CN117702028A - Ti (titanium) 2 AlNb alloy fine-grain plate and superplastic forming method and application thereof - Google Patents
Ti (titanium) 2 AlNb alloy fine-grain plate and superplastic forming method and application thereof Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 75
- 239000000956 alloy Substances 0.000 title claims abstract description 75
- 238000000034 method Methods 0.000 title claims abstract description 28
- 239000010936 titanium Substances 0.000 title claims description 65
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 title claims description 3
- 229910052719 titanium Inorganic materials 0.000 title claims description 3
- 238000005096 rolling process Methods 0.000 claims description 36
- 238000000137 annealing Methods 0.000 claims description 25
- 238000005098 hot rolling Methods 0.000 claims description 19
- 238000002360 preparation method Methods 0.000 claims description 8
- 238000005253 cladding Methods 0.000 claims description 5
- 238000010304 firing Methods 0.000 claims description 5
- 239000002245 particle Substances 0.000 claims description 5
- 238000012545 processing Methods 0.000 abstract description 3
- 229910001069 Ti alloy Inorganic materials 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 15
- 238000004321 preservation Methods 0.000 description 10
- 239000000463 material Substances 0.000 description 4
- 238000001513 hot isostatic pressing Methods 0.000 description 3
- 238000012986 modification Methods 0.000 description 3
- 230000004048 modification Effects 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 238000005498 polishing Methods 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 238000012360 testing method Methods 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
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
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- 230000001276 controlling effect Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000007599 discharging Methods 0.000 description 1
- 238000011049 filling Methods 0.000 description 1
- 239000003063 flame retardant Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000011534 incubation Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
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- 238000009849 vacuum degassing Methods 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
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Abstract
The invention relates to the technical field of alloy processing, in particular to a Ti alloy 2 An AlNb alloy fine-grain plate and a superplastic forming method and application thereof. The method not only can obtain fine-grain equiaxed structures, but also can improve the strain rate of superplastic forming and shorten the forming time of the component. Ti treated by superplastic forming method 2 The AlNb alloy fine-grain plate has higher superplasticity and is subsequent aerospace Ti 2 The forming of the AlNb alloy thin-wall complex member lays a good foundation.
Description
Technical Field
The invention relates to the technical field of alloy processing, in particular to Ti 2 An AlNb alloy fine-grain plate and a superplastic forming 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, can be used for a long time at 600-750 ℃ or used for a short time at a higher temperature, has great application potential especially in the aspect of aerospace structural materials, and has important significance in the aspects of improving thrust ratio of an aircraft, improving fuel efficiency, high-temperature service performance and the like.
Superplasticity of a material refers to the general term that under certain conditions (high temperature, fine grain and low strain rate) a material exhibits an abnormally high elongation. Materials are often judged to have superplasticity with an elongation exceeding 100%. The superplastic forming technology is used as one of the key technology for forming large integral complex thin-wall components in the aerospace field, and can be used for producing complex components with low cost, high weight reduction and near zero allowance processing.
With the rapid development of high-performance aircrafts, the method for preparing Ti 2 The need for thin-walled, complex components of an AlNb alloy is increasing. Therefore require Ti 2 The AlNb alloy sheet has good superplastic forming property and uniform deformability in different directions. But now conventional Ti 2 In order to obtain higher superplastic performance, the AlNb alloy sheet is controlled at 10 strain rate -5 s -1 This results in a long forming time of the component, which is difficult to meet the requirements of engineering applications, while conventional Ti 2 The AlNb alloy thin plate also has large anisotropy difference, and the quality of the superplastic forming member is reduced.
In view of this, the present invention has been made.
Disclosure of Invention
A first object of the present invention is to provide a Ti 2 The method can not only obtain fine grain equiaxed structure, but also improve the strain rate of superplastic forming and shorten the forming time of the component.
A second object of the present invention is to provide Ti as described above 2 Ti processed by superplastic forming method of AlNb alloy fine-grain plate 2 The AlNb alloy fine-grain plate has higher superplasticity and is subsequent aerospace Ti 2 The forming of the AlNb alloy thin-wall complex member lays a good foundation.
