CN108326041B - Equidistant rolling method for spiral conical rollers of large-size titanium alloy ultrafine-grained bar - Google Patents
Equidistant rolling method for spiral conical rollers of large-size titanium alloy ultrafine-grained bar Download PDFInfo
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 96
- 238000005096 rolling process Methods 0.000 title claims abstract description 95
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- 238000010438 heat treatment Methods 0.000 claims abstract description 23
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- 230000001186 cumulative effect Effects 0.000 description 3
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- 229910052751 metal Inorganic materials 0.000 description 2
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- 125000004122 cyclic group Chemical group 0.000 description 1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/16—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling wire rods, bars, merchant bars, rounds wire or material of like small cross-section
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B27/00—Rolls, roll alloys or roll fabrication; Lubricating, cooling or heating rolls while in use
- B21B27/02—Shape or construction of rolls
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- B21B27/025—Skew rolls
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Abstract
The invention discloses a spiral conical roller equidistant rolling method for large-size titanium alloy ultrafine crystal bars, which relates to the technical field of machining, in particular to a spiral conical roller equidistant rolling method for large-size titanium alloy ultrafine crystal bars, and comprises the following steps of S1 selecting titanium alloy blanks with the diameter D of 40-150mm and the length of 300-plus 5000mm, S2 placing the titanium alloy blanks in a heating furnace to be heated to 800-plus 1120 ℃, S3 transferring the heated titanium alloy blanks from the heating furnace to a guide chute of a skew rolling mill, S4 feeding the titanium alloy blanks in the guide chute of the skew rolling mill, feeding the titanium alloy blanks into a deformation area between an inlet and an outlet of the skew rolling mill, carrying out spiral motion of the titanium alloy blanks in the deformation area until the deformation is finished, S5 repeating the steps S2-S4, carrying out 2-8 times of spiral rolling on the titanium alloy blanks to obtain TC18 titanium alloy integral ultrafine crystal bars, and the invention has the advantages of large penetration depth of the deformation area, continuous multi-continuous and stable multi-torsion and severe rolling, and can obtain ideal three-dimensional composite grain thinning effect.
Description
Technical Field
The invention relates to the technical field of machining, in particular to an equidistant rolling method of a spiral conical roller for large-size titanium alloy ultrafine crystal bars.
Background
When the nano-scale material is prepared by adopting a Plastic Deformation mode, the equivalent strain is usually more than 6, the traditional Plastic processing method is difficult to realize, and the method can be realized by applying a super Plastic Deformation method (SPD). Modern SPD starts from the combination of high pressure and shear deformation forming method proposed by Bridgemen, the rapid development starts from soviet union and western countries before the middle of the 70 th 20 th century, and Segal develops Equal-Channel angular Extrusion (ECAP), which marks the arrival of the microstructure era of SPD research. Over the last 10 years, thousands of research results have been published.
Definition of SPD generally accepted after 2006: the metal forming method which enables the block to generate super strain without obviously changing the geometric dimension of the block and presents the grain refinement effect of a large-angle grain boundary can obtain the grain sizes of micron-scale (100-1000 nm) and nanometer-scale (less than 100 nm), and can be called nano SPD (nano SPD for short). The nano SPD material has a large amount of large-angle non-equilibrium grain boundary tissues containing high-density dislocation and high internal stress, so that the material shows mechanical behavior and a deformation mechanism different from those of the traditional coarse-grained material.
The current processing technical scheme is as follows: typical SPD methods include High Pressure Torsion (HPT), equal channel angular pressing-deforming (ECAP), cumulative rolling (ARB), Twist Extrusion (TE), and Multi-Directional Forging (MDF).
Wherein, (1) high-pressure torsional deformation, namely applying a plurality of GPa pressure on an original sample (block or powder) placed in a supporting groove, and relatively rotating an upper anvil and a lower anvil to cause the sample to generate strong shear deformation to refine grains, and the high-pressure torsional deformation is characterized in that a workpiece is disc-shaped and has a small size, the diameter is 10-20 mm, and the thickness is 0.2-0.5 mm.
