CN112725684B - High-damping twinning induced plasticity steel and preparation method thereof - Google Patents
High-damping twinning induced plasticity steel and preparation method thereof Download PDFInfo
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- 238000013016 damping Methods 0.000 title claims abstract description 69
- 229910000937 TWIP steel Inorganic materials 0.000 title claims abstract description 58
- 238000002360 preparation method Methods 0.000 title abstract description 10
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 65
- 239000010959 steel Substances 0.000 claims abstract description 65
- 238000005242 forging Methods 0.000 claims abstract description 41
- 239000000463 material Substances 0.000 claims abstract description 20
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 17
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 17
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- 238000003723 Smelting Methods 0.000 claims abstract description 13
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- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims description 11
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- 238000001816 cooling Methods 0.000 claims description 9
- 229910000592 Ferroniobium Inorganic materials 0.000 claims description 8
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- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/78—Combined heat-treatments not provided for above
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- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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Abstract
The invention discloses a high-damping twinning induced plasticity steel and a preparation method thereof, wherein the formula of the high-damping twinning induced plasticity steel is as follows: according to the mass percentage, 0.02 to 0.2 percent of C, 29 to 31 percent of Mn, 2.8 to 3.0 percent of Al, 2.9 to 3.1 percent of Si, less than or equal to 0.008 percent of P, less than or equal to 0.005 percent of S, 0.15 to 0.3 percent of V, 0.1 to 0.15 percent of Nb, less than or equal to 0.1 percent of impurity and the balance of Fe; according to the formula, the raw materials are smelted, cast into steel ingots after smelting is finished, then forged into forging stocks, then subjected to heat treatment, and then subjected to unidirectional stretching, so that the high-damping twinning-induced plastic steel is prepared. The invention can inhibit the movement of the crystal defects while increasing the density of the crystal defects, thereby improving the damping performance of the material by more than 1 time compared with the traditional twinning induced plasticity steel, and obviously improving the application effect in the fields of shock absorption, buffering and the like.
Description
Technical Field
The invention relates to twinning induced plasticity steelIn particular to high damping twinning induced plasticity steel (the high damping twinning induced plasticity steel means that the internal loss at room temperature is higher than 0.5 multiplied by 10)-2The twinning induced plasticity steel) and a preparation method thereof.
Background
Twinning induced plasticity steel (TWIP steel) is a special single phase austenitic steel. Because a large amount of deformation twin crystals are generated in the plastic elongation process, dislocation is difficult to slide locally along the habit surface, so that deformation is uniformly performed in a large range, and extremely high plasticity is shown. The generation of deformation twins reduces the dislocation mean free path, thereby producing a dynamic Hall-Petch effect, i.e., continuous strain hardening, during plastic deformation, thus exhibiting a very high product of strength and elongation after fracture. The two characteristics enable the TWIP steel to have very outstanding energy absorption capacity, and have very wide application prospects in the fields of buffering, shock absorption, fatigue resistance and the like. Increasing the energy absorption of TWIP steels can be achieved in two ways, namely increasing their strength (including yield strength and tensile strength) and increasing their ductility. However, for most passive vibration damping and noise reduction structures, dissipation of vibrational energy is accomplished over a range of elastic deformation of the material of interest. In order to make the structure have better damping and noise reduction effects, the energy consumption capability of the structural material in the elastic deformation range needs to be improved, namely, the damping is higher. Since the high energy absorption characteristic of TWIP steel can only be exerted after plastic deformation occurs, the damping performance of TWIP steel must be improved to improve its shock absorption and energy consumption capabilities. The improvement of the damping performance not only improves the energy consumption characteristic of the TWIP steel in the elastic deformation range, but also is beneficial to improving the energy absorbed in the whole deformation process from elasticity to plasticity, thereby being popularized and applied in wider fields.
In general, TWIP steel is melted and cast under the protection of inert gas to form a steel ingot, then forged and rolled to form the steel ingot, and finally austenite equiaxial crystals and a small amount of annealing twin crystals are obtained through complete recrystallization annealing.
Disclosure of Invention
Aiming at the defects in the prior art, the invention provides the high-damping twinning induced plasticity steel and the preparation method thereof, which can inhibit the movement of crystal defects while increasing the density of the crystal defects, so that the damping performance of the material is improved by more than 1 time compared with the traditional twinning induced plasticity steel, and the application effect of the twinning induced plasticity steel in the fields of shock absorption, buffering and the like can be obviously improved.