A third object of the present invention is to provide Ti as described above 2 The application of the AlNb alloy fine-grain 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:
the invention provides a Ti 2 The superplastic forming method of the AlNb alloy fine-grain plate comprises the following steps:
ti is mixed with 2 Annealing the AlNb alloy fine-grain plate at 900-1000 deg.c, and then at 900-1000 deg.c, strain rate of 1 x 10 -4 s -1 ～5×10 -3 s -1 Superplastic forming treatment is carried out between the two.
Preferably, the annealing treatment is performed for 2-3 hours.
Preferably, the Ti is 2 In the AlNb alloy fine-grain 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.
Preferably, the Ti is 2 The preparation method of the AlNb alloy fine-grain 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 the step (b) and the deformation ratio in the length direction in the step (c) is less than or equal to 20%;
in steps (a), (b) and (c), the rolling temperature is 900-1080 ℃.
Preferably, 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, 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%.
Preferably, in the step (b), the deformation ratio of each fire in the width direction is 15% to 60% independently.
Preferably, in the step (c), in the first hot rolling, the deformation rate in the length direction is 10% to 50%; the deformation rate of the cladding rolling is 15-80%.
The Ti provided by the invention 2 Ti prepared by superplastic forming method of AlNb alloy fine-grain plate 2 An AlNb alloy fine-grain plate.
The Ti provided by the invention 2 The application of the AlNb alloy fine-grain plate in preparing the aerospace thin-wall complex structural member.
Compared with the prior art, the invention has the beneficial effects that:
(1) Ti provided by the invention 2 The superplastic forming method of the AlNb alloy fine-grain plate can obtain fine-grain equiaxed structures, can improve the strain rate of the superplastic forming and shorten the forming time of the component.
(2) Ti provided by the invention 2 Superplastic forming method of AlNb alloy fine-grain plate by adopting Ti with low anisotropy 2 The AlNb alloy fine-grain plate is used as a raw material, and further fine-grain equiaxed structures are obtained through annealing, so that the alloy plate can obtain higher superplasticity.
(3) Ti provided by the invention 2 The AlNb alloy fine-grain plate has higher superplasticity and is subsequent aerospace Ti 2 The forming of the AlNb alloy thin-wall complex member lays a good foundation.
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 provided in the embodiment of the invention 2 Microstructure of the AlNb alloy fine-grain plate before annealing;
FIG. 2 shows Ti as provided in the embodiment of the invention 2 Microstructure of the AlNb alloy fine-grain plate before annealing.
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.
In a first aspect, based on existing Ti 2 The AlNb alloy fine-grain plate is characterized in that the structure of the raw material is coarse and the superplasticity is low, and the Ti provided by the invention 2 The superplastic forming method of the AlNb alloy fine-grain plate comprises the following steps:
ti is mixed with 2 Annealing the AlNb alloy fine-grain plate at 900-1000 deg.c, and then at 900-1000 deg.c, strain rate of 1 x 10 -4 s -1 ～5×10 -3 s -1 Superplastic forming treatment is carried out between the two.
The invention is characterized in thatTi provided 2 The method for superplastic forming of the AlNb alloy fine-grain plate is characterized in that elongated strip-shaped O is subjected to annealing treatment at a specific temperature, so that the elongated strip-shaped O is axially equalized in the rolling process, and meanwhile, fine equiaxial O phases are separated out, so that a fine-grain equiaxial structure is obtained, the strain rate of superplastic forming is improved, the forming time of a component is shortened, and higher superplasticity is obtained. The microscopic images before and after annealing are shown in fig. 1 and 2, and the results show that the annealing can obtain finer fine-grained equiaxed structures.
In some embodiments, the annealing treatment may be any one or a range of values of any two or any two of 900 ℃, 910 ℃, 920 ℃, 930 ℃, 940 ℃, 950 ℃, 960 ℃, 970 ℃, 980 ℃, 990 ℃, 1000 ℃.
In some embodiments, the time of the annealing treatment is from 2h to 3h, such as any one point value or range of values of any two points values of 2h, 2.5h, 3h.
