CN112746217B - High-strength low-expansion invar alloy wire and manufacturing method thereof - Google Patents
High-strength low-expansion invar alloy wire and manufacturing method thereof Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- 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
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
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- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
Abstract
The invention discloses a high-strength low-expansion invar alloy wire, which comprises the following chemical components in percentage by weight: c:0.41 to 0.60 percent; si: less than or equal to 0.40 percent; mn:0.20 to 0.60 percent; p is less than or equal to 0.02 percent; s is less than or equal to 0.02 percent; ni:35.1 to 37 percent; mo:1.51 to 3.0 percent; v:0.5 to 0.99 percent; co is less than or equal to 1.0 percent; the balance of Fe and inevitable impurities, and the total amount of impurity elements is less than 0.05wt%. The manufacturing method of the wire rod is also provided, the vacuum induction furnace is smelted, the electrode bar is electroslag remelted into a steel ingot, the steel ingot is forged into a square billet, the forged square billet is hot-rolled into a small-sized wire rod, the hot-rolled wire rod is subjected to solution treatment, and the wire rod after bright tempering is drawn into a finished wire rod according to the conventional process. The invention improves the obdurability of the alloy by proper heat treatment and cold drawing processes and depending on carbide strengthening, solid solution strengthening and deformation strengthening, ensures to obtain lower expansion performance, and has low alloy cost and wide application prospect.
Description
Technical Field
The invention relates to the field of invar alloy, and mainly relates to a high-strength low-expansion invar alloy wire and a production method thereof.
Background
The Fe-Ni36 invar alloy is widely regarded and applied because of the good expansion performance, and can be used for manufacturing structural components of precise laser and optical measurement systems, liquefied natural gas storage tanks, long-distance power transmission lines, antenna deformation control equipment, moulds of large aircraft composite materials and the like.
Fe-Ni36 invar plays an important role in different fields due to its unique properties. However, the strength and hardness of the conventional Fe-Ni36 invar alloy are low, which limits the use of the invar alloy as a structural material. In recent years, some high strength invar alloys have been developed, for example, in the power industry, the aluminum-clad steel core used for a double capacity wire is a high strength invar alloy developed by improving the strength of a common Fe-Ni36 invar alloy, and the high strength invar alloy has a small expansion coefficient, can reduce sag when being used as a wire, and can enable the wire to operate at a higher temperature, thereby increasing the amount of power transmission. However, the increase of the expansion coefficient is accompanied with the increase of the strength, so that the improvement of the strength of the alloy under the premise of keeping the expansion coefficient lower is a technically difficult task.
At present, there are two main ways to improve the strength of invar alloy. A method for strengthening Fe-Ni36 alloy by adding Be and Ni3Be intermetallic compound strengthening mechanism features high strengthening effect, high tension strength up to 1500MPa and high expansion coefficient up to 3.5-4X 10 at 20-100 deg.C -6 The martensite phase transition point of the alloy is high/° C, and the alloy is not suitable for use in a low-temperature state. The other method is based on Fe-Ni36 alloy, achieves the purpose of improving the alloy strength by adding C and carbide forming elements, and effectively improves the strength of the alloy (the tensile strength is more than or equal to 1300 MPa) by simultaneously adding a plurality of carbide forming elements at present. Some iron and steel enterprises in Japan adopt the method to produce the high-strength invar alloy, but the cost of the high-strength invar alloy which is industrially applied at present is high, and the wide application of the high-strength invar alloy is also limited.
Disclosure of Invention
Accordingly, an object of the present invention is to provide an invar alloy wire rod having high strength and low expansion. The invention also aims to provide a preparation method of the high-strength low-expansion invar alloy wire rod.
The technical scheme of the invention is that the high-strength low-expansion invar alloy wire comprises the following chemical components in percentage by weight: c:0.41 to 0.60 percent; si: less than or equal to 0.40 percent; mn:0.20 to 0.60 percent; p is less than or equal to 0.02 percent; s is less than or equal to 0.02 percent; ni:35.1 to 37 percent; mo:1.51 to 3.0 percent; v:0.5 to 0.99 percent; co is less than or equal to 1.0 percent;
the balance of Fe and inevitable impurities, and the total amount of impurity elements is less than 0.05wt%.
