CN112813294A - High-strength high-elasticity Ni-Cr-Co-W-based alloy wire and preparation method thereof - Google Patents
High-strength high-elasticity Ni-Cr-Co-W-based alloy wire and preparation method thereof Download PDFInfo
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- CN112813294A CN112813294A CN202011609297.3A CN202011609297A CN112813294A CN 112813294 A CN112813294 A CN 112813294A CN 202011609297 A CN202011609297 A CN 202011609297A CN 112813294 A CN112813294 A CN 112813294A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/023—Alloys based on nickel
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/04—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of bars or wire
- B21C37/047—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of bars or wire of fine wires
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
Abstract
The invention relates to the technical field of alloy wire materials, in particular to a high-strength high-elasticity Ni-Cr-Co-W-based alloy wire material and a preparation method thereof. The preparation method comprises the following steps: preparing materials according to the components of the Ni-Cr-Co-W-based alloy, refining and pouring to obtain a remelting electrode rod; carrying out vacuum self-consumption on the remelting electrode bar to obtain an alloy ingot; the ingredients comprise 0.05 to 0.1 percent of Zr by mass percent; homogenizing the alloy ingot, forging to obtain a square ingot blank, and hot-rolling into a wire rod; carrying out solution treatment on the wire rod, and carrying out rounding, peeling and film covering treatment; sequentially drawing and annealing the wire rod for multiple times until alloy wire materials with preset diameters are obtained; the deformation range of each fire is 20-60%, and the deformation of the last fire is 20-40%. The wire material has the advantages that the wire material has strength, elasticity and plasticity and toughness by adopting proper components and matching with the specific drawing deformation, the spring can be smoothly wound on the core rod with the diameter of 1.0mm, and the yield is high.
Description
Technical Field
The invention relates to the technical field of alloy wire materials, in particular to a high-strength high-elasticity Ni-Cr-Co-W-based alloy wire material and a preparation method thereof.
Background
The high-temperature wire spring of the aeroengine is generally selected from GH4169(IN718), GH145(X-750), GH90(Nimonic90), GH738(Waspaloy) and other high-temperature alloys. However, for some special elastic members, such as wire springs in oil lubrication systems, the high temperature alloy cannot meet the use requirements of such elastic members due to insufficient strength or elastic modulus, and therefore, the high temperature alloy with higher strength and high elastic modulus needs to be selected. Aiming at the material requirements of special elastic components of aeroengines, a nickel-chromium-cobalt-based high-temperature alloy with high strength and high elastic modulus has been developed. The alloy adopts a plurality of strengthening measures to combine: high content of W solid solution strengthening, high content of Al and Ti dispersion strengthening and cold deformation strengthening before aging. On the other hand, cold deformation also further promotes precipitation strengthening of the γ' phase during aging. This results in an alloy having a higher room temperature tensile strength and modulus of elasticity than other similar superalloys. Meanwhile, the alloy also has excellent stress relaxation resistance, fatigue strength and corrosion resistance in various corrosive mediums, and is an ideal material for manufacturing high-strength and high-elasticity components. The alloy wire has urgent needs for special elastic members of various types of aeroengines at home and abroad.
However, the alloy has unique metallurgical process and performance, the high alloying degree makes the cold and hot processing and forming of the alloy very difficult, and the process parameters are very sensitive to the performance influence, and the specific details are as follows: 1) the alloy has high alloying degree, large brittleness and narrow hot processing window; 2) the cold working hardening index is large, and the intermediate annealing cracking tendency is severe; 3) the wire is extremely uneven in deformation along the radial direction during cold drawing, so that the tissue distribution is abnormal, namely, the internal normal recrystallized tissue is coated by necklace-shaped fine-grained tissue formed by overlarge deformation of the superficial layer; 4) the cold deformation of the wire in the supply state and the aging process have very complicated influence on the subsequent processing and forming and elastic force of the spring. At present, the alloy wire is not deeply researched, the wire meeting the technical index requirements and the qualified wire spring cannot be smoothly prepared, and the yield is extremely low.
The high-strength and high-elasticity component plays an important role in the safe service of the aero-engine, and belongs to an irreplaceable key component with multiple use models, less use amount, multiple specifications and varieties and high performance requirement. Therefore, the research of the preparation method of the alloy wire with high toughness has very important significance for guaranteeing the manufacture of key equipment, and is a problem to be solved in the field.
In view of the above, the present invention is particularly proposed.
Disclosure of Invention
The first purpose of the invention is to provide a preparation method of a high-strength high-elasticity Ni-Cr-Co-W-based alloy wire, which aims to solve the technical problem that the Ni-Cr-Co-W-based alloy wire in the prior art cannot have high strength and toughness.