The purpose of the invention is realized by the following technical scheme:
a method for preparing high damping twinning induced plasticity steel comprises the following steps:
(1) preparing materials: the formula of the high-damping twinning induced plasticity steel is as follows: according to the mass percentage, 0.02 to 0.2 percent of C, 29 to 31 percent of Mn, 2.8 to 3.0 percent of Al, 2.9 to 3.1 percent of Si, less than or equal to 0.008 percent of P, less than or equal to 0.005 percent of S, 0.15 to 0.3 percent of V, 0.1 to 0.15 percent of Nb, less than or equal to 0.1 percent of impurity and the balance of Fe; weighing carbon, manganese, aluminum, silicon, iron, ferrovanadium and ferroniobium according to the formula of the high-damping twinning-induced plasticity steel;
(2) smelting: adding the carbon, manganese, aluminum, silicon, iron, ferrovanadium and ferroniobium into a vacuum induction furnace, smelting under the protection of inert gas, and pouring into steel ingots after the smelting is finished;
(3) high-temperature forging and forming: preserving the heat of the steel ingot at 850-1050 ℃ for 3-5 hours, and then forging the steel ingot into a forging stock;
(4) and (3) heat treatment: putting the forging stock or the material rolled by the forging stock into a resistance furnace, heating to 850-1000 ℃, preserving heat for 0.5-4.5 hours, then discharging from the furnace, cooling by water, reheating to 650-750 ℃, preserving heat for 3-6 hours, carrying out aging treatment, and cooling to obtain a twinning induced plastic steel blank;
(5) damping strengthening treatment: and (3) performing unidirectional stretching on the twinning induced plasticity steel blank, and stopping stretching after the stretching strain reaches 20-30%, thereby preparing the high-damping twinning induced plasticity steel.
Preferably, the steel ingot is firstly subjected to steel ingot finishing, and then the steel ingot after the steel ingot finishing is subjected to high-temperature forging forming.
Preferably, the steel ingot finishing is to perform surface turning on the steel ingot, and to cut off a riser, wherein the skin machining amount is 2-5 mm.
Preferably, during the smelting process, the manganese, the aluminum and the silicon are added into the vacuum induction furnace after other raw materials are completely melted down.
Preferably, in the high-temperature forging forming process, the steel ingot is forged one-fire to form a forged blank or the steel ingot is forged multiple-fire to form a forged blank. When the steel ingot is subjected to multi-fire forging, annealing at 850-1050 ℃ for 1-2 hours is performed between every two-fire forging.
Preferably, the material rolled by the forging stock is obtained by heating the forging stock to 1000-1050 ℃, preserving heat for 1-3 hours, then rolling the forging stock to a thin plate with the thickness of 3.0-5.0 mm in a one-fire multi-pass way, and finally rolling the forging stock to a thin plate with the thickness of 0.3-1.5 mm in a multi-pass way at room temperature.
The high-damping twinning induced plasticity steel is prepared by the preparation method of the high-damping twinning induced plasticity steel.
According to the technical scheme provided by the invention, the content of C and the content of Mn in the twinning induced plastic steel are adjusted to form a Cottrell atmosphere (Cottrell atmosphere) with a strong pinning effect, so that the energy consumed during dislocation pinning removal is increased, and meanwhile, trace elements such as V, Nb and the like with a dispersion strengthening effect are added, so that the mobility of a dislocation and a twin crystal interface is further reduced through the pinning effect of dispersion particles. In addition, the invention also improves the dislocation and twin density and makes the configuration and interaction more complicated through proper tensile deformation. Through the measures, the crystal defect density in the structure is increased, the damping sources of the twinning induced plasticity steel are obviously increased, so that the extremely high damping capacity is obtained, the damping performance of the material is improved by more than 1 time compared with the traditional twinning induced plasticity steel, and the application effect of the twinning induced plasticity steel in the fields of shock absorption, buffering and the like can be obviously improved.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings needed to be used in the description of the embodiments are briefly introduced below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and it is obvious for those skilled in the art to obtain other drawings based on the drawings without creative efforts.
FIG. 1 is the internal loss-temperature spectra of samples in different states at 0% tensile strain.
FIG. 2 is the internal loss-temperature spectra of the samples in different states at a tensile strain of 20%.
FIG. 3 is an internal loss-temperature spectrum of samples in different states at a tensile strain of 40%.
FIG. 4 is a typical grain structure diagram of a sample annealed at 1000 ℃ and having a tensile strain of 0%.
FIG. 5 is a typical grain structure of the sample at 1000 ℃ annealing with 20% tensile strain.