(2) And (3) equal-diameter angular extrusion deformation, namely extruding the material from the end to the other end through two intersecting constant-angle equal-section channels in the die, changing the movement direction of the material through a bending angle to generate pure shear deformation, and repeatedly carrying out the forming process, wherein the shear strain quantity is increased along with deformation passes.
(3) The cumulative lap rolling method is characterized in that the original plates are subjected to double-layer stacking after surface treatment, are subjected to roll welding after being heated at , are sent back to the surface treatment from middle shearing and then are subjected to the next roll welding circulation, and in order to ensure that the rolled plates can be welded at , the reduction of each pass is not less than 50 percent, but strong shearing stress conditions are required in the ARB processing process, and a lubricant cannot be used, so that the service life of the roller is not favorable.
(4) Torsion extrusion: beygelzime et al teach this process. The method also adopts a forming technology of thinning crystal grains through shearing deformation, and the columnar blank is extruded through a torsion die, so that the method has the similar problem of uneven deformation as HPT, and the effect of thinning the crystal grains is lower than that of ECAP and HPT.
(5) Multidirectional forging: the process changes the free forging direction through multiple orthogonal operations to obtain large deformation. The grain refining effect of such deformation is significantly lower than that of ECAP and HPT.
In addition, types of existing processing technical schemes include a derivation method, a basic forming principle is the same as the method, a plurality of SPD forming new technologies are derived, the methods try to simplify tool design, reduce energy consumption, improve yield, improve workpiece size, upgrade automation degree and the like, wherein the methods comprise the following steps:
(1) ECAP derivatization method: repeated bending and straightening (RCS), wherein the blank is placed between the bending devices, moves downwards along with the upper die, is bent and becomes wavy; the material structure is then refined by straightening with 2 plates and bending again, with repeated iterations, accumulating sufficient deformation without significantly changing the dimensions of the blank.
(2) A Cyclic Closed Die Forging (CCDF) is disclosed, the die consisting of a lower die having a cavity of a certain cross-section and punches of the same cross-section moving vertically within the cavity.A fully lubricated sample with graphite lubricant is placed into the lower die, heated to degrees.A workpiece is pressed into the lower die by the punches, removed, rotated 90 degrees about the Z axis in the same direction, reinserted into the lower die to deform in such a way that the workpiece is rotated 90 degrees about the Z axis between successive passes in such a way that it is subjected to 1,3 and 5 compressions, respectively.
(3) The method comprises the steps of reciprocating extrusion (CEC), wherein a die comprises two die cavities, compression belts and punches placed in the two die cavities, the cross sections of the two die cavities are equal, the two die cavities are connected through the middle compression belt on the same axes, a sample reaches the compression belts under the action of the punches in the extrusion process, the sample is extruded and deformed positively, an extruded workpiece is subjected to upsetting deformation under the action of the punches of another die cavities, then, the other punches press the workpiece back in the reverse direction according to the process, extrusion cycles are completed, and the process is repeated until the required strain is obtained.
(4) The plate is sent into a die cavity, the plate is strongly shaped and deformed at the corner of the die cavity, and is extruded out from the other side of the die cavity, a groove is processed on the surface of a feeding roller to increase friction force, and the plate can be repeatedly shaped and deformed for multiple times in the same die due to the characteristic that the cross section area of the material is not changed before and after deformation.
(5) The invented method uses the particularity of circular and elliptical shapes, and its cavity has no sharp corner region, so that the metal is easy to flow, and it can implement the combination of various deformation modes in times of technological processes.
(6) Continuous Friction Angle Extrusion (CFAE), the drive roller rotates and applies pressure P to the workpiece against its support, an th extrusion pass is formed between the drive roller and the workpiece support, the second pass is a short slot in a stationary die assembly, the sheet workpiece is processed to eight times with a maximum equivalent true strain of 5.3, and the sheet orientation remains constant at all times.