The second purpose of the invention is to provide the high-strength high-elasticity Ni-Cr-Co-W-based alloy wire prepared by the preparation method.
In order to achieve the above purpose of the present invention, the following technical solutions are adopted:
the preparation method of the high-strength high-elasticity Ni-Cr-Co-W-based alloy wire comprises the following steps:
(a) preparing materials according to the components of the Ni-Cr-Co-W-based alloy, refining and pouring to obtain a remelting electrode rod; carrying out vacuum self-consumption on the remelting electrode bar to obtain an alloy ingot; wherein, the ingredients comprise 0.05 to 0.1 percent of Zr by mass percent;
(b) homogenizing the alloy ingot, performing heat preservation treatment at 1140-1160 ℃, forging to obtain a square ingot blank of 60-80 mm, heating to 1140-1160 ℃, preserving heat for 1-2 hours, and hot-rolling to form a wire rod with the diameter of 8-12 mm;
(c) carrying out heat preservation treatment on the wire rod at 1050-1140 ℃ for 20-80 min, cooling the wire rod in a furnace to be less than or equal to 600 ℃, and then air-cooling; then rounding, peeling and film covering are carried out;
(d) sequentially drawing and annealing the wire rod processed in the step (c) for multiple times until an alloy wire with a preset diameter is obtained; wherein the deformation range of each heating is 20-60%, and the annealing temperature is 1050-1120 ℃; in the multi-fire drawing, the deformation of the last fire is 20-40%.
The method comprises the steps of proportioning raw materials according to mass percent, then carrying out vacuum induction and vacuum self-consumption duplex smelting, and casting the mixture into an alloy ingot, wherein in consideration of large alloy brittleness and narrow hot processing window, trace element Zr is added during vacuum smelting to improve the crystal boundary strength; forging the alloy ingot blank after homogenization, and then carrying out flaw detection and finishing on the alloy ingot blank and then carrying out hot rolling on the alloy ingot blank to obtain a wire rod with the diameter phi of 8-12 mm; carrying out solution treatment on the wire rod, rounding, peeling and film covering; and sequentially drawing and annealing, and drawing the wire rod to the required diameter of the alloy wire for multiple times to obtain the alloy wire finished product.
The invention carries out specific solution treatment on the wire rod, reduces the residual stress caused by water quenching, coarsens the gamma' precipitated phase and increases the cold drawing plasticity of the alloy.
In a specific embodiment of the invention, the vacuum is self-consumed while helium gas is used for cooling. So as to increase the high-temperature grain boundary strength, reduce element segregation and improve the hot cogging plasticity of the alloy ingot obtained by vacuum self-consumption.
In a specific embodiment of the present invention, the deformation amount of the last fire is 30% to 40%, preferably 38% to 40%.
According to the invention, the final cold deformation of the wire is controlled within the range, the final cold deformation is too large, the strength is high, the plasticity and toughness are poor, the wire cannot be wound, and the final cold deformation is too small, the strength of the wire is low, and the elasticity of the formed spring is insufficient, so that the reasonable final cold deformation is the key point for ensuring the good comprehensive performance of the wire.
In a specific embodiment of the invention, the ingredients comprise the following components in percentage by mass: 18 to 20 percent of Cr, 0.05 to 0.1 percent of Zr, 9 to 10.5 percent of W, 1.3 to 1.8 percent of Al, 2.7 to 3.2 percent of Ti, 5.5 to 6.7 percent of Co, less than or equal to 0.05 percent of C, less than or equal to 0.4 percent of Mn, less than or equal to 0.05 percent of Ce, less than or equal to 0.006 percent of B, and the balance of Ni and inevitable impurities.
In a specific embodiment of the invention, the ingredients comprise the following components in percentage by mass: 18 to 20 percent of Cr, 0.05 to 0.1 percent of Zr, 9 to 10.5 percent of W, 1.3 to 1.8 percent of Al, 2.7 to 3.2 percent of Ti, 5.5 to 6.7 percent of Co, less than or equal to 0.05 percent of C, less than or equal to 0.4 percent of Si, less than or equal to 0.4 percent of Mn, less than or equal to 0.01 percent of S, less than or equal to 0.015 percent of P, less than or equal to 1 percent of Fe, less than or equal to 0.07 percent of Cu, less than or equal to 0.05 percent of Ce, less than or equal to.
In the specific embodiment of the invention, the temperature of the homogenization treatment is 1180-1200 ℃, and the time of the homogenization treatment is 48-72 hours.
In a specific embodiment of the invention, the forging has a finish forging temperature of 1050 ℃ or more.
In a specific embodiment of the invention, the finishing temperature of the hot rolling is more than or equal to 950 ℃.
