2 The AlNb alloy fine-grain thin plate hot forming member lays a good foundation for the subsequent preparation of the aerospace thin-wall complex structural member.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings that are needed in the description of the embodiments or the prior art will be briefly described, and it is obvious that the drawings in the description below are some embodiments of the present invention, and other drawings can be obtained according to the drawings without inventive effort for a person skilled in the art.
FIG. 1 shows Ti as prepared in example 1 of the present invention 2 Longitudinal microstructure of the AlNb alloy fine-grain thin plate;
FIG. 2 shows Ti as prepared in example 1 of the present invention 2 A transverse microstructure of the AlNb alloy fine-grain thin plate;
FIG. 3 shows Ti as prepared in example 1 of the present invention 2 Orientation distribution diagram of O phase of AlNb alloy fine-grain thin plate on rolled surface;
FIG. 4 shows Ti as prepared in example 1 of the present invention 2 Distribution of beta/B2 phase orientation of the AlNb alloy fine grain sheet on the rolled surface.
Detailed Description
The technical solution of the present invention will be clearly and completely described below with reference to the accompanying drawings and detailed description, but it will be understood by those skilled in the art that the examples described below are some, but not all, examples of the present invention, and are intended to be illustrative of the present invention only and should not be construed as limiting the scope of the present invention. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention. The specific conditions are not noted in the examples and are carried out according to conventional conditions or conditions recommended by the manufacturer. The reagents or apparatus used were conventional products commercially available without the manufacturer's attention.
Low anisotropic powder Ti 2 Preparation of AlNb alloy fine-grain thin plateThe method comprises the following steps:
(a) Along Ti 2 First hot rolling is carried out on the AlNb alloy plate blank in the width direction, and then the plate blank is rolled along the Ti 2 Performing second hot rolling on the AlNb alloy plate blank in the length direction to obtain a plate blank A;
(b) Rolling the slab A along the width direction for at least two times to obtain a slab B;
(c) Performing primary fire rolling on the slab B along the length direction, and performing cladding rolling along the length direction;
the absolute value of the difference between the deformation ratio in the width direction in step (b) and the deformation ratio in the length direction in step (c) is not more than 20%.
The invention carries out reversing rolling for a plurality of times on the plate blank to lead the transverse and longitudinal deformation to be basically equivalent, and obtains Ti with lower anisotropism by matching with other technological parameters 2 An AlNb alloy fine-grain sheet.
As in the different embodiments, the absolute value of the difference between the amount of deformation in the width direction in step (b) and the amount of deformation in the length direction in step (c) may be 10% or less, 8% or less, 6% or less, 4% or less, 2% or less, 1% or less, or a range consisting of any two of the upper limit values thereof.
The transverse and longitudinal deformation amounts are basically equivalent by regulating and controlling the deformation amount range. In the present invention, "width direction" and "length direction" are respectively the initial Ti 2 The width direction Y direction and the length direction X direction corresponding to the AlNb alloy plate blank are mutually perpendicular and respectively correspond to the initial Ti 2 The thickness direction Z of the AlNb alloy plate blank is vertical.
In addition, the deformation amount mentioned in the invention is calculated by the following modes:
(dimension in the thickness direction before deformation-dimension in the thickness direction after deformation)/dimension in the thickness direction before deformation.
In a specific embodiment of the present invention, the temperature of the rolling is 900 to 1080 ℃.
As in the various embodiments, the temperature of the rolling may be 900 ℃, 920 ℃, 940 ℃, 960 ℃, 980 ℃, 1000 ℃, 1020 ℃, 1040 ℃, 1060 ℃, 1080 ℃, or a range of any two of these.
The high rolling temperature is adopted when the thickness of the plate is larger than 20+/-5 mm, which is favorable for recovery recrystallization and further reduces the anisotropy of the plate. When the thickness of the plate is less than or equal to 20+/-5 mm, a relatively low rolling temperature is adopted, and corresponding rolling operation is matched, so that finer grain size is obtained. That is, in a specific embodiment of the present invention, in the rolling, when the slab thickness is > 20.+ -. 5mm, a relatively high rolling temperature, such as 980 to 1080 ℃, is used; when the thickness of the slab is less than or equal to 20+/-5 mm, a relatively low rolling temperature, such as 900-980 ℃, is adopted.
In practice, the rolling comprises: and (5) carrying out rolling after heat preservation treatment at the rolling temperature. Wherein the heat preservation treatment time can be 0.7-0.9 min/mm or 60-120 min. The heat preservation treatment time is 0.7-0.9 min per mm of the slab according to the thickness of the slab; when the heat preservation time calculated by the thickness of the slab is less than 60min, the heat preservation is performed for 60min, and the heat preservation time can be properly prolonged, for example, 60-120 min. Wherein, after the first fire rolling, the subsequent fire rolling can directly return to the furnace for temperature compensation, and the temperature compensation time can be 0.3-0.5 min/mm or 30-90 min. The time of furnace return and temperature compensation is 0.3 to 0.5min per mm of the heat preservation treatment time of the slab according to the thickness of the slab; when the temperature compensation time calculated by the thickness of the slab is less than 30min, the temperature compensation is carried out according to 30 min.
In a specific embodiment of the present invention, in the step (a), the deformation ratio of the first hot rolling in the width direction is 10% to 40%, and the deformation ratio of the second hot rolling in the length direction is 10% to 40%.
As in the different embodiments, in step (a), the first hot rolling may have a deformation in the width direction of 10%, 15%, 20%, 25%, 30%, 35%, 40% or a range consisting of any two thereof; the deformation amount of the second hot rolling in the longitudinal direction may be 10%, 15%, 20%, 25%, 30%, 35%, 40 or a range composed of any two of them.
In a preferred embodiment of the present invention, in the step (a), the deformation amount of the first hot rolling in the width direction is 10% to 15%, and the deformation amount of the second hot rolling in the length direction is 10% to 15%.
