CN116623096A - Invar alloy core material with high torsion performance and preparation method thereof - Google Patents
Invar alloy core material with high torsion performance and preparation method thereof Download PDFInfo
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- 239000000956 alloy Substances 0.000 title claims abstract description 80
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 78
- 229910001374 Invar Inorganic materials 0.000 title claims abstract description 75
- 239000011162 core material Substances 0.000 title claims abstract description 45
- 238000002360 preparation method Methods 0.000 title abstract description 16
- 238000010622 cold drawing Methods 0.000 claims abstract description 40
- 238000000034 method Methods 0.000 claims abstract description 34
- 238000005242 forging Methods 0.000 claims abstract description 31
- 238000005098 hot rolling Methods 0.000 claims abstract description 31
- 238000005728 strengthening Methods 0.000 claims abstract description 19
- 238000003723 Smelting Methods 0.000 claims abstract description 14
- 238000013461 design Methods 0.000 claims abstract description 14
- 238000000265 homogenisation Methods 0.000 claims abstract description 9
- 238000005491 wire drawing Methods 0.000 claims abstract description 5
- 238000005096 rolling process Methods 0.000 claims description 30
- 239000012535 impurity Substances 0.000 claims description 12
- 238000001816 cooling Methods 0.000 claims description 10
- 230000007547 defect Effects 0.000 claims description 9
- 239000002184 metal Substances 0.000 claims description 6
- 229910052751 metal Inorganic materials 0.000 claims description 6
- 238000010438 heat treatment Methods 0.000 claims description 4
- 230000006698 induction Effects 0.000 claims description 4
- 239000000463 material Substances 0.000 claims description 4
- 238000001953 recrystallisation Methods 0.000 claims description 4
- 238000005520 cutting process Methods 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 claims 6
- 230000000052 comparative effect Effects 0.000 description 21
- 229910000881 Cu alloy Inorganic materials 0.000 description 15
- 239000002994 raw material Substances 0.000 description 10
- 239000000203 mixture Substances 0.000 description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 8
- 230000000694 effects Effects 0.000 description 8
- 229910001182 Mo alloy Inorganic materials 0.000 description 7
- 229910000756 V alloy Inorganic materials 0.000 description 3
- 230000005540 biological transmission Effects 0.000 description 3
- 230000008901 benefit Effects 0.000 description 2
- 230000006835 compression Effects 0.000 description 2
- 238000007906 compression Methods 0.000 description 2
- 239000013067 intermediate product Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 1
- 241001062472 Stokellia anisodon Species 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000010923 batch production Methods 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000002372 labelling Methods 0.000 description 1
- 230000001050 lubricating effect Effects 0.000 description 1
- 239000010687 lubricating oil Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052961 molybdenite Inorganic materials 0.000 description 1
- CWQXQMHSOZUFJS-UHFFFAOYSA-N molybdenum disulfide Chemical compound S=[Mo]=S CWQXQMHSOZUFJS-UHFFFAOYSA-N 0.000 description 1
- 229910052982 molybdenum disulfide Inorganic materials 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 229910052709 silver Inorganic materials 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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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
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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
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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Abstract
The invention discloses an invar alloy core material with high torsion performance, which comprises the following components in percentage by weight: c:0.18 to 0.30 percent; mn:0.15 to 0.50 percent; si: less than or equal to 0.30 percent; ni:35.0 to 38.0 percent; cu:0.10 to 0.60 percent, and one or more strengthening elements, wherein the weight percentage is as follows: mo:1.40 to 2.00 percent; nb:0.05 to 0.60 percent; v:0.80 to 1.20 percent. The preparation process of the invar alloy wire comprises the following steps: component design, proportioning, smelting, planing, homogenization treatment, hot forging and hot rolling to obtain a hot rolled wire rod, and scientifically proportioning a wire drawing die by matching with a wire rod cold drawing process, so that the high torsion performance of the invar alloy wire rod can be ensured, and meanwhile, the invar alloy wire rod has better thermal expansion performance.
Description
Technical Field
The invention belongs to the technical field of special material smelting, and relates to an invar alloy core material with high torsion performance and a preparation method thereof.
Background
Invar alloy attracts more importance in fields such as high-capacity flexible power transmission/ultra-high voltage power transmission cables, ultra-high power charging equipment, electronic instruments, automatic control, aerospace and the like due to extremely low thermal expansion performance. High-end core materials represented by double-capacity conductive cables and precision resistance alloys require materials having low thermal expansion rates and high strength properties under service conditions.
The core technology of the double-capacity conductive cable is that invar alloy wires are used as core materials, and the invar alloy wires have the characteristics of low thermal expansion performance, high temperature resistance, good high temperature sag characteristic, long service life and the like, so that iron tower investment can be greatly reduced when long-distance ultra-high voltage transmission cables are constructed, and the cost of each kilometer of line construction can be saved by about 5 ten thousand yuan according to measurement and calculation, so that the double-capacity conductive cable has great economic benefit and social value.
As invar core materials for long-distance power cables are required to have higher strength against the weight of the wires themselves and snow, and sufficient torsion resistance against high winds. The prior art patents have not reported the research on invar alloy wires with high strength and high torsion performance.