FIG. 6 is a typical grain structure of a sample annealed at 1000 ℃ and having a tensile strain of 40%.
Detailed Description
The technical solutions in the embodiments of the present invention are clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments of the present invention without making any creative effort, shall fall within the protection scope of the present invention.
The high damping twinning induced plasticity steel and the preparation method thereof provided by the present invention are described in detail below. Details which are not described in detail in the embodiments of the invention belong to the prior art which is known to the person skilled in the art.
A preparation method of high-damping twinning induced plasticity steel comprises the following steps:
(1) preparing materials: the formula of the high-damping twinning induced plasticity steel is as follows: according to the mass percentage, 0.02 to 0.2 percent of C, 29 to 31 percent of Mn, 2.8 to 3.0 percent of Al, 2.9 to 3.1 percent of Si, less than or equal to 0.008 percent of P, less than or equal to 0.005 percent of S, 0.15 to 0.3 percent of V, 0.1 to 0.15 percent of Nb, less than or equal to 0.1 percent of impurity and the balance of Fe; the impurities are Cr, Mg, Ni and the like. And weighing carbon, manganese, aluminum, silicon, iron, ferrovanadium and ferroniobium according to the formula of the high-damping twinning-induced plasticity steel.
(2) Smelting: adding the carbon, the manganese, the aluminum, the silicon, the iron, the ferrovanadium and the ferroniobium into a vacuum induction furnace, and smelting under the protection of inert gas (such as argon), wherein the manganese, the aluminum and the silicon are added into the vacuum induction furnace after other raw materials are completely melted down, and simultaneously, the power of the vacuum induction furnace is increased to the maximum to ensure that the raw materials are rapidly melted. And casting into steel ingots after the smelting is finished.
(3) Finishing the steel ingot: and turning the surface of the steel ingot, and cutting off a dead head, wherein the processing amount of the surface is 2-5 mm. After the riser is cut off, the material with the thickness of about 25mm is cut off from the top of the adjacent steel ingot.
(4) High-temperature forging and forming: and preserving the heat of the steel ingot after finishing at 850-1050 ℃ for 3-5 hours, forging the steel ingot into a plate blank with the cross section size of 200 x 30mm or a forging blank with other sizes by adopting one-fire forging or multi-fire forging, and naturally cooling to room temperature. When the steel ingot is subjected to multi-fire forging, annealing at 850-1050 ℃ for 1-2 hours is performed between every two-fire forging. The plate blank or forged blank obtained in the step can be directly used or can be used after being rolled, and is subjected to heat treatment and damping strengthening treatment before use.
(5) Sheet rolling and forming: reheating a plate blank with the cross section size of 200 multiplied by 30mm formed by high-temperature forging to 1000-1050 ℃, preserving heat for 1-3 hours, then carrying out one-fire multi-pass rolling to a thin plate with the thickness of 3.0-5.0 mm, and finally carrying out multi-pass rolling at room temperature to a thin plate with the thickness of 0.3-1.5 mm.
(6) And (3) heat treatment: and (3) putting the forged blank processed in the step (4) or the material rolled by the forged blank in the step (5) into a resistance furnace, heating to 850-1000 ℃, preserving heat for 0.5-4.5 hours, then discharging from the furnace, cooling by water, reheating to 650-750 ℃, preserving heat for 3-6 hours, carrying out aging treatment, and then discharging from the furnace, and naturally cooling to obtain the twinning induced plastic steel blank.
(7) Damping strengthening treatment: and (3) performing unidirectional stretching on the twinning induced plasticity steel blank, and stopping stretching after the stretching strain reaches 20-30%, thereby preparing the high-damping twinning induced plasticity steel.
Specifically, the high-damping twinning induced plasticity steel prepared by the invention has the following characteristics:
(1) chemical components: according to the mass percentage, 0.02 to 0.2 percent of C, 29 to 31 percent of Mn, 2.8 to 3.0 percent of Al, 2.9 to 3.1 percent of Si, less than or equal to 0.008 percent of P, less than or equal to 0.005 percent of S, 0.15 to 0.3 percent of V, 0.1 to 0.15 percent of Nb, less than or equal to 0.1 percent of impurity and the balance of Fe; the impurities are Cr, Mg, Ni and the like.
(2) Metallographic structure: the austenite matrix is added with a small amount of dispersed precipitates. The austenite grains are in strip shapes with different sizes, and the long axis of the austenite grains is consistent with the stretching deformation direction.