In a specific embodiment of the present invention, in each of the hot rolling in the step (a) and the step (b), the rolling pass of one hot is 2 to 6 times.
As in the various embodiments, in each of the hot rolling in step (a) and step (b), a hot rolling pass may be 2, 3, 4, 5 or 6, any two of which may constitute a range.
In a specific embodiment of the present invention, in step (b), the total deformation in the width direction is 50% to 90%; in the step (c), the total deformation amount along the length direction is 50% -90%.
As in the various embodiments, in step (b), the total deformation in the width direction may be 50%, 55%, 60%, 65%, 70%, 75%, 80%, 85%, 90% or a range consisting of any two thereof; in step (c), the total deformation in the length direction may be 50%, 55%, 60%, 65%, 70%, 75%, 80%, 85%, 90% or a range composed of any two thereof.
On the basis of performing first fire rolling and second fire rolling to obtain a plate blank A, rolling in the deformation range is performed, so that on one hand, the transverse and longitudinal deformation is basically equivalent, and on the other hand, the regulation and control of the sheet structure are ensured, so that the subsequently obtained sheet has low anisotropy, good room temperature strength and plasticity, and relatively good high temperature strength and excellent high temperature plasticity.
In a specific embodiment of the present invention, in step (b), the deformation amount of each fire in the width direction is independently 15% to 60%, preferably 20% to 45%. Due to Ti 2 The AlNb alloy has large deformation resistance, the excessive deformation rate can cause obvious increase of rolling force of equipment, the same plate difference of the plate is easy to increase, and the plate shape is easy to be deformed; and the deformation rate is too small, so that the deformation mainly occurs on the upper surface and the lower surface of the plate, and the deformation of the core part is small, so that the performance difference in the thickness direction of the plate is easily caused. The steps of the invention are realized by adopting the properProper deformation rate and ensures the performance of the plate.
As in the different embodiments, in step (b), the deformation amount of each fire in the width direction may be 15%, 20%, 25%, 30%, 35%, 40%, 45%, 50%, 55%, 60% or a range of any two of them, independently.
In a specific embodiment of the present invention, in the step (c), the deformation amount in the length direction in the first hot rolling is 15% to 60%, preferably 20% to 45%; the deformation amount of the cladding rolling is 15% -80%, preferably 40% -70%.
As in the different embodiments, in step (c), the deformation amount in the length direction in the one-pass rolling may be 10%, 15%, 20%, 25%, 30%, 35%, 40%, 45%, 50%, 55%, 60% or a range composed of any two thereof; the deformation amount of the clad-rolling may be 15%, 20%, 25%, 30%, 35%, 40%, 45%, 50%, 55%, 60%, 65%, 70%, 75%, 80% or a range of any two of the compositions.
In a specific embodiment of the present invention, the slab is subjected to cladding rolling after being divided into a plurality of portions in the Y direction before the cladding rolling. Further, the multiple halves include halves, thirds, quarters, etc., and can be adjusted according to the slab and jacket dimensions, etc. The cladding rolling comprises two slabs, three slabs, four slabs and five slabs.
In a specific embodiment of the present invention, the Ti 2 The preparation of the AlNb alloy plate blank comprises the following steps: adopts Ti 2 Preparation of Ti from AlNb prealloyed powder by hot isostatic pressing 2 An AlNb alloy slab;
the conditions of the hot isostatic pressing include: the temperature is 980-1200 ℃, the pressure is more than or equal to 100MPa, and the heat preservation time is more than or equal to 1h.
As in the various embodiments, the temperature of the hot isostatic pressing may be 980 ℃, 1000 ℃, 1020 ℃, 1040 ℃, 1050 ℃, 1060 ℃, 1080 ℃, 1100 ℃, 1120 ℃, 1140 ℃, 1150 ℃, 1160 ℃, 1180 ℃, 1200 ℃, or a range of any two thereof; the pressure of the hot isostatic pressing can be more than or equal to 100MPa, more than or equal to 120MPa, more than or equal to 140MPa, more than or equal to 150MPa, more than or equal to 160MPa, more than or equal to 180MPa, more than or equal to 200MPa or a range formed by any two lower limit values thereof; the heat preservation time can be more than or equal to 1h, more than or equal to 2h, more than or equal to 3h, more than or equal to 4h, more than or equal to 5h, more than or equal to 6h or a range formed by any two lower limit values.
In practice, the hot isostatic pressing comprises: ti is mixed with 2 Filling AlNb prealloy powder into a low-carbon steel sheath, wherein the filling density is about 65%, such as 60% -70%, and performing hot isostatic pressing after high-temperature vacuum degassing seal welding; after hot isostatic pressing, cooling by adopting a furnace cooling or air cooling mode, and discharging when the furnace temperature is lower than 300 ℃. After discharging from the furnace, removing the sheath to obtain Ti 2 And (3) an AlNb alloy plate blank.
Wherein, the low-carbon steel sheath can be removed by adopting a mechanical processing or chemical milling mode. When the sheath is removed by mechanical processing, the powder metallurgy Ti is needed to be 2 The AlNb alloy blank and the diffusion reaction layer of the sheath are removed together, the surface roughness Ra of the machined alloy blank is less than or equal to 6.3, and the transitional arc radius R between adjacent surfaces is more than or equal to 5mm. When the jacket is removed by chemical milling, the solution used by the chemical milling is nitric acid, the concentration of the nitric acid is in the range of 1-8 mol/L, and the temperature is in the range of room temperature to 80 ℃. And after the chemical milling is finished, the reaction layer is removed by adopting modes such as polishing or machining.
In a specific embodiment of the invention, the prealloyed powder has a particle size of 250 μm or less, such as 50 to 150 μm.
As in the various embodiments, the prealloyed powder can have a particle size of 250 μm or less, 240 μm or less, 230 μm or less, 220 μm or less, 210 μm or less, 200 μm or less, and the like.