HPT derived method is applied to high pressure torsion (HPTT) of a pipe, the pipe being located within a rigid disk, a mandrel placed within the pipe and compressed in its elastic state by a compressor, the expansion being limited by the pipe and disk due to axial compression of the mandrel, expansion being limited by the axial compression of the mandrel, creating large hydrostatic stresses in the pipe, creating large frictional forces on both sides of the pipe.
The TE-derived processes, ultra-high torsion (STS), localize the Torsional Strain (TS) region by making this region less resistant to deformation than the other two parts by localized heating and cooling, at the same time as the TS region is created, the rod moves along the longitudinal axis, thus continuously creating an ultra-large plastic strain throughout the rod.
The patent reports of titanium alloy ultrafine crystal process at home and abroad are relatively less, the Zhongnan university national ministry of sciences et al in a patent [ CN 103014574A ] mention a preparation method of TC18 ultrafine crystal titanium alloys, wherein mention is made of detailed heat treatment and ultrafine crystal process parameters of multi-pass upsetting, the process adopts a multi-direction upsetting mode for deformation, belongs to a traditional forging method, and because the range and penetration depth of a single-pass deformation zone are smaller, in order to obtain an ultrafine crystal structure, generally needs more than 8-10 passes of repeated deformation, the cycle is long, the efficiency is low, and generally has obvious nonuniform deformation.
The Wangliqiang et al of Shanghai university of traffic mentioned a method for preparing ultrafine grained Ti-based composite material by deformation of equal-diameter curved channel, and the introduction of this patent background suggested that although severe plastic deformation could be repeated, the size after deformation was 10X 10X 100mm, which is difficult to satisfy the industrial demand.
The patent (CN 107030111A) by Hei Hua of northeast university mentions a preparation method of ultrafine crystal TC4 titanium alloy plates with equal thickness, the method is similar to the cumulative rolling in the introduction of the patent background, the process needs strong shearing stress conditions, the load is large, the size condition is greatly limited, only the plates can be prepared, and the bars cannot be prepared.
The comprehensive analysis shows that: the titanium alloy ultrafine grain process mentioned in the existing patent or paper adopts the traditional methods of HPT, ECAP, ARB and the like to prepare small-sized uniform ultrafine grain materials under extremely high load, is only limited to be developed in laboratories at present, and is difficult to prepare industrial-grade large-sized materials with integral ultrafine grains.
Disclosure of Invention
The invention aims to provide equidistant rolling methods for spiral conical rollers of large-size titanium alloy ultrafine-grained bars, so as to solve the problems of limited size, large load, low efficiency and the like in the background art.
The invention discloses an equidistant rolling method of spiral conical rollers for large-size titanium alloy ultrafine crystal bars, which comprises the following steps:
s1: selecting a titanium alloy blank with the diameter dimension D of 40-150mm and the length of 300-5000 mm;
s2: placing the titanium alloy blank in a heating furnace, heating to 800-1120 ℃, wherein the heating time is as follows: the diameter Dx (0.6-0.8) of the titanium alloy blank is min;
s3: transferring the heated titanium alloy blank from the heating furnace into a guide chute of a skew rolling mill for 5-20 s;
s4, feeding materials in a guide chute of the skew rolling mill, feeding the titanium alloy blank into a deformation zone between an inlet and an outlet of the skew rolling mill, spirally moving the titanium alloy blank in the deformation zone until the deformation is finished to obtain a TC18 titanium alloy bar material with the diameter Dm, wherein m is the rolling frequency, the diameter of the TC18 titanium alloy bar material obtained by times of rolling is D1, the diameter of the TC18 titanium alloy bar material obtained by twice rolling is D2, and the like;
s5: repeating the steps S2-S4, and carrying out 2-8 times of spiral rolling on the titanium alloy blank to obtain a TC18 titanium alloy integral superfine crystal bar;
the skew rolling mill is a two-roller skew rolling mill, the rollers are single-tapered rollers, spiral grooves are formed in the rollers, the screwing direction of the spiral grooves is the same as that of the titanium alloy blank in the rolling process, the taper angle gamma 1 is 17-19 degrees, the radius r of an arc formed by the rollers when the rollers bite into the titanium alloy blank is 60-400mm, the feeding angle α of the rollers is 19-21 degrees, the rolling angle β of the rollers is 17-19 degrees, the roller distance Dg between the two rollers is 87% -95% of the diameter D of the titanium alloy blank, and the rotating speed n of the rollers is 30-55 r/min;
the titanium alloy blank is a large-size TC18 titanium alloy bar;
and in the step S5, the heating time of the repeated rolling process is TC18 titanium alloy bar diameter Dm x (0.3-0.4) min.