In a specific embodiment of the present invention, the hot rolling temperature is 950 to 1140 ℃.
In a specific embodiment of the invention, the temperature of refining is 1490-1550 ℃. Further, the refining comprises: refining for 20-40 min under the vacuum degree condition of 0.1-5 Pa, and then refining for 10-20 min under the vacuum degree condition of less than or equal to 0.1 Pa. Specifically, still include: and after the furnace burden is melted down, stirring for 1-3 min under the condition of 100-200 kW.
In the embodiment of the invention, in the step (b), forging is carried out after heat preservation treatment at 1140-1160 ℃ for 0.5-1 h.
In actual operation, the square ingot blank is subjected to flaw detection and finishing treatment, and then hot rolling treatment is performed.
In the specific embodiment of the invention, in the step (d), the annealing heat preservation time is determined according to the diameter of the wire, specifically (3.5-4.5) min/mm × Φ mm, wherein Φ is the diameter of the wire to be annealed.
The invention also provides a high-strength high-elasticity Ni-Cr-Co-W-based alloy wire prepared by the preparation method of any one of the high-strength high-elasticity Ni-Cr-Co-W-based alloy wires.
In an embodiment of the invention, the high-strength and high-elasticity Ni-Cr-Co-W-based alloy wire has a diameter of 0.5 to 1.0mm, preferably 0.75 to 0.85mm, such as 0.8 mm.
In a specific embodiment of the invention, the cold-drawing room-temperature mechanical properties of the high-strength high-elasticity Ni-Cr-Co-W-based alloy wire are as follows: the tensile strength is 1500-2100 MPa; the elongation after fracture is 3.5-9.5%.
The alloy wire prepared by the invention has uniform fine-grain structure, and the average grain size is finer than grade 5. The mechanical property and the process property after cold drawing and aging meet the technical index requirements, the 5-time magnifier does not find out the standard exceeding defect visually, the performance of the finally aged spring component can be effectively ensured, and the technical index requirements of wire springs for aero-engines and the like are met.
Compared with the prior art, the invention has the beneficial effects that:
(1) according to the preparation method of the Ni-Cr-Co-W-based high-temperature alloy wire, the wire has the advantages that the strength, the elasticity and the plasticity and toughness are realized by adopting the proper components and matching with the specific drawing deformation, the spring can be smoothly wound on the core rod with the diameter of 1.0mm, and the yield is high;
(2) the Ni-Cr-Co-W-based high-temperature alloy wire prepared by the preparation method has the advantages of high dimensional precision, good surface quality, uniform components and tissues, excellent mechanical property and process property, high toughness and wide application in the field of processing of high-temperature alloy wires for special elastic members of aircraft engines.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the embodiments or the prior art will be briefly described below, and it is obvious that the drawings in the following description are some embodiments of the present invention, and other drawings can be obtained by those skilled in the art without creative efforts.
FIG. 1 is a drawing of the finished wire of example 1;
FIG. 2 is a graph of the cold-drawn grain structure of the wire of example 1.
Detailed Description
The technical solutions of the present invention will be clearly and completely described below with reference to the accompanying drawings and the detailed description, but those skilled in the art will understand that the following described embodiments are some, not all, of the embodiments of the present invention, and are only used for illustrating the present invention, and should not be construed as limiting the scope of the present invention. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention. The examples, in which specific conditions are not specified, were conducted under conventional conditions or conditions recommended by the manufacturer. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products available commercially.
The preparation method of the high-strength high-elasticity Ni-Cr-Co-W-based alloy wire comprises the following steps:
(a) preparing materials according to the components of the Ni-Cr-Co-W-based alloy, refining and pouring to obtain a remelting electrode rod; carrying out vacuum self-consumption on the remelting electrode bar to obtain an alloy ingot; wherein, the ingredients comprise 0.05 to 0.1 percent of Zr by mass percent;
(b) homogenizing the alloy ingot, performing heat preservation treatment at 1140-1160 ℃, forging to obtain a square ingot blank of 60-80 mm, heating to 1140-1160 ℃, preserving heat for 1-2 hours, and hot-rolling to form a wire rod with the diameter of 8-12 mm;
(c) carrying out heat preservation treatment on the wire rod at 1050-1140 ℃ for 20-80 min, cooling the wire rod in a furnace to be less than or equal to 600 ℃, and then air-cooling; then rounding, peeling and film covering are carried out;
(d) sequentially drawing and annealing the wire rod processed in the step (c) for multiple times until an alloy wire with a preset diameter is obtained; wherein the deformation range of each heating is 20-60%, and the annealing temperature is 1050-1120 ℃; in the multi-fire drawing, the deformation of the last fire is 20-40%.