To ensure that the prepared Ti 2 The purity and the compactness of the AlNb alloy plate blank are achieved by selecting prealloy powder which meets the requirements that the oxygen content is less than or equal to 1500ppm, the nitrogen content is less than or equal to 500ppm, the hydrogen content is less than or equal to 50ppm and the hollow powder rate is less than or equal to 1%.
In actual operation, the Ti is 2 The preparation method of the AlNb prealloyed powder comprises the following steps: ti is mixed with 2 The AlNb alloy bar is machined into a powder electrode, and the powder electrode is atomized or sprayed by adopting a plasma rotating electrodeCrucible-free induction smelting ultrasonic gas atomization process for preparing Ti 2 An AlNb prealloyed powder.
Ti produced by the above method 2 The AlNb alloy plate blank has good structural uniformity and relatively small grain size.
In a specific embodiment of the present invention, further comprising: and annealing and sanding the plate blank subjected to cladding and rolling.
In a specific embodiment of the present invention, the annealing includes: the annealing temperature is between 940 and 980 ℃, the heat preservation time is between 1 and 6 hours, and the air cooling is performed after the heat preservation is finished.
The invention also provides a low anisotropic powder Ti using any one of the above 2 Low anisotropic powder Ti prepared by preparation method of AlNb alloy fine-grain thin plate 2 An AlNb alloy fine-grain sheet.
In a specific embodiment of the present invention, the low anisotropy powder Ti 2 In the AlNb alloy fine-grain thin plate, the structure is a fine equiaxed structure, the size of O phase particles is less than 5 mu m, the aspect ratio of the O phase particles is less than 3: 1,O, the crystallographic orientation of the B2 phase is not preferentially distributed, the B2 phase presents a {111} < 110 > texture with certain strength, the strength of the texture in all directions on the plane of the plate is very close, and the isotropy tends to be realized on the plane of the plate.
In a specific embodiment of the present invention, the low anisotropy powder Ti 2 In the AlNb alloy fine-grain sheet, the relative volume of the {111} < 110 > texture in the B2 phase is 50 to 65%. Wherein, the relative volume refers to the proportion of the volume content of a certain texture type of the B2 phase to the total volume content of the B2 phase.
In a specific embodiment of the present invention, the low anisotropy powder Ti 2 The yield strength of the AlNb alloy fine-grain thin plate at the transverse room temperature is more than or equal to 800MPa, preferably more than or equal to 850MPa; the transverse room temperature tensile strength is more than or equal to 950MPa, preferably more than or equal to 1000MPa; the elongation rate at the transverse room temperature is more than or equal to 6%, preferably more than or equal to 7%, preferably more than or equal to 8%, preferably more than or equal to 9%, preferably more than or equal to 10%;
the yield strength of the longitudinal room temperature is more than or equal to 800MPa, preferably more than or equal to 850MPa; the longitudinal room temperature tensile strength is more than or equal to 950MPa, preferably more than or equal to 1000MPa; the longitudinal room temperature elongation is not less than 8%, preferably not less than 9%, preferably not less than 10%, preferably not less than 11%, preferably not less than 12%;
the absolute value of the difference value of the tensile strength of the transverse room temperature and the longitudinal room temperature is less than or equal to 100MPa, preferably less than or equal to 80MPa, preferably less than or equal to 60MPa, preferably less than or equal to 50MPa, preferably less than or equal to 20MPa; the absolute value of the elongation difference in the transverse and longitudinal directions at room temperature is less than or equal to 4%, preferably less than or equal to 3%, preferably less than or equal to 2%, preferably less than or equal to 1%.
The invention also provides the low anisotropic powder Ti 2 The application of the AlNb alloy fine-grain thin plate in preparing the aerospace thin-wall complex structural member.
Example 1
The present embodiment provides a low anisotropic powder Ti 2 The preparation method of the AlNb alloy fine-grain thin plate comprises the following steps:
(1) Ti is mixed with 2 Filling AlNb prealloy powder into a low-carbon steel sheath, and sequentially carrying out vacuum degassing, seal welding and hot isostatic pressing at 1080 ℃/140MPa/4h to obtain Ti with the size of XXYXZ=430 mm×400mm×53mm 2 An AlNb alloy slab;
(2) The alloy slab obtained in the step (1) is rolled after heat preservation for 2 hours at 1040 ℃, the transfer time from discharging to rolling is less than 40 seconds, the slab with the size of X multiplied by Y multiplied by Z=430 mm multiplied by 451mm multiplied by 47mm is obtained by first fire rolling along the Y direction (width direction), then the slab is returned to the furnace for 1040 ℃/30min for temperature compensation, and the slab with the size of X multiplied by Y multiplied by Z=487 mm multiplied by 451mm multiplied by 41.5mm is obtained by second fire rolling along the X direction (length direction); wherein the deformation of the first fire along the Y direction is 11.3%, and the deformation of the second fire along the X direction is 11.7%;
the first firing time comprises three passes, and the reduction in the thickness direction of each pass is 2mm; the second firing time comprises three passes, and the reduction in the thickness direction of each pass is 2mm, 2mm and 1.5mm respectively;
(3) Returning the slab obtained in the step (2) to a furnace for 1040 ℃/30min for temperature compensation, and then performing third-pass rolling along the Y direction to obtain a slab with X multiplied by Y multiplied by Z=487 mm multiplied by 576mm multiplied by 32.5 mm; returning the slab to the furnace for 1040 ℃/30min for temperature compensation, and then continuing to roll for the fourth time along the Y direction to obtain a slab with X multiplied by Y multiplied by Z=487 mm multiplied by 796mm multiplied by 23.5 mm; continuously returning the slab to the furnace for 1040 ℃/30min for temperature compensation, and then rolling for the fifth time along the Y square to obtain a slab with X multiplied by Y multiplied by Z=487 mm multiplied by 1291mm multiplied by 14.5 mm; then carrying out heat treatment on the slab at 940 ℃/30min, and carrying out sixth fire rolling along the Y direction to obtain a slab with X multiplied by Y multiplied by Z=487 mm multiplied by 1780mm multiplied by 10.5 mm; in the step, the deformation amount of the third to sixth fires is 21.7%, 27.6%, 38.5% and 27.5% in sequence along the Y direction, and the total deformation amount of the third to sixth fires is 74.7%;