The reason for selecting the chemical composition range of the alloy steel of the invention is as follows:
c: the increase of the C content can improve the strength of the alloy and simultaneously improve the expansion coefficient of the alloy. C usually exists in the form of interstitial atoms in the iron-nickel invar alloy, and also exists in the form of carbides when carbide forming elements exist in the alloy, and C, mo, V and other strong carbide forming elements in the alloy exist in the form of carbides, so that the strength of the alloy is greatly improved, and meanwhile, the content of Ni corresponding to the minimum expansion coefficient of the alloy can be reduced correspondingly compared with that of Ni in the common Fe-Ni36 by the C existing in the form of interstitial atoms. Therefore, when designing the composition, the alloy is ensured to have sufficient C, wherein a part of C exists in the form of carbide and a part of C exists in the form of interstitial atoms, and the adding amount of C in the alloy is controlled according to the following formula: c% =0.063Mo% +0.2V% + 0.15-0.30%. The preferable composition range is 0.41 to 0.60%, and beyond this range, there is an unsatisfactory strength or expansion coefficient of the alloy.
Si: the alloy is added to play a role in deoxidation, when Si exists in a solid solution state, the strength of a matrix can be improved, but the ductile-brittle transition temperature and the expansion coefficient of the material are improved, the plastic toughness of the alloy is reduced, and the Si content in the alloy is reduced as much as possible under the condition of ensuring good deoxidation of molten steel. Preferably Si is 0.40% or less.
Mn: is both a deoxidizing element and a strengthening element. Mn is an element that can increase the strength of the alloy with minimal detriment to toughness and plasticity. Increasing the Mn content of the alloy increases the strength of the alloy, but higher Mn contents impair the toughness and increase the expansion coefficient of the alloy. For this reason, the Mn content is preferably 0.20 to 0.60%.
Ni: ni is the main element in the invar alloy, and when the Ni content in the iron-nickel invar alloy is about 36 percent, the expansion coefficient is the lowest, and deviates from a certain range, the expansion coefficient of the alloy can be rapidly increased, so the nickel content of the alloy is controlled in a certain range, and the low expansion characteristic of the alloy can be ensured. However, by increasing the C content of the alloy and by suitably reducing the Ni content, a correspondingly lower coefficient of expansion can be obtained. Meanwhile, ni also has the function of stabilizing austenite, and when the content of Ni is lower, martensitic transformation can occur at low temperature, once the martensitic transformation occurs, the expansion coefficient of the alloy can be rapidly increased, and the low-temperature mechanical property is also rapidly deteriorated. Preferably, the Ni content of the alloy is 35.1-37%, and beyond this range, the expansion coefficient of the alloy will not meet the requirement.
Mo: mo is a medium-strength carbide forming element, and is added into the alloy, so that on one hand, the Mo can play a role in stabilizing austenite, on the other hand, mo and C are combined to form Mo2C and Mo6C type carbides, so that the strength of the alloy can be improved, and the Mo content is controlled within the range of 1.51-3.0%.
V: vanadium is a strong carbide forming element, and carbide formed by V and C plays roles of precipitation strengthening and grain refinement, and can improve the strength and plasticity of the alloy, but the ductility and toughness of the alloy can be obviously reduced by too high V. The V and C contents in the alloy can be properly proportioned to exert the best effect. The invention controls the V content in the range of 0.5-0.99%.
Co: the alloy has similar effect with Ni, the content of Ni can be correspondingly reduced by adding Co, the expansion coefficient of the alloy can be favorably reduced by adding a proper amount, and the temperature range of low expansion performance can be expanded by adding Co. However, the price of Co is very high, and the content range of Co is controlled to be less than or equal to 1.0 percent.
P: is an element harmful to toughness, and a compound with a low melting point P can be segregated in a grain boundary, so that the brittleness of the grain boundary is increased, and microcracks can be formed under the action of thermal stress. Therefore, the P content should be controlled as low as possible. The invention controls P to be less than or equal to 0.020%.
S: is a harmful impurity element and can reduce the ductility and toughness of the alloy. S and Mn can form low-melting-point MnS which is segregated in a grain boundary, so that the grain boundary is embrittled, and intergranular cracks are formed under the action of stress. Therefore, the lower the S content in the alloy, the better. The invention controls the S to be less than or equal to 0.020%.
According to the high-strength low-expansion invar alloy wire rod, preferably, the alloy steel comprises the following chemical components in percentage by weight: c:0.41 to 0.60 percent; si: less than or equal to 0.40 percent; mn:0.20 to 0.60 percent; p is less than or equal to 0.02 percent; s is less than or equal to 0.02 percent; ni:36 to 37 percent; mo:1.6 to 3.0 percent; v:0.5 to 0.9 percent; co is less than or equal to 1.0 percent;
the balance of Fe and inevitable impurities, and the total amount of impurity elements is less than 0.05wt%.