Wherein the drawing and annealing for a plurality of times comprises: drawing at each fire, annealing after drawing at each fire and final drawing. Namely, except the last drawing, annealing is carried out after each drawing, and the annealing treatment is not carried out after the last drawing, so that the cold-drawn steel is put into use.
According to the invention, a great deal of research shows that for the Ni-Cr-Co-W-based alloy, when the final cold deformation is too small, the strength of the wire after aging is insufficient, and the spring elasticity is insufficient; when the final cold deformation is too large, the wire has high strength but low ductility and toughness, the spring cannot be smoothly wound on the mandrel with the diameter of 1.0mm, and the yield is extremely low.
In the invention, a certain amount of trace element Zr is added during vacuum smelting to improve the crystal boundary strength; and the alloy wire prepared by matching with specific solid solution treatment and multi-train drawing deformation has high toughness and meets the use requirement of a special elastic member.
In the course of the study, when Zr is not added to the Ni-Cr-Co-W-based alloy composition, the alloy has poor thermoplasticity and cannot be hot worked.
In actual operation, when the diameter of the wire rod is larger than or equal to 10mm, the peeling thickness is 1-1.5 mm, and when the diameter of the wire rod is smaller than 10mm, the peeling thickness is smaller than or equal to 0.5 mm.
In a specific embodiment of the invention, the vacuum is self-consumed while helium gas is used for cooling. So as to increase the high-temperature grain boundary strength, reduce element segregation and improve the hot cogging plasticity of the alloy ingot obtained by vacuum self-consumption.
In a specific embodiment of the present invention, the deformation amount of the last fire is 30% to 40%, preferably 38% to 40%.
As in the different embodiments, the number of times of the multi-fire drawing can be 6-8 times.
According to the invention, the final cold deformation of the wire is controlled within the range, the final cold deformation is too large, the strength is high, the plasticity and toughness are poor, the wire cannot be wound, and the final cold deformation is too small, the strength of the wire is low, and the elasticity of the formed spring is insufficient, so that the reasonable final cold deformation is the key point for ensuring the good comprehensive performance of the wire.
In a specific embodiment of the present invention, the deformation amount per fire is in the range of 25% to 60%.
In a specific embodiment of the invention, the ingredients comprise the following components in percentage by mass: 18 to 20 percent of Cr, 0.05 to 0.1 percent of Zr, 9 to 10.5 percent of W, 1.3 to 1.8 percent of Al, 2.7 to 3.2 percent of Ti, 5.5 to 6.7 percent of Co, less than or equal to 0.05 percent of C, less than or equal to 0.4 percent of Mn, less than or equal to 0.05 percent of Ce, less than or equal to 0.006 percent of B, and the balance of Ni and inevitable impurities.
In a specific embodiment of the invention, the ingredients comprise the following components in percentage by mass: 18 to 20 percent of Cr, 0.05 to 0.1 percent of Zr, 9 to 10.5 percent of W, 1.3 to 1.8 percent of Al, 2.7 to 3.2 percent of Ti, 5.5 to 6.7 percent of Co, less than or equal to 0.05 percent of C, less than or equal to 0.4 percent of Si, less than or equal to 0.4 percent of Mn, less than or equal to 0.01 percent of S, less than or equal to 0.015 percent of P, less than or equal to 1 percent of Fe, less than or equal to 0.07 percent of Cu, less than or equal to 0.05 percent of Ce, less than or equal to.
In the specific embodiment of the invention, the temperature of the homogenization treatment is 1180-1200 ℃, and the time of the homogenization treatment is 48-72 hours.
In a specific embodiment of the invention, the forging has a finish forging temperature of 1050 ℃ or more.
In a specific embodiment of the invention, the finishing temperature of the hot rolling is more than or equal to 950 ℃.
In a specific embodiment of the present invention, the hot rolling temperature is 950 to 1140 ℃.
In a specific embodiment of the invention, the temperature of refining is 1490-1550 ℃. Further, the refining comprises: refining for 20-40 min under the vacuum degree condition of 0.1-5 Pa, and then refining for 10-20 min under the vacuum degree condition of less than or equal to 0.1 Pa. Specifically, still include: and after the furnace burden is melted down, stirring for 1-3 min under the condition of 100-200 kW.
In the embodiment of the invention, in the step (b), forging is carried out after heat preservation treatment at 1140-1160 ℃ for 0.5-1 h.
In actual operation, the square ingot blank is subjected to flaw detection and finishing treatment, and then hot rolling treatment is performed.
In the specific embodiment of the invention, in the step (d), the annealing heat preservation time is determined according to the diameter of the wire, specifically (3.5-4.5) min/mm × Φ mm, wherein Φ is the diameter of the wire to be annealed. The holding time for annealing varies depending on the diameter of the wire obtained by each drawing.