the third firing time comprises three passes, and the reduction in the thickness direction of each pass is 3mm; the fourth heat comprises three passes, and the reduction in the thickness direction of each pass is 3mm; the fifth firing time comprises three passes, and the reduction in the thickness direction of each pass is 3mm; the sixth heat comprises two passes, and the reduction in the thickness direction of each pass is 2.5mm and 2mm respectively;
(4) Flattening the slab obtained in the step (3), polishing and blanking to obtain three slabs with the dimensions of XXYXZ=460 mm X500 mm X10 mm, carrying out heat preservation treatment on the three slabs at 940 ℃/60min, and then rolling the three slabs with seventh fire along the X direction to obtain slabs with the dimensions of XXYXZ=766 mm X500 mm X6 mm, wherein the total deformation of the seventh fire along the X direction is 40%;
the seventh fire comprises two passes, and the reduction in the thickness direction of each pass is 2mm;
(5) Polishing the three slabs obtained in the step (4) to obtain slabs with X, Y, Z=766 mm, 500mm and 5.5 mm; then placing two slabs in a steel sheath, carrying out heat preservation treatment at 940 ℃/120min, and then carrying out eighth fire rolling along the X direction to obtain slabs with X multiplied by Y multiplied by Z=1755 mm multiplied by 500mm multiplied by 2.4mm, wherein the total deformation of the seventh fire and the eighth fire along the X direction is 74.7%;
the eighth pass comprises four passes, a single piece of Ti 2 The reduction of each pass of the AlNb alloy plate blank along the thickness direction is respectively 1mm, 0.8mm, 0.7mm and 0.6mm;
(6) And (3) carrying out the working procedures of stress relief annealing and sanding at 940 ℃/1h on the sheet obtained in the step (5) to obtain a 2mm finished plate.
Example 2
The present embodiment provides a low anisotropic powder Ti 2 AlNThe preparation method of the b alloy fine-grain thin plate comprises the following steps:
(1) Ti is mixed with 2 Filling AlNb prealloy powder into a low-carbon steel sheath, and sequentially carrying out vacuum degassing, seal welding and hot isostatic pressing at 1080 ℃/140MPa/4h to obtain Ti with the size of XXYXZ=430 mm×400mm×53mm 2 An AlNb alloy slab;
(2) The alloy slab obtained in the step (1) is rolled after being insulated for 2 hours at 1040 ℃, the transfer time from discharging to rolling is less than 40 seconds, the slab with the size of X multiplied by Y multiplied by Z=430 mm multiplied by 498.5mm multiplied by 42.5mm is obtained by first fire rolling along the Y direction (width direction), then the slab is returned to the furnace for 1040 ℃/30min for temperature compensation, and the slab with the size of X multiplied by Y multiplied by Z=537 mm multiplied by 498.5mm multiplied by 34mm is obtained by second fire rolling along the X direction (length direction); wherein the deformation of the first fire along the Y direction is 19.8%, and the deformation of the second fire along the X direction is 19.9%;
the first firing time comprises four passes, and the reduction of each pass in the thickness direction is 3mm, 2.5mm and 2mm respectively; the second firing time comprises three passes, and the reduction in the thickness direction of each pass is 3mm, 3mm and 2.5mm respectively;
(3) Returning the slab obtained in the step (2) to a furnace for 1040 ℃/30min for temperature compensation, and then performing third-pass rolling along the Y direction to obtain a slab with X multiplied by Y multiplied by Z=537 mm multiplied by 712mm multiplied by 23.5 mm; then carrying out 1040 ℃/30min heat preservation treatment on the slab, and continuing to carry out fourth-pass rolling along the Y direction to obtain a slab with X multiplied by Y multiplied by Z multiplied by 537mm multiplied by 1660mm multiplied by 10 mm; in the step, the deformation of the third fire and the fourth fire is 30.0% and 57.1% in sequence along the Y direction, and the total deformation of the third fire to the fourth fire is 70.0%;
the third firing time comprises four passes, and the reduction in the thickness direction of each pass is 3mm, 2.5mm and 2mm respectively; the fourth heat comprises five passes, and the reduction in the thickness direction of each pass is respectively 3mm, 2.5mm and 2mm;
(4) Flattening the slab obtained in the step (3), polishing and blanking to obtain two slabs with the dimensions of XXYXZ=530 mm multiplied by 800mm multiplied by 9.5mm, carrying out heat preservation treatment on the two slabs at 940 ℃/60min, and then rolling the slabs with the fifth fire time along the X direction to obtain slabs with the dimensions of XXYXZ=774 mm multiplied by 800mm multiplied by 6.5mm, wherein the total deformation of the slabs with the fifth fire time along the X direction is 31.5%;
the fifth pass includes one pass;
(5) Polishing the two slabs obtained in the step (4) to obtain slabs with X multiplied by Y multiplied by Z=774mm multiplied by 800mm multiplied by 6mm; then placing the two slabs in a steel ladle, carrying out heat preservation treatment at 940 ℃/120min, and then rolling for the sixth fire along the X direction to obtain slabs with X multiplied by Y multiplied by Z=1766 mm multiplied by 800mm multiplied by 2.3mm, wherein the total deformation of the fifth fire and the sixth fire along the X direction is 70.0%;
the sixth pass comprises four passes, a piece of Ti 2 The reduction of each pass of the AlNb alloy plate blank along the thickness direction is respectively 1.2mm, 1.0mm, 0.9mm and 0.6mm;
(6) And (3) carrying out the working procedures of stress relief annealing and sanding at 940 ℃/1h on the sheet obtained in the step (5) to obtain a 2mm finished plate.