The invention selects the annealing temperature from the O+B2 two-phase region to alpha through reasonable annealing treatment temperature and time 2 The temperature between the +O and B2 three-phase regions (the specific temperature is between 900 ℃ and 1000 ℃) can avoid the growth of the grain size in the temperature region, and provide a fine structure for superplastic forming. Reasonable temperature and time of superplastic forming treatment are favorable for obtaining fine-grain equiaxed structures.
In some embodiments, the invention employs Ti with low anisotropy 2 The AlNb alloy fine-grain plate has fine equiaxed structure, O phase grain size smaller than 5 microns, O phase grain length-width ratio smaller than 3: 1,O phase crystallographic orientation, and B2 phase with {111} < 110 > structure. Further, the relative volume of {111} < 110 > texture in the B2 phase is 50-65%. 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 some embodiments, ti 2 The AlNb alloy fine-grain plate is low-anisotropy 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 AlNb alloy slabPerforming second hot rolling in the length direction 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 the width direction in the step (b) and the deformation ratio in the length direction in the step (c) is less than or equal to 20%;
in steps (a), (b) and (c), the rolling temperature is 900 to 1080 ℃, for example 900 ℃, 920 ℃, 950 ℃, 980 ℃, 1000 ℃, 1050 ℃, 1080 ℃ or a range of values of any one or any two points.
The invention obtains the required Ti with low anisotropism by the method 2 The AlNb alloy fine-grain plate is favorable for further obtaining fine-grain equiaxed structures through annealing treatment.
In some 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 limits 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 perpendicular to the thickness direction Z direction of the initial Ti2AlNb alloy plate blank.
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 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 some embodiments, in step (a), the first hot rolling has a deformation ratio in the width direction of 10% to 40%, and the second hot rolling has a deformation ratio in the length direction of 10% to 40%.
In some embodiments, in step (a), the first pass rolling may have a deformation in the width direction of 10%, 15%, 20%, 25%, 30%, 35%, 40% or a range of any two thereof; the deformation amount of the second hot rolling in the longitudinal direction may be any one point value or a range of any two point values of 10%, 15%, 20%, 25%, 30%, 35%, 40%.
Specifically, in the step (a), the deformation rate of the first hot rolling in the width direction is 10% -40%, and the deformation rate of the second hot rolling in the length direction is 10% -40%. Further, the deformation amount of the first hot rolling in the width direction may be any one point value or a range of any two point values of 10%, 18%, 20%, 24%, 32%, 38%, 40%; the deformation amount of the second hot rolling in the longitudinal direction may be any one point value or a range of any two point values of 10%, 15%, 20%, 25%, 30%, 35%, 40.
In some embodiments, in each of the hot rolling in step (a) and step (b), the rolling pass for one hot is 2 to 6 times.
In some embodiments, in step (a), the total deformation ratio in the width direction in step (b) is 50% to 90%; in the step (c), the total deformation rate along the length direction is 50-90%.
Specifically, in step (b), the total deformation amount in the width direction may be 50%, 55%, 60%, 65%, 70%, 75%, 80%, 85%, 90% or a range composed of any two thereof; in the step (c), the total deformation amount in the longitudinal direction may be any one point value or a range of any two point values of 50%, 55%, 60%, 65%, 70%, 75%, 80%, 85%, 90%.
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 some embodiments, in step (b), the deformation ratio of each fire in the width direction is each independently 15% to 60%, for example, any one point value or a range of any two point values of 15%, 20%, 25%, 30%, 35%, 40%, 45%, 50%, 55%, 60%.
In some embodiments, in step (c), the deformation ratio in the length direction in one pass rolling is 10% to 50%, for example, any one point value or a range of any two point values of 10%, 15%, 20%, 25%, 30%, 35%, 40%, 45%, 50%; the deformation ratio of the clad-rolling is 15% to 80%, for example, 15%, 20%, 25%, 30%, 35%, 40%, 45%, 50%, 55%, 60%, 65%, 70%, 75%, 80% or a range of values between any two points.