Preferably, the small end surface of the roller is arranged to be a circular arc surface, and the radius of the circular arc surface is 60-400 mm.
Preferably, the pass ovality factor is the guide plate distance DdAnd the ratio of the roll spacing Dg to the pass ovality coefficient of 1.25-1.4 is adopted for rolling the titanium alloy blank in the deformation zone in the step S4.
Preferably, in the rolling process of the titanium alloy blank, the roll distance Dg between the two rolls is fixed, which is beneficial to realizing multi-pass repeated rolling.
Preferably, the pitch iota of the spiral rolling groove is 6-15 mm, and the tooth height h is 6-15 mm.
Preferably, the shape of the deformed region is maintained during the repeated rolling at step S5.
Compared with the prior art, the invention has the beneficial effects that:
(1) the method comprises the following steps of (1) carrying out cross rolling on a high-temperature alloy blank, wherein a deformation area is large in penetration depth and capable of obtaining a large-size integral ultrafine grain structure, plastic deformation in the material during cross rolling consists of two parts, is compression deformation between rollers, the deformation is periodic discontinuous deformation, and parts are continuously torsional deformation, wherein the superposition of the compression deformation and the torsional deformation enables three-dimensional severe plastic deformation which is obviously different from conventional forging to be generated in the deformation area during the cross rolling process, (2) the diameter of the bar before and after the cross rolling is kept unchanged, the bar can be repeatedly rolled for multiple times, the width expansion exists during the cross rolling process, and the equivalent diameter in the cross section of the high-temperature alloy blank is kept unchanged, (3) continuously stabilizing local deformation, the rolling load is small, the deformation process is stable, the actual contact area of a workpiece and the high-temperature alloy blank in the cross rolling process is only a very small part of the surface area of the high-temperature alloy blank, and is local contact.
Drawings
FIG. 1 is a schematic view of a roll of the present invention.
FIG. 2 is a schematic diagram of original structure grains.
FIG. 3 is a schematic diagram of the number of rolling passes of according to an embodiment of the present invention as 2.
FIG. 4 is a schematic diagram of the number of rolling times of according to the embodiment of the present invention being 6.
FIG. 5 shows the relative positions of the dies during skew rolling according to the present invention.
FIG. 6 is a top view of the relative positions of the dies during skew rolling in accordance with the present invention.
FIG. 7 is a left side view of the relative positions of the dies during cross-piercing in accordance with the present invention.
FIG. 8 is a schematic view of the deformation zone of the skew rolling process of the present invention.
Reference numerals: 1-roller, 2-titanium alloy blank and 3-guide plate.