Example 3
The present embodiment provides a low anisotropic powder Ti 2 The preparation method of the AlNb alloy fine-grain thin plate comprises the following steps:
(1) Ti is mixed with 2 Filling AlNb prealloy powder into a low-carbon steel sheath, and sequentially carrying out vacuum degassing, seal welding and hot isostatic pressing at 1080 ℃/140MPa/4h to obtain Ti with the size of XXYXZ=430 mm×400mm×53mm 2 An AlNb alloy slab;
(2) The alloy slab obtained in the step (1) is rolled after heat preservation for 2 hours at 1040 ℃, the transfer time from discharging to rolling is less than 40 seconds, the slab with the size of X multiplied by Y multiplied by Z=430 mm multiplied by 445mm multiplied by 47.5mm is obtained by first fire rolling along the Y direction (width direction), then the slab is returned to the furnace for 1040 ℃/30min for temperature compensation, and the slab with the size of X multiplied by Y multiplied by Z=478 mm multiplied by 445mm multiplied by 42.5mm is obtained by second fire rolling along the X direction (length direction); wherein the deformation of the first fire along the Y direction is 10.1%, and the deformation of the second fire along the X direction is 10.0%;
the first firing time comprises three passes, and the reduction in the thickness direction of each pass is 2mm, 2mm and 1.5mm respectively; the second firing time comprises two passes, and the reduction in the thickness direction of each pass is 3mm and 2mm respectively;
(3) Returning the slab obtained in the step (2) to a furnace for 1040 ℃/30min for temperature compensation, and then performing third-pass rolling along the Y direction to obtain a slab with X multiplied by Y multiplied by Z=478 mm multiplied by 548mm multiplied by 34.5 mm; returning the slab to the furnace for 1040 ℃/30min for temperature compensation, and then continuing to roll for the fourth time along the Y direction to obtain a slab with X multiplied by Y multiplied by Z multiplied by 478mm multiplied by 675mm multiplied by 28 mm; returning the slab to the furnace for 1040 ℃/30min for temperature compensation, and continuing to roll for the fifth time along the Y direction to obtain a slab with X multiplied by Y multiplied by Z multiplied by 478mm multiplied by 840mm multiplied by 22.5 mm; returning the slab to the furnace for 1040 ℃/30min for temperature compensation, and continuing to roll for the sixth fire time along the Y direction to obtain a slab with X multiplied by Y multiplied by Z multiplied by 478mm multiplied by 1021.5mm multiplied by 18.5 mm;
(4) Then carrying out heat preservation treatment on the slab at 940 ℃/30min, and continuing to carry out seventh fire rolling along the Y direction to obtain a slab with X multiplied by Y multiplied by Z multiplied by 478mm multiplied by 1259.5mm multiplied by 15 mm; returning the slab to the furnace for 940 ℃/30min for temperature compensation, and continuing to perform eighth fire rolling along the Y direction to obtain a slab with X multiplied by Y multiplied by Z=478 mm multiplied by 1511mm multiplied by 12.5 mm; returning the slab to the furnace for 940 ℃/30min for temperature compensation, and continuing to roll for the ninth fire time along the Y direction to obtain a slab with X multiplied by Y multiplied by Z multiplied by 478mm multiplied by 1798.5mm multiplied by 10.5 mm; in this step, the deformation amounts of the third to ninth fires are 18.8%, 19.6%, 17.8%, 18.9%, 16.6% and 19.0% in this order in the Y direction, and the total deformation amount of the third to ninth fires is 75.3%;
the third firing time comprises three passes, and the reduction in the thickness direction of each pass is 3mm, 3mm and 2mm respectively; the fourth heat comprises two passes, and the reduction in the thickness direction of each pass is 3.5mm and 3mm respectively; the fifth heat comprises two passes, and the reduction in the thickness direction of each pass is 3mm and 2.5mm respectively; the sixth firing time comprises two times, and the reduction in the thickness direction of each time is 2mm; the seventh pass includes a pass; the eighth pass includes one pass; the ninth pass includes one pass;
(5) Flattening the slab obtained in the step (4), polishing and blanking to obtain three slabs with the dimensions of XXYXZ=450 mm multiplied by 500mm multiplied by 10mm, carrying out heat preservation treatment on the three slabs at 940 ℃/60min, and then rolling the slabs with the dimensions of XXYXZ=750 mm multiplied by 500mm multiplied by 6mm along the X direction for tenth fire time to obtain a slab with the total deformation of 40% along the X direction;
the tenth fire comprises two passes, and the reduction in the thickness direction of each pass is 2mm;
(6) Polishing the three slabs obtained in the step (5) to obtain slabs with the X, Y, Z=750 mm, 500mm and 5.5 mm; then placing two slabs in a steel sheath, carrying out heat preservation treatment at 940 ℃/120min, and rolling for the eleventh fire time along the X direction to obtain slabs with X multiplied by Y multiplied by Z=1875mm multiplied by 500mm multiplied by 2.2mm, wherein the total deformation of the tenth fire time and the eleventh fire time along the X direction is 76.0%;
the eleventh pass comprises four passes, a single piece of Ti 2 The reduction of each pass of the AlNb alloy plate blank along the thickness direction is respectively 1.1mm, 0.9mm, 0.7mm and 0.6mm;
(7) And (3) carrying out the working procedures of stress relief annealing and sanding at 940 ℃/1h on the sheet obtained in the step (6) to obtain a 2mm finished plate.