(3) Typical damping performance: the internal consumption at room temperature is up to 0.0057.
Furthermore, the invention designs the components of the twinning induced plasticity steel, generates a large amount of Coriolis air mass and dispersed particles in the material tissue to reduce the dislocation mobility, increases the dislocation and twin crystal density through room temperature stretching deformation, strengthens the interaction among the dislocation, the crystal boundary and the twin boundary, and inhibits the crystal defect movement while increasing the crystal defect density, thereby generating extremely high damping effect. Compared with the twin induced plasticity steel prepared by the traditional process, the high damping twin induced plasticity steel prepared by the invention improves the damping capacity by more than 1 time, is beneficial to improving the damping and buffering performances of the twin induced plasticity steel structure, and shows more excellent service effect under the vibration or impact condition.
In conclusion, the embodiment of the invention can inhibit the movement of the crystal defects while increasing the density of the crystal defects, thereby improving the damping performance of the material by more than 1 time compared with the traditional twinning induced plasticity steel, and obviously improving the application effect in the fields of shock absorption, buffering and the like.
In order to more clearly show the technical scheme and the technical effects provided by the present invention, the high damping twinning induced plasticity steel and the preparation method thereof provided by the embodiments of the present invention are described in detail with specific embodiments below.
Example 1
A preparation method of high-damping twinning induced plasticity steel comprises the following steps:
(1) preparing materials: the formula of the high-damping twinning induced plasticity steel is as follows: according to the mass percentage, 0.02 to 0.2 percent of C, 29 to 31 percent of Mn, 2.8 to 3.0 percent of Al, 2.9 to 3.1 percent of Si, less than or equal to 0.008 percent of P, less than or equal to 0.005 percent of S, 0.15 to 0.3 percent of V, 0.1 to 0.15 percent of Nb, less than or equal to 0.1 percent of impurity and the balance of Fe; the impurities are Cr, Mg, Ni and the like. Weighing pure carbon (graphite), pure manganese, pure aluminum, pure silicon, pure iron, ferrovanadium and ferroniobium according to the formula of the high-damping twinning-induced plasticity steel.
(2) Smelting: adding the pure carbon (graphite), the pure iron, the ferrovanadium and the ferroniobium into a vacuum induction furnace, smelting under the protection of argon, adding the pure manganese, the pure aluminum and the pure silicon into the vacuum induction furnace after all the raw materials in the vacuum induction furnace are melted, simultaneously increasing the power of the vacuum induction furnace to 200kW, melting down within 10 minutes, and then immediately pouring to form a steel ingot.
(3) Finishing the steel ingot: and turning the surface of the steel ingot, wherein the surface machining amount is 2mm, and cutting off a riser and the top material of the steel ingot adjacent to the riser, wherein the cutting thickness of the top material of the steel ingot is about 25 mm.
(4) High-temperature forging and forming: and (3) preserving the heat of the steel ingot after finishing at 1050 ℃ for 4 hours, forging and drawing according to the forging ratio of 0.4, and forging the steel ingot into a plate blank with the cross section size of 200 multiplied by 30mm by one fire.
(5) Sheet rolling and forming: the slab with the cross section size of 200 multiplied by 30mm formed by high-temperature forging is reheated to 1000 ℃, the temperature is preserved for 3 hours, then the slab is rolled to a thin plate with the thickness of 3.0mm in a multi-pass mode by one fire, and finally the thin plate with the thickness of 1.5mm is rolled in a multi-pass mode at room temperature.
(6) And (3) heat treatment: and (3) putting the sheet with the thickness of 1.5mm processed in the step (5) into a resistance furnace, heating to 1000 ℃, preserving heat for 1 hour, discharging from the furnace, cooling by water, reheating to 650 ℃, preserving heat for 3 hours, carrying out aging treatment, discharging from the furnace, and naturally cooling to obtain the twinning induced plasticity steel blank.
(7) Damping strengthening treatment: and (3) processing the twin induced plastic steel blank after heat treatment into a dumbbell type tensile sample, wherein the length direction of the sample is in the same direction with the axial direction of the forging stock, the gauge length section size is 6 multiplied by 2 multiplied by 60mm, then carrying out unidirectional stretching, and stopping stretching after the tensile strain reaches 20%, thereby preparing the high-damping twin induced plastic steel.