Detailed Description
The invention discloses an equidistant rolling method of spiral conical rollers for large-size titanium alloy ultrafine crystal bars, which comprises the following steps:
s1: selecting a titanium alloy blank 2 with the diameter dimension D of 40-150mm and the length of 300-5000 mm;
s2: placing the titanium alloy blank 2 in a heating furnace, heating to 800-1120 ℃, wherein the heating time is as follows: 2, the diameter Dx (0.6-0.8) of the titanium alloy blank is min;
s3: transferring the heated titanium alloy blank 2 from the heating furnace into a guide chute of a skew rolling mill for 5-20 s;
s4, feeding materials in a guide chute of the skew rolling mill, feeding the titanium alloy blank 2 into a deformation zone between an inlet and an outlet of the skew rolling mill, spirally moving the titanium alloy blank 2 in the deformation zone until the deformation is finished to obtain a TC18 titanium alloy bar material with the diameter Dm, wherein m is the rolling frequency, the diameter of the TC18 titanium alloy bar material obtained by times of rolling is D1, the diameter of the TC18 titanium alloy bar material obtained by twice rolling is D2, and the like;
s5: repeating the steps S2-S4, and carrying out 2-8 times of spiral rolling on the titanium alloy blank 2 to obtain a TC18 titanium alloy integral ultrafine grain bar;
the skew rolling mill is a two-roller skew rolling mill, the rollers 1 are single-conical rollers 1, spiral grooves are formed in the rollers 1, the screwing direction of the spiral grooves is the same as that of the titanium alloy blank 2 in the rolling process, the cone angle gamma 1 is 17-19 degrees, the arc radius r of the titanium alloy blank 2 which is gripped by the rollers 1 is 60-400mm, the feeding angle α of the rollers 1 is 19-21 degrees, the rolling angle β of the rollers 1 is 17-19 degrees, the roller distance Dg between the two rollers 1 is 87% -95% of the diameter D of the titanium alloy blank 2, and the rotating speed n of the rollers 1 is 30-55 r/min;
the titanium alloy blank 2 is a large-size TC18 titanium alloy bar;
and in the step S5, the heating time of the repeated rolling process is TC18 titanium alloy bar diameter Dm x (0.3-0.4) min.
The small end surface of the roller 1 is arranged to be an arc surface, and the radius of the arc surface is 60-400 mm.
Pass ovality coefficient as guide plate distance DdAnd the ratio of the roll spacing Dg, the titanium alloy blank 2 is rolled in a deformation zone by adopting a pass ovality coefficient of 1.25-1.4 in the step S4.
In the rolling process of the titanium alloy blank 2, the roll distance Dg between the two rollers 1 is fixed, which is beneficial to realizing multi-pass repeated rolling.
The pitch iota of the spiral rolling groove is 6-15 mm, and the tooth height h is 6-15 mm.
During the repeated rolling in step S5, the deformed zone shape remains unchanged.
The method comprises the steps of forming a roller 1, forming a cylindrical titanium alloy blank 2 into an elliptic cylinder, forming a conical surface on the small end surface of the roller 1, forming a conical surface on the conical surface of the cylindrical titanium alloy blank 2, forming a conical surface on the conical surface of the cylindrical titanium alloy blank 1, forming a cone angle equal to a rolling angle, increasing the length of an outer diameter compression deformation zone to 2 times compared with a common roller 1, accumulating and forming a longer deformation zone than that the common roller, and forming a common roller, so that the conical surface, forming a large plastic deformation zone, accumulating and forming a large plastic deformation.
the method is characterized in that the material processing type is distinguished by recrystallization temperature, hot processing is carried out above the recrystallization temperature, cold processing is carried out below the recrystallization temperature, cold processing is adopted in the prior art for preparing the ultra-fine crystal, and due to insufficient deformation, only small crystal grains can be obtained by dislocation accumulation, but the crystal grains have poor thermal stability and can not be subjected to heat treatment.
Therefore, the method provides practical choices for the industrial preparation of large-size TC18 integral ultrafine crystal bars.
Example :
by adopting the technical parameters, the spiral rolling roller 1 is designed and processed as shown in figure 1;
s1, selecting titanium alloy TC18 as main deformation parameters, wherein the diameter D is 100mm, the length is 800mm, the radius r of a gripping arc of the spiral roller 1 is 60mm, the cone angle gamma 1 of the conical roller is 18 degrees, the feed angle α is 20 degrees, the rolling angle β is 18 degrees, the pitch iota of the spiral roller 1 is 13mm, the tooth height h is 9mm, the distance Dg between the rollers 1 is 88 percent of the blank diameter D, the ovality coefficient is 1.25, and the rotating speed n of the roller 1 is 32 r/min;
s2: heating the titanium alloy cylindrical blank to 850 ℃ in a heating furnace for 80 minutes;
s3: transferring the blank heated to the temperature from the heating furnace into a guide chute of the skew rolling mill for 10 s;
s4: the blank spirally moves in the deformation zone until the deformation is finished;
and S5, repeated rolling for 2 times and 6 times, sampling and analyzing, wherein the effect on the grain refinement of the titanium alloy is remarkable, the grain size is small, the heating time in the repeated rolling process is TC18 titanium alloy bar diameter Dm x (0.3-0.4) min, m is the rolling frequency, the diameter of the TC18 titanium alloy bar obtained by times of rolling is D1, the rolling is carried out twice, the TC18 titanium alloy bar with the diameter of D1 is adopted as a blank to be rolled again, the diameter of the obtained TC18 titanium alloy bar is D2, and by analogy, the shape of a deformation area is kept unchanged in the repeated rolling process.