The invention also provides a high-strength high-elasticity Ni-Cr-Co-W-based alloy wire prepared by the preparation method of any one of the high-strength high-elasticity Ni-Cr-Co-W-based alloy wires.
In an embodiment of the invention, the high-strength and high-elasticity Ni-Cr-Co-W-based alloy wire has a diameter of 0.5 to 1.0mm, preferably 0.75 to 0.85mm, such as 0.8 mm.
In a specific embodiment of the invention, the cold-drawing room-temperature mechanical properties of the high-strength high-elasticity Ni-Cr-Co-W-based alloy wire are as follows: the tensile strength is 1500-2100 MPa; the elongation after fracture is 3.5-9.5%.
The alloy wire prepared by the invention has uniform fine-grain structure, and the average grain size is finer than grade 5. The mechanical property and the process property after cold drawing and aging meet the technical index requirements, the 5-time magnifier does not find out the standard exceeding defect visually, the performance of the finally aged spring component can be effectively ensured, and the technical index requirements of wire springs for aero-engines and the like are met.
Example 1
The embodiment provides a preparation method of a high-strength high-elasticity Ni-Cr-Co-W-based alloy wire, which comprises the following steps:
(1) preparing materials according to alloy component requirements, wherein the chemical components comprise the following components in percentage by mass: 18.5% of Cr, 1.4% of Al, 2.80% of Ti, 9.5% of W, 6.0% of Co, 0.1% of Mn, 0.02% of C, 0.05% of Ce, 0.003% of B, 0.05% of Zr and the balance of Ni.
(2) Refining the material prepared in the step (1) in a vacuum furnace at 1490-1550 ℃ under the vacuum degree of 1Pa for 20min, and then refining under the vacuum degree of 0.1Pa for 10 min; and after the furnace burden is melted down, electromagnetically stirring for 2min by adopting 100kW power, and pouring at the temperature of 1490 ℃ to obtain the remelting electrode rod.
(3) Carrying out vacuum self-consumption on the remelting electrode bar prepared in the step (2) to obtain an alloy ingot;
(4) and (3) carrying out homogenization treatment on the alloy ingot obtained in the step (3) at 1190 ℃ for 48h, then carrying out heat preservation on the alloy ingot at 1150 ℃ for 1h, then immediately forging, controlling the finish forging temperature to be not less than 1050 ℃, forging to obtain a square billet of 80mm multiplied by l, carrying out flaw detection and finishing, heating the square billet to 1150 ℃, carrying out heat preservation for 80min, immediately taking out of a furnace, and then carrying out hot rolling to obtain a wire rod with the diameter of 12mm, wherein the finish rolling temperature is not less than 950 ℃.
(5) Performing solution treatment on the wire rod obtained in the step (4), specifically, heating the wire rod at 1050 ℃, putting the wire rod into a furnace when the temperature is up to the temperature, keeping the temperature for 30min, cooling the furnace to 600 ℃, and then discharging the wire rod out of the furnace for air cooling;
(6) rounding, peeling and laminating the wire rod subjected to the solution treatment in the step (5), wherein the peeling thickness is 1-1.5 mm;
(7) sequentially drawing and annealing the wire rod processed in the step (6); the specific intermediate annealing temperature and the temperature of the last annealing (the last annealing refers to annealing before last drawing) are both 1050 ℃, the heat preservation time of each annealing is determined according to the diameter of the wire, the heat preservation time of the annealing is 4min/mm, and if the diameter of the wire is 7mm, the heat preservation time of the annealing is 28 min; the specific drawing process is as follows: phi 10mm → phi 7.0mm → phi 5.2mm → phi 3.5mm → phi 2.5mm → phi 1.6mm → phi 1.2mm → phi 1.02mm → phi 0.8mm, the deformation amount of each fire is 51%, 44.8%, 54.7%, 48.9%, 59%, 43.8%, 27.8% and 38.4% in sequence. And (3) annealing and finishing the wire after each fire drawing, wherein the final fire cold deformation is 38.4%, annealing is not performed after the final fire drawing, and the wire is put into use in a cold drawing state.
(8) And (4) carrying out visual inspection on the surface of the finished wire product obtained in the step (7) by using a 5-time magnifying lens.
The high-strength high-elasticity Ni-Cr-Co-based alloy wire prepared by the embodiment has good surface quality and does not have overproof defects such as cracks, pull marks and the like. The diameter is 0.8mm, the size precision is +/-0.001 mm, and the ovality is less than or equal to 0.01 mm.