According to the high strength low expansion invar alloy wire rod of the present invention, it is preferable that the amount of C added is controlled as follows: c% =0.063Mo% +0.2V% + 0.15-0.30%.
The high-strength low-expansion invar alloy wire rod according to the present invention is preferably one having a tensile strength of 1300MPa or more and A 250 More than or equal to 1.5 percent, and the linear expansion coefficient of between 20 and 230 ℃ is less than or equal to 3.0 multiplied by 10 -6 The linear expansion coefficient of the material is less than or equal to 10.8 multiplied by 10 at the temperature of 230-290 DEG C -6 /℃。
The alloy of the invention has the characteristics of component design:
for Fe-Ni alloys, the corresponding lowest linear expansion coefficient can also be obtained by increasing the C content of the alloy and decreasing the Ni content of the alloy. Therefore, the content of Ni in the alloy is reduced by increasing the content of C in the alloy, and simultaneously carbide forming elements Mo and V are added, so that the aim of reducing the alloy cost is fulfilled while the alloy strength and the lower expansion coefficient are ensured. In order to ensure the strength and low linear expansion coefficient of the alloy, the addition amount of C, mo and V is controlled according to the following formula: c% =0.063Mo% +0.2V% + 0.15-0.30%. While Mo and V form carbide, a certain amount of C needs to be dissolved in the alloy in a solid solution mode. The aim of reducing the Ni content in the alloy is achieved by solid solution of a certain amount of C, so that a correspondingly lower expansion coefficient is obtained.
The steel is formed into a steel ingot by adopting a method of vacuum induction and electroslag remelting or a method of electric furnace and external refining and continuous casting of a square billet or a die cast steel ingot, the steel ingot is forged or hot-rolled into a square billet, the forged or hot-rolled square billet or continuous casting square billet is hot-rolled into a wire rod, and the wire rod is subjected to solution treatment and tempering treatment and then is cold-drawn into a finished wire rod. The said process can reach the best strength and expansion performance indexes. The invention only exemplifies one of the production modes.
The invention also provides a manufacturing method of the high-strength low-expansion invar alloy wire rod,
1) Adding raw materials containing the metal elements and Si, and smelting by a vacuum induction furnace to obtain an alloy with high purity; c is added in the early stage of charging when the high proportion reaches the upper limit of the control specification, namely 0.55-0.60%; when melting, the materials in the crucible are preheated by low power, and vacuum pumping is carried out; refining with high power until the alloy is completely melted, adding Si, V-Fe and other alloys, continuously heating to completely melt down the later added alloys, raising the temperature of the molten steel to 1510-1530 ℃, refining, and reducing the power to 30-40% of rated power when the temperature reaches 1570-1590 ℃ for heat preservation refining; then filling Ar and adding Mn, and melting at high power to ensure that the pressure of Ar exceeds the steam partial pressure of Mn; sampling and analyzing after full melting, tapping after the components are qualified, and casting into an electrode rod;
2) Remelting electrode bar electroslag into steel ingot by adopting quaternary slag system CaF 2 :Al 2 O 3 CaO, mgO =65-80, and further removing S and impurities;
3) Forging the steel ingot into a square billet, heating the steel ingot to 1130-1250 ℃ before hot working, carrying out high-temperature homogenization treatment, and preserving heat; the open forging temperature is more than or equal to 1000 ℃, and the finish forging temperature is more than or equal to 800 ℃;
4) Hot rolling the forged square billet into a small-specification wire rod, wherein the heating temperature of the square billet is controlled to be 1110-1180 ℃, the initial rolling temperature is 1040-1140 ℃, and the final rolling temperature is 800-950 ℃;
5) Carrying out solid solution treatment on the hot-rolled wire rod, wherein the temperature of the solid solution treatment is 800-1150 ℃; tempering treatment is carried out, protective atmosphere is adopted, and the heat treatment process is 450-700 ℃;
6) And drawing the bright tempered wire into a finished wire according to a conventional process.
In the step 1), raw materials such as metal strips and pure iron are required to be clean and free of dirt such as oil stain, rust, dust and the like, so that the deoxidation burden is reduced.