In particular, the low anisotropy Ti used in the present invention 2 The AlNb alloy fine-grain plate is made of Ti 2 The preparation method 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 And (3) an AlNb alloy plate blank. Preferably, the conditions of hot isostatic pressing include: the temperature is 980-1200 ℃ (for example 980 ℃, 1000 ℃, 1020 ℃, 1040 ℃, 1050 ℃, 1060 ℃, 1080 ℃, 1100 ℃, 1120 ℃, 1140 ℃, 1150 ℃, 1160 ℃, 1180 ℃, 1200 ℃ or any two point value range value), the pressure is more than or equal to 100MPa (for example 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 to180MPa, or 200MPa, or a range of any two points), the incubation time is 1h or more (e.g., 1h, 2h, 3h, 4h, 5h, 6h, or a range of any two points). However, other conventional methods for producing alloy slabs are also possible, and the examples of the present invention are not limited to these examples.
In a second aspect, the invention provides Ti 2 Ti prepared by superplastic forming method of AlNb alloy fine-grain plate 2 An AlNb alloy fine-grain plate.
In a third aspect, the invention provides Ti 2 The application of the AlNb alloy fine-grain plate in preparing the aerospace thin-wall complex structural member.
Preparation of raw material 1: the preparation method of the 2mm sample 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.
The microstructure of the sheet was shown in FIG. 1, the relative volume of the B2 phase {111} < 110 > texture was 60%, the average size of the O phase particles was 4 μm, and the average aspect ratio was 1.1.
Example 1
Annealing the 2mm finished plate at 940 ℃ for 2 hours, and then performing superplastic forming treatment, wherein the superplastic forming treatment temperature is 940 ℃ and the strain rate is 1 multiplied by 10 -3 s -1 。
Example 2
Annealing the 2mm finished plate at 900 ℃ for 3 hours, and then performing superplastic forming treatment, wherein the superplastic forming treatment temperature is 900 ℃ and the strain rate is 1 multiplied by 10 -4 s -1 。
Example 3
Annealing the 2mm finished plate at 960 ℃ for 2.5h, and then performing superplastic forming treatment, wherein the superplastic forming treatment temperature is 1000 ℃ and the strain rate is 5 multiplied by 10 -4 s -1 。
Example 4
Annealing the 2mm finished plate at 940 ℃ for 2 hours, and then performing superplastic forming treatment, wherein the superplastic forming treatment temperature is 940 ℃ and the strain rate is 6 multiplied by 10 -4 s -1 。
Comparative example 1
Comparative example 1 was conducted without annealing treatment, and only superplastic forming treatment was conducted, and the treatment temperature and strain rate were the same as in example 1.
Comparative example 2
Comparative example 2 was conducted by performing only superplastic forming treatment without annealing treatment as compared with example 4, and the treatment temperature and strain rate were the same as those of example 4.
Comparative example 3
Comparative example 3 was identical to example 1 except that the annealing temperature was 1050 ℃.
Comparative example 4
Comparative example 4 was identical to example 1 except that the annealing temperature was 880 ℃.
Comparative example 5
Comparative example 5 was the same as example 1 except that the temperature of the superplastic forming treatment was 1100 ℃.
Comparative example 6
Comparative example 6 was identical to example 1 except that the temperature of the superplastic forming treatment was 880 ℃.
Comparative example 7
Comparative example 7 compared with example 1, the rate of superplastic forming treatment was 1X 10 alone -5 s -1 The remainder being the same.
Experimental example
To make a comparison of Ti after superplastic forming treatment of 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 a table 1.
TABLE 1Ti 2 Mechanical property test result of AlNb alloy plate superplastic forming treatment
From the above test results, it is understood that Ti is produced by the superplastic forming method of the present invention 2 The AlN plate Jin Xijing sheet has good strength and plasticity, has high elongation and good superplasticity, and lays a good foundation for the subsequent preparation of the aerospace thin-wall complex structural member.
While the invention has been illustrated and described with reference to specific embodiments, it is to be understood that the above embodiments are merely illustrative of the technical aspects of the invention and not restrictive thereof; those of ordinary skill in the art will appreciate that: modifications may be made to the technical solutions described in the foregoing embodiments, or equivalents may be substituted for some or all of the technical features thereof, without departing from the spirit and scope of the present invention; such modifications and substitutions do not depart from the spirit of the corresponding technical solutions; it is therefore intended to cover in the appended claims all such alternatives and modifications as fall within the scope of the invention.