Based on the above example, the original structure is shown in fig. 2, wherein β grains are used as main grains, the average size of β grains is 80um, the method of the invention is adopted, fig. 3 is a typical titanium alloy grain diagram with 2 rolling times, wherein the grain size is about 8um, and the grain refinement degree is 90%, fig. 4 is a titanium alloy grain diagram with 6 rolling times, wherein the grain size is about 2.5um, and the grain refinement degree is 96.88%, the working principle is shown in fig. 8, and the position relationship between the roller 1 and the guide plate 3 is shown in fig. 5, 6 and 7.
In conclusion, the constant roll pitch rolling method of the spiral conical roll of the large-size TC18 titanium alloy integral ultrafine crystal bars, provided by the invention, comprises the steps of designing the shape of the spiral conical roll, keeping the roll pitch in a deformation zone unchanged, repeatedly carrying out multi-pass rolling by adopting a pass ellipticity coefficient of an overlarge deformation zone, and gradually accumulating the pass ellipticity coefficient into overlarge plastic deformation, wherein the method can carry out multi-pass spiral rolling, the rolling frequency for different types of titanium alloys is within the range of 2-8, the refining effect for titanium alloy crystal grains is optimal, and the obtained integral ultrafine crystal size is minimum.
The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art should be considered to be within the technical scope of the present invention, and the technical solutions and the inventive concepts thereof according to the present invention should be equivalent or changed within the scope of the present invention.
Claims (5)
1, spiral conical roller equidistant rolling method of large-size titanium alloy ultrafine crystal bar, which is characterized by comprising the following steps:
s1: selecting a titanium alloy blank (2) with the diameter dimension D of 40-150mm and the length of 300-5000 mm;
s2: placing the titanium alloy blank (2) in a heating furnace, and heating to 800-: the diameter Dx (0.6-0.8) of the titanium alloy blank (2) is min;
s3: transferring the heated titanium alloy blank (2) from the heating furnace to a guide chute of a skew rolling mill for 5-20 s;
s4: feeding materials in a guide chute of a skew rolling mill, feeding the titanium alloy blank (2) into a deformation zone between an inlet and an outlet of the skew rolling mill, and performing spiral motion on the titanium alloy blank (2) in the deformation zone until the deformation is finished to obtain a titanium alloy bar with the diameter Dm, wherein m is the rolling frequency;
s5: repeating the steps S2-S4, and carrying out 2-8 times of spiral rolling on the titanium alloy blank (2) to obtain a TC18 titanium alloy whole ultrafine crystal bar;
the skew rolling mill is a two-roller skew rolling mill, the rollers (1) are single tapered rollers (1), spiral grooves are arranged on the rollers (1), the screwing direction of the spiral grooves is the same as the screwing direction of the titanium alloy blank (2) in the rolling process, the cone angle gamma 1 is 17-19 degrees, the arc radius r of the titanium alloy blank (2) which is bitten by the rollers (1) is 60-400mm, the feeding angle α of the rollers (1) is 19-21 degrees, the rolling angle β of the rollers (1) is 17-19 degrees, the roll distance Dg between the two rollers (1) is 87-95% of the diameter D of the titanium alloy blank (2), and the rotating speed n of the rollers (1) is 30-55 r/min;
the titanium alloy blank (2) is a large-size TC18 titanium alloy bar;
the heating time of the repeated rolling process in the step S5 is TC18 titanium alloy bar diameter Dm x (0.3-0.4) min;
in the rolling process of the titanium alloy blank (2), the roll distance Dg between the two rollers (1) is fixed.