C is added in the early stage of charging to provide sufficient C amount for C-O reaction, and the carbon-oxygen boiling reaction in the melting period can accelerate the removal of gases such as N, O and the like in steel, thereby being beneficial to obtaining high-purity alloy.
The degassing is created by high temperature and high vacuum degree. The high-power electromagnetic stirring strengthens the dynamic conditions of the degassing process, and plays an important role in improving the degassing efficiency in the refining period. Sampling and analyzing components during refining and heat preservation, and carrying out component fine adjustment.
Since metal Mn is easily volatilized in a high vacuum state, metal Mn is added after Ar filling so that the pressure of Ar exceeds the vapor partial pressure of Mn.
The operation of the step 2) can ensure that the alloy with high purity is obtained, and the as-cast structure is uniform and compact, so that the alloy obtains good plasticity and toughness.
Step 3) keeping the temperature for a long enough time to ensure that segregation in the as-cast structure is eliminated, so that the plasticity of the as-cast structure is in the optimal state to prevent hot working cracking
Step 5) the large-particle carbides which are not uniformly distributed can be fully dissolved through solution treatment, the alloy is ensured to be in a soft state, cold drawing processing into a wire rod is facilitated, and meanwhile preparation is made for the carbides to be dispersed and separated out during tempering treatment; and protective atmosphere is adopted during tempering treatment, so that the surface is not oxidized. The carbide can be dispersed and precipitated through tempering, and the alloy is ensured to obtain high strength.
Finally, a large amount of dislocation and substructures are generated inside the alloy through cold-drawing deformation, and crystal grains are obviously refined, so that the strength of the alloy is further improved.
According to the method for manufacturing the high-strength low-expansion invar alloy wire rod of the present invention, it is preferable that the raw materials of step 1) are clean metal Mo strip, metal Ni, metal Mn, metal V, metal Co, crystalline Si, pure iron; adding metal Mn at the later stage;
preferably, when the temperature of the molten steel is increased to 1510-1530 ℃ in the step 1), the refining time is kept for 8-20min;
preferably, the power is reduced to 30-40% of the rated power in the step 1) for heat preservation refining, and the refining time is more than or equal to 60min.
According to the manufacturing method of the high-strength low-expansion invar alloy wire rod, preferably, the melting in the step 1) is preheated by low power, and the low power is 20-30% of rated power; vacuumizing to a vacuum degree of less than or equal to 2.7Pa; the high power is more than 90% of rated power; the continuous heating time is more than 20 min.
Preferably, the quaternary slag system mass ratio CaF in the step 2) 2 :Al 2 O 3 CaO, mgO = 65-80. The slag system ratio refers to a mass ratio.
According to the method for manufacturing the high-strength low-expansion invar alloy wire rod, the heat preservation time in the step 3) is preferably more than or equal to 12 hours. This step is incubated for a sufficient period of time.
According to the method for manufacturing the high-strength low-expansion invar alloy wire rod of the present invention, it is preferable that the protective atmosphere in the step 5) is one or more selected from hydrogen, nitrogen, and argon.
The invention provides a high-strength low-expansion Fe-Ni invar alloy, which reduces the content of an alloy element Ni by increasing the content of C in the alloy, simultaneously adds a proper amount of carbide to form elements Mo and V, and ensures that the alloy not only can keep higher strength and certain elongation percentage, but also has relatively lower linear expansion coefficient through a proper heat treatment process and a cold drawing process, and the performance indexes are as follows: tensile strength is more than or equal to 1300MPa, A250 is more than or equal to 1.5 percent, and linear expansion coefficient is less than or equal to 3.0 multiplied by 10 at the temperature of between 20 and 230 DEG C -6 The linear expansion coefficient of the material is less than or equal to 10.8 multiplied by 10 at the temperature of 230-290 DEG C -6 The temperature per DEG C can completely replace the wire for the double-capacity wire in the current industrial application, and is also suitable for standard measuring tools such as microwave technology, geodetic survey and the like, and the application prospect is wide.
Advantageous effects
Compared with the prior art, the invention has the prominent characteristics and advantages that:
the steel of the invention adopts the Fe-Ni36 alloy as the base, reduces the content of Ni element in the alloy by improving the content of C, properly adds Mo, V and other alloy elements, and keeps the expansion coefficient low while realizing high strength by proper heat treatment and cold drawing processes. By means of carbide strengthening, solid solution strengthening and deformation strengthening, the strength and toughness of the alloy are improved, lower expansion performance is guaranteed, and the alloy cost is low. The double-capacity transmission line can be used for double-capacity transmission lines, is also suitable for standard measuring tools such as microwave technology and geodetic survey, and has wide application prospect.