Specifically, the high damping twinning induced plasticity steel prepared in the embodiment 1 of the invention is the twinning induced plasticity steel which is annealed at 1000 ℃ and has the tensile strain of 20%. An internal friction (damping) test sample (with the size of 3 multiplied by 1.5 multiplied by 50mm) is processed from a gauge length section of the high-damping twin induced plastic steel prepared in the embodiment 1 of the invention by adopting a wire cut electrical discharge machining tool, and then an internal friction-temperature spectrum of the internal friction (damping) test sample is tested on a multifunctional internal friction instrument under the conditions of different frequencies and different strain amplitudes, namely the internal friction-temperature spectrum of the sample when the annealing temperature is 1000 ℃ and the tensile strain is 20%. Respectively testing the internal friction-temperature spectrum of the traditional twinning induced plastic steel sample when the rolling state and the tensile strain are 0 percent, the internal friction-temperature spectrum of the traditional twinning induced plastic steel sample when the annealing is carried out at 750 ℃ and the tensile strain is 0 percent, and the internal friction-temperature spectrum of the traditional twinning induced plastic steel sample when the annealing is carried out at 1000 ℃ and the tensile strain is 0 percent according to the internal friction testing method, so that the internal friction-temperature spectrums of the samples in different states when the tensile strain is 0 percent as shown in figure 1 can be obtained; according to the internal friction test method, the internal friction-temperature spectrum of the sample of the embodiment 1 of the invention when the rolling state and the tensile strain are 20%, the internal friction-temperature spectrum of the sample of the embodiment 1 of the invention when the annealing at 750 ℃ and the tensile strain are 20%, and the internal friction-temperature spectrum of the sample of the embodiment 1 of the invention when the annealing at 1000 ℃ and the tensile strain are 20% are respectively tested, so that the internal friction-temperature spectra of the samples in different states when the tensile strain is 20% as shown in FIG. 2 can be obtained; according to the internal friction test method, the internal friction-temperature spectrum of the twin induced plastic steel sample with the same formula as that of the example 1 of the invention when the rolling state and the tensile strain are 40%, the internal friction-temperature spectrum of the twin induced plastic steel sample with the same formula as that of the example 1 of the invention when the annealing is carried out at 750 ℃ and the tensile strain is 40%, and the internal friction-temperature spectrum of the twin induced plastic steel sample with the same formula as that of the example 1 of the invention when the annealing is carried out at 1000 ℃ and the tensile strain is 40% are respectively tested, so that the internal friction-temperature spectra of the samples in different states when the tensile strain is 40% as shown in fig. 3 can be obtained.
Further, a sample is sampled from the sample when the annealing temperature is 1000 ℃ and the tensile strain is 0%, and the structure appearance is observed under a metallographic microscope, so that a typical grain structure diagram of the sample when the annealing temperature is 1000 ℃ and the tensile strain is 0% can be obtained as shown in FIG. 4; sampling the sample when the annealing temperature is 1000 ℃ and the tensile strain is 20%, and observing the structure appearance under a metallographic microscope, thereby obtaining a typical grain structure diagram of the sample when the annealing temperature is 1000 ℃ and the tensile strain is 20% as shown in FIG. 5; the sample is sampled from the sample when the sample is annealed at 1000 ℃ and the tensile strain is 40%, and the structure appearance is observed under a metallographic microscope, so that a typical grain structure diagram of the sample when the sample is annealed at 1000 ℃ and the tensile strain is 40% can be obtained as shown in fig. 6.
As can be seen from fig. 1 and 2: when the tensile strain is 0%, the internal loss of the rolled sample is 0.29X 10 in a temperature range from room temperature to 250 DEG C-2About, the internal loss of the sample is 0.36 multiplied by 10 when the sample is annealed at 1000 DEG C-2Left and right; when the tensile strain is 20%, the internal friction of the rolled sample is increased to 0.37X 10 in a temperature range from room temperature to 250 DEG C-2About, the internal consumption of the sample is improved to 0.57 multiplied by 10 when the sample is annealed at 1000 DEG C-2Left and right; this shows that the damping performance of the twin induced plasticity steel can be obviously improved by more than 1 time by formula adjustment and 20% tensile strain, that is, the damping performance of the high damping twin induced plasticity steel prepared in embodiment 1 of the present invention is improved by more than 1 time compared with the conventional twin induced plasticity steel. As can be seen from fig. 1, 2 and 3: when the tensile strain is 40%, the internal consumption of the rolled sample in the same temperature zone is only 0.26 multiplied by 10-2The internal consumption of the sample annealed at 1000 ℃ is only 0.32 multiplied by 10-2This means that when the tensile strain is too large, the damping properties of the twinning induced plasticity steel are rather degraded, and therefore only by appropriate tensile deformation can the crystal defect configuration be obtained which is advantageous for enhancing the energy consumption, including certain combinations of deformation twins and dislocations. This result is demonstrated by the typical crystal structures shown in fig. 4, 5 and 6. The high-damping twinning-induced plastic steel prepared in the embodiment 1 has higher damping, so that the shock absorption and buffering performance of the related twinning-induced plastic steel structure can be improved, and the steel can be used in vibration or twinningThe service effect is more excellent under the impact condition.