2. The method for rolling the large-size ultrafine titanium alloy bars at equal intervals by using the spiral conical rollers as claimed in claim 1, wherein the small end surfaces of the rollers (1) are provided with arc surfaces, and the radius of the arc surfaces is 60-400 mm.
3. The method for equidistantly rolling spiral conical rolls of large-size ultrafine titanium alloy bars according to claim 1, wherein the pass ovality factor is the guide plate distance DdAnd the ratio of the roll spacing Dg to the pass ovality coefficient of 1.25-1.4 is adopted for rolling the titanium alloy blank (2) in the deformation zone in the step S4.
4. The method for rolling the large-size ultrafine titanium alloy bars at equal intervals by using the conical spiral rollers as claimed in claim 1, wherein the pitch l of the spiral grooves is 6-15 mm, and the tooth height h is 6-15 mm.
5. The spiral conical roller equidistant rolling method for kinds of ultra-fine grain bars of large size titanium alloy as claimed in claim 1, wherein the shape of the deformation zone is kept constant during the repeated rolling in S5 steps.
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| CN109909296B (en) * | 2019-02-28 | 2020-04-07 | 西安建筑科技大学 | Reverse-cone spiral roller superfine crystal rolling method for large-size titanium alloy bar |
| CN111441020B (en) * | 2020-04-30 | 2022-05-10 | 西安建筑科技大学 | Method for preparing TC4 titanium alloy sputtering target material at low cost |
| CN112059309B (en) * | 2020-08-26 | 2022-08-19 | 深圳宏友金钻石工具有限公司 | Round equipment is articulated to bar |
| CN115301731B (en) * | 2022-08-12 | 2023-10-31 | 索罗曼(常州)合金新材料有限公司 | Equidistant rolling method for spiral conical rollers of large-size titanium alloy bars |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JPS6054209A (en) * | 1983-08-31 | 1985-03-28 | Kawasaki Steel Corp | Skew rolling mill for manufacturing seamless steel pipe |
| SU1328030A1 (en) * | 1985-08-01 | 1987-08-07 | Предприятие П/Я М-5481 | Method of twisting bar stock |
| JPS6244523A (en) * | 1985-08-20 | 1987-02-26 | Sumitomo Metal Ind Ltd | Manufacture of austenitic stainless steel bar |
| JP3785916B2 (en) * | 2000-10-02 | 2006-06-14 | 住友金属工業株式会社 | Rolling method for seamless metal pipe |
| CN1546715A (en) * | 2003-11-29 | 2004-11-17 | 燕山大学 | Medium and high-carbon steel shaft parts of ultra-fine crystal grain and its production technology |
| DE102007041992B4 (en) * | 2007-09-05 | 2015-02-19 | Kocks Technik Gmbh & Co. Kg | Device for the oblique rolling of tubular or rod-shaped rolling stock |
| DE102012007379B4 (en) * | 2012-04-12 | 2016-12-29 | Zhozef Rotenberg | Process for the cross rolling of cylindrical products |
| CN104971940A (en) * | 2014-04-14 | 2015-10-14 | 西安中泰新材料科技有限公司 | Screw rolling method and screw rolling device for titanium rod |
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Effective date of registration: 20210223 Address after: 401135 No. 618 Liangjiang Avenue, Longxing Town, Yubei District, Chongqing Patentee after: Chongqing lianghang metal material Co.,Ltd. Address before: Beilin District Shaanxi province Xi'an City friendship road 710072 No. 127 Patentee before: Northwestern Polytechnical University |
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Denomination of invention: A spiral cone roller equidistant rolling method for large-sized titanium alloy ultrafine grain bars Granted publication date: 20200131 Pledgee: Chongqing Bank Co.,Ltd. Yuzui Branch Pledgor: Chongqing lianghang metal material Co.,Ltd. Registration number: Y2024500000013 |