Example 4
The present embodiment provides a low anisotropic powder Ti 2 The preparation method of the AlNb alloy fine-grain thin plate comprises the following steps:
(1) Ti is mixed with 2 Filling AlNb prealloy powder into a low-carbon steel sheath, and sequentially carrying out vacuum degassing, seal welding and hot isostatic pressing at 1080 ℃/140MPa/4h to obtain Ti with the size of XXYXZ=430 mm×400mm×53mm 2 An AlNb alloy slab;
(2) The alloy slab obtained in the step (1) is rolled after heat preservation for 2 hours at 1040 ℃, the transfer time from discharging to rolling is less than 40 seconds, the slab with the size of X multiplied by Y multiplied by Z=430 mm multiplied by 460.5mm multiplied by 46mm is obtained by first fire rolling along the Y direction (width direction), then the slab is returned to the furnace for 1040 ℃/30min for temperature compensation, and the slab with the size of X multiplied by Y multiplied by Z= 494.5mm multiplied by 460.5mm multiplied by 40mm is obtained by second fire rolling along the X direction (length direction); wherein the deformation rate of the first fire along the Y direction is 13.1%, and the deformation rate of the second fire along the X direction is 13.0%;
the first firing time comprises three passes, and the reduction in the thickness direction of each pass is 3mm, 2mm and 2mm respectively; the second firing time comprises two passes, and the reduction in the thickness direction of each pass is 3mm;
(3) Returning the slab obtained in the step (2) to a furnace for 1040 ℃/30min for temperature compensation, and then performing third-pass rolling along the Y direction to obtain a slab with X multiplied by Y multiplied by Z= 494.5mm multiplied by 921mm multiplied by 20 mm; then carrying out heat preservation treatment on the slab at 940 ℃/30min, and continuing to carry out fourth-pass rolling along the Y direction to obtain a slab with X multiplied by Y multiplied by Z= 494.5mm multiplied by 1754mm multiplied by 10.5 mm; in the step, the deformation of the third to fourth fires is sequentially 50.0% and 47.5% along the Y direction, and the total deformation of the third to fourth fires is 73.7%;
the third heat comprises six passes, and the reduction in the thickness direction of each pass is 3.5mm, 3mm and 3mm respectively; the fourth heat comprises three passes, and the reduction in the thickness direction of each pass is 3.5mm, 3mm and 3mm respectively;
(4) Flattening the slab obtained in the step (3), polishing and blanking to obtain three slabs with the dimensions of XXYXZ=480 mm multiplied by 500mm multiplied by 10mm, carrying out heat preservation treatment on the three slabs at 940 ℃/60min, and then rolling the three slabs with fifth fire along the X direction to obtain slabs with the dimensions of XXYXZ=800 mm multiplied by 500mm multiplied by 6mm, wherein the total deformation of the fifth fire along the X direction is 40%;
the fifth firing time comprises two passes, and the reduction in the thickness direction of each pass is 2mm;
(5) Polishing the three slabs obtained in the step (4) to obtain slabs with X, Y, Z=800 mm, 500mm and 5.5 mm; then placing two slabs in a steel sheath, carrying out heat preservation treatment at 940 ℃/120min, and then rolling with sixth fire along the X direction to obtain slabs with X multiplied by Y multiplied by Z=1833 mm multiplied by 500mm multiplied by 2.3mm, wherein the total deformation of the fifth fire and the sixth fire along the X direction is 73.8%;
the sixth pass comprises four passes, a piece of Ti 2 The reduction of each pass of the AlNb alloy plate blank along the thickness direction is respectively 1mm, 0.8mm, 0.7mm and 0.7mm;
(6) And (3) carrying out the working procedures of stress relief annealing and sanding at 940 ℃/1h on the sheet obtained in the step (5) to obtain a 2mm finished plate.
Example 5
The present embodiment provides a low anisotropic powder Ti 2 The preparation method of the AlNb alloy fine-grain thin plate comprises the following steps:
(1) Ti is mixed with 2 Filling AlNb prealloy powder into a low-carbon steel sheath, and sequentially removing the powder by vacuumTi with dimensions of XXYXZ=430 mm×400mm×53mm is obtained after gas, seal welding and hot isostatic pressing of 1080 ℃/140MPa/4h 2 An AlNb alloy slab;
(2) The alloy slab obtained in the step (1) is rolled after heat preservation for 2 hours at 1040 ℃, the transfer time from discharging to rolling is less than 40 seconds, the slab with the size of X multiplied by Y multiplied by Z=430 mm multiplied by 460.5mm multiplied by 46mm is obtained by first fire rolling along the Y direction (width direction), then the slab is returned to the furnace for 1040 ℃/30min for temperature compensation, and the slab with the size of X multiplied by Y multiplied by Z= 494.5mm multiplied by 460.5mm multiplied by 40mm is obtained by second fire rolling along the X direction (length direction); wherein, the deformation of the first fire along the Y direction is 13.1 percent, and the deformation of the second fire along the X direction is 13.0 percent;
the first firing time comprises three passes, and the reduction in the thickness direction of each pass is 3mm, 2mm and 2mm respectively; the second firing time comprises two passes, and the reduction in the thickness direction of each pass is 3mm;
(3) Returning the slab obtained in the step (2) to a furnace for 1040 ℃/30min for temperature compensation, and then performing third-pass rolling along the Y direction to obtain a slab with X multiplied by Y multiplied by Z= 494.5mm multiplied by 614mm multiplied by 30 mm; returning the slab to the furnace for 1040 ℃/30min for temperature compensation, and then continuing to roll for the fourth time along the Y direction to obtain a slab with X multiplied by Y multiplied by Z= 494.5mm multiplied by 837mm multiplied by 22 mm; and continuously returning the slab to the furnace for 1040 ℃/30min for temperature compensation, and then carrying out fifth-pass rolling along the Y square to obtain the slab with the X multiplied by Y multiplied by Z= 494.5mm multiplied by 1227.5mm multiplied by 15 mm. Then carrying out heat preservation treatment on the slab at 940 ℃/30min, and carrying out sixth fire rolling along the Y direction to obtain a slab with X multiplied by Y multiplied by Z= 494.5mm multiplied by 1673.5mm multiplied by 11 mm; in the step, the deformation amount of the third to sixth fires is 25%, 26.6%, 31.8% and 26.7% in sequence along the Y direction, and the total deformation amount of the third to sixth fires is 72.5%;