Example 2
The embodiment provides a preparation method of a high-strength high-elasticity Ni-Cr-Co-W-based alloy wire, which comprises the following steps:
(1) preparing materials according to alloy component requirements, wherein the chemical components comprise the following components in percentage by mass: 19.5% of Cr, 1.8% of Al, 3.20% of Ti, 10.0% of W, 6.5% of Co, 0.2% of Mn, 0.04% of C, 0.05% of Ce, 0.003% of B, 0.1% of Zr and the balance of Ni.
(2) Refining the material prepared in the step (1) in a vacuum furnace at 1490-1550 ℃ and 2Pa for 40min, and then refining at 0.008Pa for 20 min; and after the furnace burden is melted down, electromagnetically stirring for 3min by adopting 200kW power, and pouring at the temperature of 1550 ℃ to obtain the remelting electrode rod.
(3) Carrying out vacuum self-consumption on the remelting electrode bar prepared in the step (2) to obtain an alloy ingot;
(4) and (3) carrying out homogenization treatment on the alloy ingot obtained in the step (3) at 1190 ℃ for 72h, then carrying out heat preservation on the alloy ingot at 1150 ℃ for 1h, then immediately forging, controlling the finish forging temperature to be not less than 1050 ℃, forging to obtain a 60mm multiplied by l square billet, carrying out flaw detection and finishing, heating the square billet to 1150 ℃, carrying out heat preservation for 80min, immediately taking out of a furnace, and then carrying out hot rolling to obtain a wire rod with the diameter of 8mm, wherein the finish rolling temperature is not less than 950 ℃.
(5) Carrying out solution treatment on the wire rod obtained in the step (4), specifically, heating the wire rod to 1120 ℃, putting the wire rod into a furnace when the temperature is up to the temperature, keeping the temperature for 30min, cooling the furnace to 600 ℃, and then discharging the wire rod out of the furnace for air cooling;
(6) rounding, peeling and laminating the wire rod subjected to the solution treatment in the step (5), wherein the peeling thickness is less than or equal to 0.5 mm;
(7) drawing and annealing the wire rod processed in the step (6) in sequence, wherein the specific intermediate annealing temperature and the temperature of the last annealing (the last annealing refers to the annealing before the last drawing) are 1120 ℃, and the heat preservation time of the annealing is determined according to the diameter of the wire material and is 4 min/mm; the specific drawing process is as follows: phi 8mm → phi 5.5mm → phi 3.8mm → phi 2.5mm → phi 1.6mm → phi 1.03mm → phi 0.8mm, the deformation amount of each fire is 52.7%, 52.2%, 56.7%, 59%, 58.5% and 39.6% in sequence. And (3) annealing and finishing the wire after drawing at each fire, wherein the cold deformation of the last fire is 39.6%, annealing is not performed after drawing at the last fire, and the wire is put into use in a cold-drawn state.
(8) And (4) carrying out visual inspection on the surface of the finished wire product obtained in the step (7) by using a 5-time magnifying lens.
The high-strength high-elasticity Ni-Cr-Co-based alloy wire prepared by the embodiment has good surface quality and does not have overproof defects such as cracks, pull marks and the like. The diameter is 0.79mm, the dimensional accuracy is +/-0.001 mm, and the ovality is less than or equal to 0.01 mm.
Comparative example 1
Comparative example 1 the preparation of example 2 was followed with the following exceptions: in the step (7), the specific drawing process is as follows: phi 8mm → phi 5.5mm → phi 3.8mm → phi 2.5mm → phi 1.8mm → phi 1.3mm → phi 0.88mm → phi 0.81mm, the deformation amount of each heat is 52.7%, 52.2%, 56.7%, 48.2%, 47.8%, 54.2% and 15.3% in sequence. The final heat secondary cold deformation amount is 15.3%.
Comparative example 2
Comparative example 2 the preparation of example 2 was referenced, differing only in that: in the step (7), the specific drawing process is as follows: phi 8mm → phi 5.5mm → phi 3.8mm → phi 2.5mm → phi 1.6mm → phi 1.12mm → phi 0.82mm, the deformation amount of each fire is 52.7%, 52.2%, 56.7%, 59%, 51.0% and 46.4% in sequence. The final heat secondary cold deformation amount was 46.4%.
Experimental example 1
The mechanical properties of the alloy wires obtained in examples 1 and 2 of the present invention and comparative examples 1 and 2 were measured in a cold-drawn state and in an aging state according to a schedule (800. + -. 10 ℃ C.. times.1 hours, 700. + -. 10 ℃ C.. times.2 hours, air-cooled), and the results are shown in Table 1.