Detailed Description
The chemical composition and the production method designed according to the invention produce 6-furnace alloy, the specific composition of the alloy is shown in table 2, and the performance test result is shown in table 3.
Example 1:
1) The alloy with higher purity is obtained by smelting in a vacuum induction furnace. C is up to 0.60% high and is added at the early stage of charging. When melting, the material in the crucible is preheated by 20 percent of rated power, and the crucible is vacuumized until the vacuum degree is less than or equal to 2.7Pa. And then increasing the power to more than 90% of the rated power until the alloy is completely melted, adding alloys such as Si, V-Fe and the like, continuously heating for 20min, keeping the refining time for 8min when the alloy is completely melted down and the temperature of the molten steel is increased to T =1530 ℃, and reducing the power to 30% of the rated power for heat preservation and refining when the temperature reaches 1590 ℃, wherein the refining time is 60min. Sampling and analyzing components during refining and heat preservation, carrying out component fine adjustment, adding metal Mn after filling Ar6666Pa, melting by adopting 90% of rated power, sampling and analyzing after full melting, tapping after the components are qualified, and casting into an electrode rod.
2) Electroslag remelting: adopts quaternary slag system CaF 2 :Al 2 O 3 CaO and MgO =69, and the electrode bar is electroslag remelted into a steel ingot.
3) Forging: the ingot was heated to 1250 ℃. The forging temperature is 1100 ℃, the finish forging temperature is 890 ℃, and the steel ingot is forged into a square billet of 160 mm.
4) Hot rolling: hot rolling 160mm square billet into
The heating temperature of the wire rod and the square billet is controlled at 1110 ℃, the initial rolling temperature is 1040 ℃, and the final rolling temperature is 800 ℃.
5) And (3) heat treatment: the hot-rolled wire rod is subjected to solution treatment, and the temperature of the solution treatment is 1150 ℃. The temperature of the bright tempering treatment is 700 ℃, and the nitrogen protective atmosphere is adopted.
6) Drawing the bright-tempered wire into a finished wire according to a conventional process.
Example 2:
1) The alloy with higher purity is obtained by smelting in a vacuum induction furnace. C was made up to 0.55% high and was added at the early stage of charging. When melting, the materials in the crucible are preheated by 25 percent of rated power, and the crucible is vacuumized until the vacuum degree is less than or equal to 2.7Pa. And then increasing the power to more than 90% of the rated power until the alloy is completely melted, adding alloys such as Si, V-Fe and the like, continuing to heat for 20min, keeping the refining time for 15min when the alloy is completely melted down and the temperature of the molten steel is increased to T =1510 ℃, and reducing the power to 40% of the rated power to carry out heat preservation refining when the temperature reaches 1570 ℃, wherein the refining time is 60min. Sampling and analyzing components during refining and heat preservation, carrying out component fine adjustment, adding metal Mn after filling Ar6666Pa, melting by adopting 90% of rated power, sampling and analyzing after full melting, tapping after the components are qualified, and casting into an electrode rod.
2) Electroslag remelting: adopts quaternary slag system CaF 2 :Al 2 O 3 CaO and MgO =76, and electroslag remelting the electrode rod into a steel ingot.
3) Forging: the ingot was heated to 1130 ℃. And the forging temperature is 1000 ℃, the finish forging temperature is 800 ℃, and the steel ingot is forged into a square billet of 160 mm.
4) Hot rolling: hot rolling 160mm square billet into
The heating temperature of the wire rod and the square billet is controlled to be 1130 ℃, the initial rolling temperature is 1050 ℃, and the final rolling temperature is 900 ℃.
5) And (3) heat treatment: the hot-rolled wire rod is subjected to solution treatment, and the temperature of the solution treatment is 800 ℃. The temperature of the bright tempering treatment is 600 ℃, and a nitrogen protective atmosphere is adopted.
6) And drawing the bright tempered wire into a finished wire according to a conventional process.