the third firing time comprises three passes, and the reduction in the thickness direction of each pass is 3.5mm, 3.5mm and 3mm respectively; the fourth heat comprises three passes, and the reduction in the thickness direction of each pass is 3mm, 3mm and 2mm respectively; the fifth heat comprises three passes, and the reduction in the thickness direction of each pass is 3mm, 2mm and 2mm respectively; the sixth firing time comprises two times, and the reduction in the thickness direction of each time is 2mm;
(4) Flattening the slab obtained in the step (3), polishing and blanking to obtain three slabs with the dimensions of XXYXZ=470 mm X500 mm X10.5 mm, carrying out heat preservation treatment on the three slabs at 940 ℃/60min, and then rolling the three slabs with seventh fire along the X direction to obtain slabs with the dimensions of XXYXZ= 587.5mm X500 mm X8.4 mm, wherein the total deformation of the seventh fire along the X direction is 20%;
the seventh pass includes a pass;
(5) Polishing the three slabs obtained in the step (4) to obtain slabs with the X, Y, Z= 587.5mm, 500mm and 8 mm; then placing two slabs in a steel sheath, carrying out heat preservation treatment at 940 ℃/120min, and then carrying out eighth fire rolling along the X direction to obtain slabs with X multiplied by Y multiplied by Z= 1740.5mm multiplied by 500mm multiplied by 2.3mm, wherein the total deformation of the seventh fire and the eighth fire along the X direction is 73.0%;
the eighth firing time comprises two passes, and the reduction in the thickness direction of each pass is 3.2mm and 2.5mm respectively;
(6) And (3) carrying out the stress relief annealing and sanding process of 960 ℃/1h on the thin plate obtained in the step (5) to obtain a 2mm finished plate.
Example 6
The present embodiment provides a low anisotropic powder Ti 2 The manufacturing method of the thin-crystal sheet of the AlNb alloy, referring to example 5, differs only in that: steps (4) to (5) are different.
Examples (4) to (5) of the present embodiment include:
(4) Flattening the slab obtained in the step (3), polishing and blanking to obtain three slabs with the dimensions of XXYXZ=470 mm X500 mm X10.5 mm, carrying out heat preservation treatment on the three slabs at 940 ℃/60min, and then carrying out seventh fire rolling along the X direction to obtain slabs with the dimensions of XXYXZ=897 mm X500 mm X5.5 mm, wherein the total deformation of the seventh fire along the X direction is 47.6%;
the seventh fire comprises two passes, and the reduction in the thickness direction of each pass is 3mm and 2mm respectively;
(5) Polishing the three slabs obtained in the step (4) to obtain slabs with the X, Y, Z=897 mm, 500mm and 5mm; then placing two slabs in a steel sheath, carrying out heat preservation treatment at 940 ℃/120min, and then carrying out eighth fire rolling along the X direction to obtain slabs with X multiplied by Y multiplied by Z=1750 mm multiplied by 500mm multiplied by 2.3mm, wherein the total deformation of the seventh fire and the eighth fire along the X direction is 72.7%;
the eighth pass includes one pass.
Example 7
The present embodiment provides a low anisotropic powder Ti 2 The manufacturing method of the thin-crystal sheet of the AlNb alloy, referring to example 1, differs only in that: the corresponding rolling temperatures in steps (2) to (5) are all 940 ℃.
Example 8
The present embodiment provides a low anisotropic powder Ti 2 The manufacturing method of the thin-crystal sheet of the AlNb alloy, referring to example 1, differs only in that: the corresponding rolling temperatures in steps (2) to (5) are all 1040 ℃.
Comparative example 1
Comparative example 1 provides a Ti 2 The preparation method of the AlNb alloy plate comprises the following steps:
(1) Ti is mixed with 2 Filling AlNb prealloy powder into a low-carbon steel sheath, and sequentially carrying out vacuum degassing, seal welding and hot isostatic pressing at 1080 ℃/140MPa/4h to obtain Ti with the dimensions of XXYXZ=420 mm X373 mm X55 mm 2 An AlNb alloy slab;
(2) The alloy plate blank obtained in the step (1) is rolled after heat preservation for 2 hours at 940 ℃, the transfer time from discharging to rolling is less than 40 seconds, after first fire rolling is carried out along the Y direction (width direction), the furnace is returned to carry out 940 ℃/30min temperature compensation, and second fire rolling is carried out, so that the plate blank with X multiplied by Y multiplied by Z=425 mm multiplied by 505mm multiplied by 40mm is obtained, wherein the deformation amount of the first fire rolling is 3mm in the thickness direction of each pass, the second fire rolling is carried out for two passes, and the deformation amount of each pass in the thickness direction is 3mm;
then carrying out heat preservation treatment at 940 ℃/1h, rolling along the X direction (length direction), carrying out heat preservation treatment at 940 ℃/1h between two adjacent heat times, and rolling at four heat times to obtain a slab with X multiplied by Y multiplied by Z=1650mm multiplied by 510mm multiplied by 10mm, wherein three passes are rolled at the third heat time, the deformation amount of each pass in the thickness direction is 3mm, three passes are rolled at the fourth heat time, the deformation amount of each pass in the thickness direction is 3mm, two passes are rolled at the fifth heat time, the deformation amount of each pass in the thickness direction is 3mm, two passes are rolled at the sixth heat time, and the deformation amount of each pass in the thickness direction is 3mm;
(3) Cutting a slab with the dimensions of XXYXZ=1650 mm×510mm×10mm to obtain a slab with the dimensions of XXYXZ=800 mm×510mm×10mm, polishing the slab to obtain a slab with the dimensions of XXYXZ=800 mm×510mm×9mm, cladding-rolling the slab at the rolling temperature of 940 ℃ for 120min, performing seventh three-pass rolling along the Y direction, and obtaining slabs with the thickness of 2mm after sanding, wherein the deformation amounts of the three passes in the thickness direction are respectively 3mm, 2mm and 1.7 mm; in the whole rolling process, the final rolling temperature is controlled to be higher than 750 ℃;
(4) And (3) preserving heat of the plate obtained in the step (3) for 2 hours at 940 ℃, and then air-cooling.