TABLE 1 test results of room temperature mechanical properties of different alloy wire materials
Remarking: in Table 1, two sets of mechanical property test results of examples 1 to 2 and comparative examples 1 to 2 are obtained from the same wire material by repeated sampling twice; actual measurement in the index requirements means that no specific index requirements exist, and comparison is performed according to actual measurement results.
The finished wire of example 1 had a grain size of grade 6.5 after standard aging. FIG. 1 is a drawing of a finished wire of example 1, and FIG. 2 is a drawing of a cold-drawn grain structure of the wire of example 1. The finished wire of example 2 had a grain size of grade 5.0 after standard aging.
Finally, it should be noted that: the above embodiments are only used to illustrate the technical solution of the present invention, and not to limit the same; while the invention has been described in detail and with reference to the foregoing embodiments, it will be understood by those skilled in the art that: the technical solutions described in the foregoing embodiments may still be modified, or some or all of the technical features may be equivalently replaced; and the modifications or the substitutions do not make the essence of the corresponding technical solutions depart from the scope of the technical solutions of the embodiments of the present invention.
Claims (10)
1. The preparation method of the high-strength high-elasticity Ni-Cr-Co-W-based alloy wire is characterized by comprising the following steps of:
(a) preparing materials according to the components of the Ni-Cr-Co-W-based alloy, refining and pouring to obtain a remelting electrode rod; carrying out vacuum self-consumption on the remelting electrode bar to obtain an alloy ingot; wherein, the ingredients comprise 0.05 to 0.1 percent of Zr by mass percent;
(b) homogenizing the alloy ingot, performing heat preservation treatment at 1140-1160 ℃, forging to obtain a square ingot blank of 60-80 mm, heating to 1140-1160 ℃, preserving heat for 1-2 hours, and hot-rolling to form a wire rod with the diameter of 8-12 mm;
(c) carrying out heat preservation treatment on the wire rod at 1050-1140 ℃ for 20-80 min, cooling the wire rod in a furnace to be less than or equal to 600 ℃, and then air-cooling; then rounding, peeling and film covering are carried out;
(d) sequentially drawing and annealing the wire rod processed in the step (c) for multiple times until an alloy wire with a preset diameter is obtained; wherein the deformation range of each heating is 20-60%, and the annealing temperature is 1050-1120 ℃; in the multi-fire drawing, the deformation of the last fire is 20-40%.
2. The method for preparing the high-strength high-elasticity Ni-Cr-Co-W-based alloy wire material according to claim 1, wherein in the multi-fire drawing, the deformation of the last fire is 30-40%;
preferably, the final heat deflection is 38-40%.
3. The method for preparing the high-strength high-elasticity Ni-Cr-Co-W-based alloy wire according to claim 1, wherein the ingredients comprise the following components in percentage by mass: 18 to 20 percent of Cr, 0.05 to 0.1 percent of Zr, 9 to 10.5 percent of W, 1.3 to 1.8 percent of Al, 2.7 to 3.2 percent of Ti, 5.5 to 6.7 percent of Co, less than or equal to 0.05 percent of C, less than or equal to 0.4 percent of Mn, less than or equal to 0.05 percent of Ce, less than or equal to 0.006 percent of B, and the balance of Ni and inevitable impurities;
preferably, the ingredients comprise the following components in percentage by mass: 18 to 20 percent of Cr, 0.05 to 0.1 percent of Zr, 9 to 10.5 percent of W, 1.3 to 1.8 percent of Al, 2.7 to 3.2 percent of Ti, 5.5 to 6.7 percent of Co, less than or equal to 0.05 percent of C, less than or equal to 0.4 percent of Si, less than or equal to 0.4 percent of Mn, less than or equal to 0.01 percent of S, less than or equal to 0.015 percent of P, less than or equal to 1 percent of Fe, less than or equal to 0.07 percent of Cu, less than or equal to 0.05 percent of Ce, less than or equal to.
4. The method for preparing the high-strength high-elasticity Ni-Cr-Co-W-based alloy wire according to claim 1, wherein the homogenization treatment temperature is 1180-1200 ℃, and the homogenization treatment time is 48-72 hours.
5. The method for preparing the high-strength high-elasticity Ni-Cr-Co-W-based alloy wire material according to claim 1, wherein the final forging temperature of the forging is not less than 1050 ℃; the final rolling temperature of the hot rolling is more than or equal to 950 ℃;
preferably, the hot rolling temperature is 950-1140 ℃.
6. The method for preparing the high-strength high-elasticity Ni-Cr-Co-W-based alloy wire according to claim 1, wherein the refining temperature is 1490-1550 ℃;
preferably, the refining comprises: refining for 20-40 min under the vacuum degree condition of 0.1-5 Pa, and then refining for 10-20 min under the vacuum degree condition of less than or equal to 0.1 Pa;
preferably, the refining further comprises: and after the furnace burden is melted down, stirring for 1-3 min under the condition of 100-200 kW.