In conclusion, the embodiment of the invention can inhibit the movement of the crystal defects while increasing the density of the crystal defects, thereby improving the damping performance of the material by more than 1 time compared with the traditional twinning induced plasticity steel, and obviously improving the application effect in the fields of shock absorption, buffering and the like.
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 changes or substitutions that can be easily conceived by those skilled in the art within the technical scope of the present invention are included in the scope of the present invention. Therefore, the protection scope of the present invention shall be subject to the protection scope of the claims.
Claims (8)
1. A method for preparing high-damping twinning-induced plasticity steel is characterized by comprising the following steps:
(1) preparing materials: the formula of the high-damping twinning induced plasticity steel is as follows: according to the mass percentage, 0.02 to 0.2 percent of C, 29 to 31 percent of Mn, 2.8 to 3.0 percent of Al, 2.9 to 3.1 percent of Si, less than or equal to 0.008 percent of P, less than or equal to 0.005 percent of S, 0.15 to 0.3 percent of V, 0.1 to 0.15 percent of Nb, less than or equal to 0.1 percent of impurity and the balance of Fe; weighing carbon, manganese, aluminum, silicon, iron, ferrovanadium and ferroniobium according to the formula of the high-damping twinning-induced plasticity steel;
(2) smelting: adding the carbon, manganese, aluminum, silicon, iron, ferrovanadium and ferroniobium into a vacuum induction furnace, smelting under the protection of inert gas, and pouring into steel ingots after the smelting is finished;
(3) high-temperature forging and forming: preserving the heat of the steel ingot at 850-1050 ℃ for 3-5 hours, and then forging the steel ingot into a forging stock;
(4) and (3) heat treatment: putting the forging stock or the material rolled by the forging stock into a resistance furnace, heating to 850-1000 ℃, preserving heat for 0.5-4.5 hours, then discharging from the furnace, cooling by water, reheating to 650-750 ℃, preserving heat for 3-6 hours, carrying out aging treatment, and cooling to obtain a twinning induced plastic steel blank;
(5) damping strengthening treatment: and (3) performing unidirectional stretching on the twinning induced plasticity steel blank, and stopping stretching after the stretching strain reaches 20-30%, thereby preparing the high-damping twinning induced plasticity steel.
2. The method for producing a high-damping twinning induced plasticity steel according to claim 1, wherein the steel ingot is subjected to steel ingot finishing, and then the steel ingot after the steel ingot finishing is subjected to high-temperature forging forming.
3. The method for preparing the high-damping twinning induced plasticity steel according to claim 2, wherein the steel ingot finishing is to perform surface turning on the steel ingot, a dead head is cut off, and the surface machining amount is 2-5 mm.
4. The method for producing a high-damping twinning induced plasticity steel according to any one of claims 1 to 3, wherein the manganese, the aluminum and the silicon are required to be added into a vacuum induction furnace after other raw materials are completely melted down in a melting process.
5. A method of producing a high damping twinning induced plasticity steel as claimed in any one of claims 1 to 3, wherein the ingot is forged on one fire to form a wrought billet or the ingot is forged on multiple fires to form a wrought billet during the high temperature forging forming process.
6. The method for producing a high-damping twinning-induced plastic steel as claimed in claim 5, wherein annealing is performed between each two-fire forging at 850 to 1050 ℃ for 1 to 2 hours when the steel ingot is subjected to the multi-fire forging.
7. The method for preparing a high damping twinning induced plasticity steel as claimed in any one of claims 1 to 3, wherein the material rolled from the forging stock is obtained by heating the forging stock to 1000-1050 ℃, keeping the temperature for 1-3 hours, then rolling the forging stock to a thin plate with the thickness of 3.0-5.0 mm in a multi-pass way by one fire, and finally rolling the forging stock to a thin plate with the thickness of 0.3-1.5 mm in a multi-pass way at room temperature.
8. A high damping twinning induced plasticity steel, characterized by being prepared by the method for preparing the high damping twinning induced plasticity steel according to any one of claims 1 to 7.
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