Experimental example 1
For comparative purposes, ti prepared in the different examples and comparative examples 2 Differences of AlNb alloy plates, with respect to the obtained Ti 2 Characterization of the longitudinal and transverse microstructures of the AlNb alloy plate, FIGS. 1-2 show the Ti prepared in example 1 of the present invention 2 Longitudinal and transverse microstructure diagrams of the AlNb alloy fine-grain sheet are shown in FIGS. 3 to 4, which show the orientation distribution diagrams of the O phase and the beta/B2 phase on the rolled surface, respectively. The difference in sheet transverse and longitudinal directions is related to the relative volume of the B2 phase {111} < 110 > texture of the sheet, while the O phase has no apparent orientation distribution, i.e., is substantially isotropic in all directions. The microstructural data for the remaining examples and comparative examples are shown in table 1.
TABLE 1 different Ti 2 Relative volume of phase {111} < 110 > texture of AlNb alloy plate B2
From the above test results, it is known that Ti is prepared by the method of the present invention 2 The AlNb alloy fine-grain thin plate has small difference of transverse and longitudinal microstructure, low anisotropy and uniform structureThe uniformity is good.
Experimental example 2
For comparative purposes, ti prepared in the different examples and comparative examples 2 Mechanical property difference of AlNb alloy plate, to the obtained Ti 2 The longitudinal and transverse mechanical properties of the AlNb alloy plate are characterized, and the longitudinal and transverse mechanical properties are shown in Table 2.
TABLE 2 different Ti 2 Mechanical property test result of AlNb alloy plate at room temperature (23℃)
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As can be seen from the above test results, the Ti prepared by the method of the present invention 2 The AlNb alloy fine-grain thin plate has good room temperature strength and plasticity, relatively low high temperature strength and excellent high temperature plasticity, and is beneficial to Ti 2 The AlNb alloy fine-grain thin plate hot forming member lays a good foundation for the subsequent preparation of the aerospace thin-wall complex structural member.
Finally, it should be noted that: the above embodiments are only for illustrating the technical solution of the present invention, and not for limiting the same; although the invention has been described in detail with reference to the foregoing embodiments, it will be understood by those of ordinary skill in the art that: the technical scheme described in the foregoing embodiments can be modified or some or all of the technical features thereof can be replaced by equivalents; such modifications and substitutions do not depart from the spirit of the invention.
Claims (10)
1. Low anisotropic powder Ti 2 The preparation method of the AlNb alloy fine-grain thin plate is characterized by comprising the following steps of:
(a) Along Ti 2 First hot rolling is carried out on the AlNb alloy plate blank in the width direction, and then the plate blank is rolled along the Ti 2 Performing second hot rolling in length direction of AlNb alloy plate blankObtaining a plate blank A;
(b) Rolling the slab A along the width direction for at least two times to obtain a slab B;
(c) Performing primary fire rolling on the slab B along the length direction, and performing cladding rolling along the length direction;
the absolute value of the difference between the deformation ratio in the width direction in step (b) and the deformation ratio in the length direction in step (c) is not more than 20%.
2. The method according to claim 1, wherein the temperature of the rolling is 900 to 1080 ℃.
3. The production method according to claim 1, wherein in the step (a), the deformation ratio of the first hot rolling in the width direction is 10% to 40%, and the deformation ratio of the second hot rolling in the length direction is 10% to 40%;
preferably, the deformation rate of the first hot rolling in the width direction is 10% -15%, and the deformation rate of the second hot rolling in the length direction is 10% -15%.
4. The method according to claim 1, wherein in the step (b), the total deformation ratio in the width direction is 50% to 90%; in the step (c), the total deformation rate along the length direction is 50-90%.
5. The production method according to claim 1, wherein in the step (b), the deformation rate of each firing in the width direction is 15% to 60% independently;
preferably, in the step (b), the deformation rate of each fire in the width direction is 20% to 45% independently.
6. The method according to claim 1, wherein in the step (c), the deformation ratio in the longitudinal direction in the one-pass rolling is 10% to 50%; the deformation rate of the cladding rolling is 15% -80%;
preferably, in the step (c), in the first hot rolling, the deformation rate in the length direction is 35% -45%; the deformation rate of the cladding rolling is 40% -70%.
7. The method according to claim 1, wherein the Ti is 2 The preparation of the AlNb alloy plate blank comprises the following steps: adopts Ti 2 Preparation of Ti from AlNb prealloyed powder by hot isostatic pressing 2 An AlNb alloy slab;
the conditions of the hot isostatic pressing include: the temperature is 980-1200 ℃, the pressure is more than or equal to 100MPa, and the heat preservation time is more than or equal to 1h;
preferably, the particle size of the prealloyed powder is less than or equal to 250 mu m.
8. A low anisotropic powder Ti prepared by the process according to any one of claims 1 to 7 2 An AlNb alloy fine-grain sheet.
9. The low anisotropy powder Ti according to claim 8 2 The AlNb alloy fine-grain thin plate is characterized in that the low anisotropic powder Ti 2 In the AlNb alloy fine-grain thin plate, the structure is a fine equiaxed structure, the size of O phase particles is less than 5 mu m, the aspect ratio of the O phase particles is less than 3: 1,O, the crystallographic orientation of the B2 phase is not preferentially distributed, and the B2 phase has {111} < 110 > texture.
10. The low anisotropy powder Ti of claim 8 or 9 2 The application of the AlNb alloy fine-grain thin plate in preparing the aerospace thin-wall complex structural member.
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