7. The method for preparing a high-strength high-elasticity Ni-Cr-Co-W-based alloy wire material as claimed in claim 1, wherein in the step (b), forging is carried out after heat preservation treatment at 1140-1160 ℃ for 0.5-1 h.
8. A high-strength high-resilience Ni-Cr-Co-W-based alloy wire produced by the method for producing a high-strength high-resilience Ni-Cr-Co-W-based alloy wire according to any one of claims 1 to 7.
9. The high-strength high-resilience Ni-Cr-Co-W-based alloy wire according to claim 8, wherein the high-strength high-resilience Ni-Cr-Co-W-based alloy wire has a diameter of 0.5 to 1.0 mm;
preferably, the diameter of the high-strength high-elasticity Ni-Cr-Co-W-based alloy wire is 0.75-0.85 mm.
10. The high-strength high-elasticity Ni-Cr-Co-W-based alloy wire according to claim 8, wherein the high-strength high-elasticity Ni-Cr-Co-W-based alloy wire has cold-drawn room temperature mechanical properties of: the tensile strength is 1500-2100 MPa; the elongation after fracture is 3.5-9.5%.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN117187668A (en) * | 2023-09-22 | 2023-12-08 | 西安钢研功能材料股份有限公司 | Preparation method of high-strength high-elasticity alloy wire |
| CN117187668B (en) * | 2023-09-22 | 2024-05-14 | 西安钢研功能材料股份有限公司 | Preparation method of high-strength high-elasticity alloy wire |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008144202A (en) * | 2006-12-07 | 2008-06-26 | Daido Steel Co Ltd | Heat-resistant spring and manufacturing method therefor |
| CN105483448A (en) * | 2015-12-28 | 2016-04-13 | 钢铁研究总院 | Manufacturing method of nuclear nickel-base high-temperature alloy GH 4145 wire |
| CN106435281A (en) * | 2016-11-11 | 2017-02-22 | 太原钢铁(集团)有限公司 | High-endurance-strength nickel base alloy and preparing method thereof |
| CN109128102A (en) * | 2018-07-19 | 2019-01-04 | 钢铁研究总院 | A kind of high strength and high flexibility nickel base superalloy band and preparation method thereof |
| CN109182844A (en) * | 2018-11-16 | 2019-01-11 | 泰尔重工股份有限公司 | A kind of high temperature alloy metallurgy blade and its manufacturing method |
| US20190232349A1 (en) * | 2016-09-30 | 2019-08-01 | Hitachi Metals, Ltd. | Method of manufacturing ni-based super heat resistant alloy extruded material, and ni-based super heat resistant alloy extruded material |
| CN111826553A (en) * | 2019-04-17 | 2020-10-27 | 江苏图南合金股份有限公司 | Cast high-temperature master alloy and production method thereof |
-
2020
- 2020-12-30 CN CN202011609297.3A patent/CN112813294B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008144202A (en) * | 2006-12-07 | 2008-06-26 | Daido Steel Co Ltd | Heat-resistant spring and manufacturing method therefor |
| CN105483448A (en) * | 2015-12-28 | 2016-04-13 | 钢铁研究总院 | Manufacturing method of nuclear nickel-base high-temperature alloy GH 4145 wire |
| US20190232349A1 (en) * | 2016-09-30 | 2019-08-01 | Hitachi Metals, Ltd. | Method of manufacturing ni-based super heat resistant alloy extruded material, and ni-based super heat resistant alloy extruded material |
| CN106435281A (en) * | 2016-11-11 | 2017-02-22 | 太原钢铁(集团)有限公司 | High-endurance-strength nickel base alloy and preparing method thereof |
| CN109128102A (en) * | 2018-07-19 | 2019-01-04 | 钢铁研究总院 | A kind of high strength and high flexibility nickel base superalloy band and preparation method thereof |
| CN109182844A (en) * | 2018-11-16 | 2019-01-11 | 泰尔重工股份有限公司 | A kind of high temperature alloy metallurgy blade and its manufacturing method |
| CN111826553A (en) * | 2019-04-17 | 2020-10-27 | 江苏图南合金股份有限公司 | Cast high-temperature master alloy and production method thereof |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN117187668A (en) * | 2023-09-22 | 2023-12-08 | 西安钢研功能材料股份有限公司 | Preparation method of high-strength high-elasticity alloy wire |
| CN117187668B (en) * | 2023-09-22 | 2024-05-14 | 西安钢研功能材料股份有限公司 | Preparation method of high-strength high-elasticity alloy wire |
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