Example 3:
1) The alloy with higher purity is obtained by smelting in a vacuum induction furnace. C was made up to 0.58% high and was added at the early stage of charging. When melting, the material in the crucible is preheated by 30% of rated power, and the crucible is vacuumized until the vacuum degree is less than or equal to 2.7Pa. And then increasing the power to more than 90% of the rated power until the power is completely melted, then adding alloys such as Si, V-Fe and the like, continuously heating for 20min, when the alloys are completely melted down, increasing the temperature of the molten steel to T =1520 ℃, keeping the refining time for 20min, and when the temperature reaches 1580 ℃, reducing the power to 35% of the rated power, and carrying out heat preservation refining for 60min. Sampling and analyzing components during refining and heat preservation, carrying out component fine adjustment, adding metal Mn after filling Ar6666Pa, melting by adopting 90% of rated power, sampling and analyzing after full melting, tapping after the components are qualified, and casting into an electrode rod.
2) Electroslag remelting: adopts quaternary slag system CaF 2 :Al 2 O 3 CaO, mgO =71, and electroslag remelting of the electrode rod into a steel ingot.
3) Forging: the ingot was heated to 1200 ℃. And forging the steel ingot into a square billet of 160mm at the beginning forging temperature of 1050 ℃ and the end forging temperature of 850 ℃.
4) Hot rolling: hot rolling 160mm square billet into
Heating the wire rod and the square billet at 1180 deg.c, the initial rolling temperature of 1120 deg.c and the final rolling temperature of 950 deg.c.
5) And (3) heat treatment: the hot-rolled wire rod is subjected to solution treatment, and the solution treatment temperature is 1100 ℃. The bright tempering temperature is 450 ℃, and nitrogen protective atmosphere is adopted.
6) And drawing the bright tempered wire into a finished wire according to a conventional process.
Example 4:
1) The alloy with higher purity is obtained by smelting in a vacuum induction furnace. C was made up to 0.55% high and was added at the early stage of charging. When melting, the material in the crucible is preheated by 20 percent of rated power, and the crucible is vacuumized until the vacuum degree is less than or equal to 2.7Pa. And then increasing the power to more than 90% of the rated power until the power is completely melted, adding alloys such as Si, V-Fe and the like, continuously heating for 20min, keeping the refining time for 15min when the alloys are completely melted down and the temperature of the molten steel is increased to T =1520 ℃, and reducing the power to 40% of the rated power for heat preservation and refining when the temperature reaches 1580 ℃, wherein the refining time is 60min. Sampling and analyzing components during refining and heat preservation, carrying out component fine adjustment, adding metal Mn after filling Ar6666Pa, melting by adopting 90% of rated power, sampling and analyzing after full melting, tapping after the components are qualified, and casting into an electrode rod.
2) Electroslag remelting: adopts quaternary slag system CaF 2 :Al 2 O 3 CaO, mgO =72, and electroslag remelting of the electrode rod into a steel ingot.
3) Forging: the ingot was heated to 1180 ℃. And the forging temperature is 1010 ℃, the finish forging temperature is 800 ℃, and the steel ingot is forged into a square billet of 160 mm.
4) Hot rolling: hot rolling 160mm square billet into
The heating temperature of the wire rod and the square billet is controlled at 1110 ℃, the initial rolling temperature is 1040 ℃, and the final rolling temperature is 820 ℃.
5) And (3) heat treatment: the hot-rolled wire rod is subjected to solution treatment, and the solution treatment temperature is 1050 ℃. The temperature of the bright tempering treatment is 660 ℃, and the nitrogen protective atmosphere is adopted.
6) And drawing the bright tempered wire into a finished wire according to a conventional process.
Example 5:
1) The alloy with higher purity is obtained by smelting in a vacuum induction furnace. C is added to 0.60% at the high level in the early stage of charging. When melting, the material in the crucible is preheated by 30% of rated power, and the crucible is vacuumized until the vacuum degree is less than or equal to 2.7Pa. And then increasing the power to more than 90% of the rated power until the power is completely melted, adding alloys such as Si, V-Fe and the like, continuously heating for 20min, keeping the refining time for 10min when the alloys are completely melted down and the temperature of the molten steel is increased to T =1520 ℃, and reducing the power to 40% of the rated power for heat preservation and refining when the temperature reaches 1580 ℃, wherein the refining time is 60min. Sampling and analyzing components during refining and heat preservation, carrying out component fine adjustment, adding metal Mn after filling Ar6666Pa, melting by adopting 90% of rated power, sampling and analyzing after full melting, tapping after the components are qualified, and casting into an electrode rod.
2) Electroslag remelting: adopts quaternary slag system CaF 2 :Al 2 O 3 CaO, mgO =72, and electroslag remelting of the electrode rod into a steel ingot.