Claims (10)
1. Ti (titanium) 2 The superplastic forming method of the AlNb alloy fine-grain plate is characterized by comprising the following steps of:
ti is mixed with 2 Annealing the AlNb alloy fine-grain plate at 900-1000 deg.c, and then at 900-1000 deg.c, strain rate of 1 x 10 -4 s -1 ～5×10 -3 s -1 Superplastic forming treatment is carried out between the two.
2. Ti according to claim 1 2 The superplastic forming method of the AlNb alloy fine-grain plate is characterized in that the annealing treatment time is 2-3 hours.
3. Ti according to claim 1 2 A method for superplastic forming of an AlNb alloy fine-grain plate, characterized by comprising the steps of 2 In the AlNb alloy fine-grain 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.
4. A Ti according to claim 3 2 A method for superplastic forming of an AlNb alloy fine-grain plate, characterized by comprising the steps of 2 The preparation method of the AlNb alloy fine-grain 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 the step (b) and the deformation ratio in the length direction in the step (c) is less than or equal to 20%;
in steps (a), (b) and (c), the rolling temperature is 900-1080 ℃.
5. Ti according to claim 4 2 The superplastic forming method of the AlNb alloy fine-grain plate is characterized in that in the step (a), the deformation rate of the first hot rolling in the width direction is 10% -40%, and the deformation rate of the second hot rolling in the length direction is 10% -40%.
6. Ti according to claim 4 2 The superplastic forming method of the AlNb alloy fine-grain plate is characterized in that in the step (b), the total deformation rate in the width direction is 50-90%; in the step (c), the total deformation rate along the length direction is 50-90%.
7. Ti according to claim 4 2 A method for superplastic forming of an AlNb alloy fine-grain plate, characterized in that in the step (b), the deformation rate of each firing in the width direction is 15 to 60% independently of each other.
8. Ti according to claim 4 2 The superplastic forming method of the AlNb alloy fine-grain plate is characterized in that in the step (c), the deformation rate in the length direction in the first-pass rolling is 10-50%; the deformation rate of the cladding rolling is 15-80%.
9. Ti according to any one of claims 1-8 2 Ti prepared by superplastic forming method of AlNb alloy fine-grain plate 2 An AlNb alloy fine-grain plate.
10. Ti according to claim 9 2 The application of the AlNb alloy fine-grain plate in preparing the aerospace thin-wall complex structural member.
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102212766A (en) * | 2011-05-24 | 2011-10-12 | 哈尔滨工业大学 | Hot machining method for thinning Ti2AlNb-based alloy grains |
| WO2014007359A1 (en) * | 2012-07-02 | 2014-01-09 | 日本発條株式会社 | α+β TYPE Ti ALLOY AND PROCESS FOR PRODUCING SAME |
| CN105088118A (en) * | 2014-05-04 | 2015-11-25 | 中国科学院金属研究所 | Grain ultra-fining method for nickel-based superalloy board |
| CN108088760A (en) * | 2017-12-15 | 2018-05-29 | 佛山三维二次方科技有限公司 | Ti2AlNb alloys superplastic forming/diffusion connecting process |
| CN111085546A (en) * | 2019-12-21 | 2020-05-01 | 江苏骏茂新材料科技有限公司 | Preparation method of super-large wide alloy plate |
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Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102212766A (en) * | 2011-05-24 | 2011-10-12 | 哈尔滨工业大学 | Hot machining method for thinning Ti2AlNb-based alloy grains |
| WO2014007359A1 (en) * | 2012-07-02 | 2014-01-09 | 日本発條株式会社 | α+β TYPE Ti ALLOY AND PROCESS FOR PRODUCING SAME |
| CN105088118A (en) * | 2014-05-04 | 2015-11-25 | 中国科学院金属研究所 | Grain ultra-fining method for nickel-based superalloy board |
| CN108088760A (en) * | 2017-12-15 | 2018-05-29 | 佛山三维二次方科技有限公司 | Ti2AlNb alloys superplastic forming/diffusion connecting process |
| CN111085546A (en) * | 2019-12-21 | 2020-05-01 | 江苏骏茂新材料科技有限公司 | Preparation method of super-large wide alloy plate |
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