3) Forging: the ingot was heated to 1180 ℃. And the forging temperature is 1050 ℃, the finish forging temperature is 810 ℃, and the steel ingot is forged into a square billet of 160 mm.
4) Hot rolling: hot rolling 160mm square billet into
The heating temperature of the wire rod and the square billet is controlled to be 1140 ℃, the initial rolling temperature is 1100 ℃, and the final rolling temperature is 900 ℃.
5) And (3) heat treatment: the hot-rolled wire rod is subjected to solution treatment, and the solution treatment temperature is 1100 ℃. The temperature of the bright tempering treatment is 660 ℃, and the nitrogen protective atmosphere is adopted.
6) And drawing the bright tempered wire into a finished wire according to a conventional process.
Example 6:
1) The alloy with higher purity is obtained by smelting in a vacuum induction furnace. C is added to 0.60% at the high level in the early stage of charging. When melting, the materials in the crucible are preheated by 25 percent of rated power, and the crucible is vacuumized until the vacuum degree is less than or equal to 2.7Pa. And then increasing the power to more than 90% of the rated power until the power is completely melted, then adding alloys such as Si, V-Fe and the like, continuing to heat for 20min, keeping the refining time for 15min when the alloys are completely melted down and the temperature of the molten steel is increased to T =1510 ℃, and reducing the power to 35% of the rated power to carry out heat preservation refining when the temperature reaches 1570 ℃, wherein the refining time is 60min. Sampling and analyzing components during refining and heat preservation, carrying out component fine adjustment, adding metal Mn after filling Ar6666Pa, melting by adopting 90% of rated power, sampling and analyzing after full melting, tapping after the components are qualified, and casting into an electrode rod.
2) Electroslag remelting: adopts quaternary slag system CaF 2 :Al 2 O 3 CaO and MgO =69, and the electrode bar is electroslag remelted into a steel ingot.
3) Forging: the ingot was heated to 1190 ℃. Forging the steel ingot into a square billet of 160mm at the open forging temperature of 1030 ℃ and the finish forging temperature of 820 ℃.
4) Hot rolling: hot rolling 160mm square billet into
The heating temperature of the wire rod and the square billet is controlled to be 1150 ℃, the initial rolling temperature is 1110 ℃, and the final rolling temperature is 905 ℃.
5) And (3) heat treatment: the hot-rolled wire rod is subjected to solution treatment, and the solution treatment temperature is 1050 ℃. The bright tempering temperature is 662 ℃ and nitrogen protective atmosphere is adopted.
6) Drawing the bright-tempered wire into a finished wire according to a conventional process.
TABLE 2 chemical composition of the steel alloys according to the invention, wt.%
| Steel grade | C | Si | Mn | P | S | Ni | Mo | V | Co |
| A1 | 0.45 | 0.40 | 0.33 | 0.017 | 0.020 | 35.2 | 2.2 | 0.73 | 0.5 |
| A2 | 0.55 | 0.25 | 0.40 | 0.016 | 0.012 | 35.6 | 1.52 | 0.82 | 0.8 |
| A3 | 0.49 | 0.32 | 0.29 | 0.020 | 0.018 | 35.0 | 1.6 | 0.98 | 0.2 |
| A4 | 0.60 | 0.10 | 0.60 | 0.007 | 0.005 | 36.0 | 1.9 | 0.90 | 1.0 |
| A5 | 0.48 | 0.20 | 0.55 | 0.009 | 0.011 | 35.5 | 2.3 | 0.68 | 0.4 |
| A6 | 0.41 | 0.19 | 0.20 | 0.005 | 0.008 | 37.0 | 3.0 | 0.50 | 0 |
TABLE 3 Properties of inventive steels
The Fe-Ni invar alloy has higher strength and low expansion coefficient, can be used for a transmission lead with double capacity, is a preferred product for solving the bottleneck of power transmission, is also an urgent product for current power development, is also suitable for standard measuring tools such as microwave technology, geodetic survey and the like, and has wide application prospect.
Claims (8)
1. A high-strength low-expansion invar alloy wire is characterized in that: the alloy steel comprises the following chemical components in percentage by weight: c:0.41 to 0.60 percent; si: less than or equal to 0.40 percent; mn:0.20 to 0.60 percent; p is less than or equal to 0.02 percent; s is less than or equal to 0.02 percent; ni:35.1 to 37 percent; mo:1.51 to 3.0 percent; v:0.5 to 0.99 percent; co is less than or equal to 1.0 percent; the addition of C is controlled according to the following formula: c% =0.063Mo% +0.2V% + 0.15-0.30%;
the balance of Fe and inevitable impurities, and the total amount of impurity elements is less than 0.05wt%; the tensile strength of the high-strength low-expansion invar alloy wire is more than or equal to 1300MPa 250 More than or equal to 1.5 percent, and the linear expansion coefficient of between 20 and 230 ℃ is less than or equal to 3.0 multiplied by 10 -6 Per DEG C, linear expansion coefficient of less than or equal to 10.8 multiplied by 10 at 230-290 DEG C -6 /℃。
2. The high strength low expansion invar alloy wire of claim 1, wherein: the alloy steel comprises the following chemical components in percentage by weight: c:0.41 to 0.60 percent; si: less than or equal to 0.40 percent; mn:0.20 to 0.60 percent; p is less than or equal to 0.02 percent; s is less than or equal to 0.02 percent; ni:36 to 37 percent; mo:1.6 to 3.0 percent; v:0.5 to 0.9 percent; co is less than or equal to 1.0 percent;
the balance of Fe and inevitable impurities, and the total amount of impurity elements is less than 0.05wt%.
3. The method for manufacturing a high-strength low-expansion invar alloy wire according to claim 1, wherein:
1) Adding raw materials containing metal elements of Ni, mo, V and Co and Si, and smelting by a vacuum induction furnace to obtain an alloy with high purity; c is added in the early stage of charging when the high proportion reaches the upper limit of the control specification, namely 0.55-0.60%; when melting, the materials in the crucible are preheated by low power, and vacuum pumping is carried out; refining with high power until the alloy is completely melted, adding Si and V-Fe alloy, continuously heating to completely melt down the alloy added in the later period, raising the temperature of the molten steel to 1510-1530 ℃, refining, and reducing the power to 30-40% of rated power when the temperature reaches 1570-1590 ℃ for heat preservation refining; then filling Ar and adding Mn, and melting at high power to ensure that the pressure of Ar exceeds the steam partial pressure of Mn; after the full melting, sampling and analyzing, tapping after the components are qualified, and casting into an electrode rod; step 1), preheating by using low power during melting, wherein the low power is 20-30% of rated power; the high power is more than 90% of rated power;
2) Remelting electrode bar electroslag into steel ingot by adopting quaternary slag system CaF 2 :Al 2 O 3 CaO, mgO =65-80, and further removing S and impurities;
3) Forging the steel ingot into a square billet, heating the steel ingot to 1130-1250 ℃ before hot working, carrying out high-temperature homogenization treatment, and preserving heat; the open forging temperature is more than or equal to 1000 ℃, and the finish forging temperature is more than or equal to 800 ℃;
4) Hot rolling the forged square billet into a small-specification wire rod, wherein the heating temperature of the square billet is controlled to be 1110-1180 ℃, the initial rolling temperature is 1040-1140 ℃, and the final rolling temperature is 800-950 ℃;
5) Carrying out solid solution treatment on the hot-rolled wire rod, wherein the temperature of the solid solution treatment is 800-1150 ℃; tempering treatment is carried out, protective atmosphere is adopted, and the heat treatment process is 450-700 ℃;
6) And drawing the bright tempered wire into a finished wire according to a conventional process.
4. The method of manufacturing a high-strength low-expansion invar alloy wire according to claim 3, wherein:
when the temperature of the molten steel is increased to 1510-1530 ℃ in the step 1), the refining time is kept for 8-20min;
and (3) reducing the power to 30-40% of the rated power in the step 1) and carrying out heat preservation refining, wherein the refining time is more than or equal to 60min.
5. The method for manufacturing high-strength low-expansion invar alloy wire according to claim 3, wherein: step 1), vacuumizing until the vacuum degree is less than or equal to 2.7Pa; the continuous heating time is more than 20 min.
6. The method for manufacturing high-strength low-expansion invar alloy wire according to claim 3, wherein: step 2) the quaternary slag system mass ratio CaF 2 :Al 2 O 3 :CaO:MgO＝65-80:15-20:4-6:4-6。
7. The method of manufacturing a high-strength low-expansion invar alloy wire according to claim 3, wherein: and 3) the heat preservation time is more than or equal to 12 hours.
8. The method of manufacturing a high-strength low-expansion invar alloy wire according to claim 3, wherein: and 5) selecting the protective atmosphere from one or more of hydrogen, nitrogen and argon.
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