According to the invention, a fine-grain strengthening method is adopted, and the temperature, rolling speed and cooling speed in the hot rolling step are controlled mainly by adding carbide forming elements, so that the grain structure is refined, a wire rod which is uniform and stable and has an average grain diameter of less than 2 mu m is obtained, a better wire rod is provided for subsequently improving the performance of the invar alloy wire rod as an intermediate product, and the wire rod is subjected to cold drawing treatment, so that a core material with high torsion performance is obtained.
Disclosure of Invention
The main technical scheme of the invention is to provide an invar alloy material containing one or more strengthening elements, adopting a fine-grain strengthening method, adding carbide forming elements, and controlling the temperature, rolling speed and cooling speed in the hot rolling step to refine the grain structure, thereby obtaining a wire rod with the average grain diameter of less than 2 mu m, the tensile strength of more than or equal to 700Mpa and the diameter of phi 6.5 mm; further, the core material with better torsion performance is obtained by matching with a wire rod cold drawing process.
The technical scheme of the invention is to provide an invar alloy material containing one or more solidification or strengthening elements, further, the solidification and strengthening elements comprise Nb, mo, V, cu and the like, especially Cu is added, so that the performance of the wire rod can be improved, wherein the weight percentage of Cu is as follows: 0.10 to 0.60 percent, preferably, cu is in weight percent: 0.30 to 0.50 percent. Cu, mo, nb, and V are similar to each other and have effects of solid solution strengthening and precipitation strengthening, but complex addition cost, influence on thermal expansion coefficient, influence on wire rod drawing, and influence on core material conductivity need to be comprehensively examined. The invention discovers that the effect of adding Cu in a proper range is better than that of independently adding one element to refine crystal grains and the comprehensive performance.
The invar alloy core material with high torsion performance comprises the following components in percentage by weight: c:0.18 to 0.30 percent; mn:0.15 to 0.50 percent; si: less than or equal to 0.30 percent; ni:35.0 to 38.0 percent; cu:0.10 to 0.60 percent, and one or more strengthening elements selected from the following components in percentage by weight: mo:1.40 to 2.00 percent; nb:0.05 to 0.60 percent; v:0.80 to 1.20 percent; in addition, the balance being Fe and unavoidable impurities.
Preferably, the invar core material with high torsional property comprises the following components in percentage by weight: c:0.20 to 0.28 percent; mn:0.25 to 0.40 percent; si: less than or equal to 0.20 percent; ni:36.0 to 37.8 percent; cu:0.30 to 0.50 percent, and one or more strengthening elements selected from the following components in percentage by weight: mo:1.60 to 1.80 percent; nb:0.10 to 0.30 percent; v:0.90 to 0.98 percent; in addition, the balance being Fe and unavoidable impurities.
Preferably, the invention also provides an invar alloy core material, which comprises the following components in percentage by weight: c:0.20 to 0.28 percent; mn:0.25 to 0.40 percent; si: less than or equal to 0.20 percent; ni:36.0 to 37.8 percent; v:0.90 to 0.98 percent; cu:0.30 to 0.50 percent; the balance being Fe and unavoidable impurities.
Further, the invention also provides an invar alloy core material, which comprises the following components in percentage by weight: c:0.24%; mn:0.31%; si:0.17%; ni:37.5%; v:0.96%; cu:0.32%; the balance being Fe and unavoidable impurities.
Preferably, the invention also provides an invar alloy core material, which comprises the following components in percentage by weight: c:0.20 to 0.28 percent; mn:0.25 to 0.40 percent; si: less than or equal to 0.20 percent; ni:36.0 to 37.8 percent; mo:1.60 to 1.80 percent; cu:0.30 to 0.50 percent; the balance being Fe and unavoidable impurities.
Further, the invention also provides an invar alloy core material, which comprises the following components in percentage by weight: c:0.23%; mn:0.30%; si:0.13%; ni:37.1%; mo:1.7%; cu:0.5%; the balance being Fe and unavoidable impurities.
The invention also provides a preparation process of the invar alloy wire rod, which mainly adopts a vacuum induction furnace to smelt and prepare an invar alloy square ingot, and performs hot forging after planing the square ingot, and then prepares the invar alloy hot-rolled wire rod through hot rolling. The method specifically comprises the following steps: component design, material proportioning, smelting, planing, homogenization treatment, hot forging, hot rolling to obtain a hot rolled wire rod, and cold drawing to obtain a core material.
Preferably, the preparation process of the invar alloy core material comprises the following steps:
s1, designing components;
s2, batching;
s3, smelting: smelting into square ingots by adopting a vacuum induction furnace, and cutting off parts with obvious shrinkage cavities at the head and the tail;
s4, planing: the planing machine is adopted to carry out planing treatment on the side surface to remove the defects of surface shrinkage cavity, oxide skin and the like, so that the influence of the surface defects on the subsequent hot forging and hot rolling process is reduced;
s5, homogenizing: before hot forging, the cast ingot is placed in a furnace to be heated for 2 to 5 hours so as to homogenize the structure;
s6, hot forging: hot forging is carried out within the range of 1100-1200 ℃, and if the temperature is reduced to below 900 ℃ in the hot forging process, the hot forging process should be returned to the furnace again for heating, the surface is polished after the hot forging, and the surface oxide film is removed until no obvious defect exists, and the next hot rolling stage can be carried out;
s7, hot rolling: rolling the metal above the recrystallization temperature;
s8, obtaining a hot rolled wire rod;
s9, cold drawing, wherein the cold drawing comprises three stages, and a core material is obtained.
Further, in the step S5 of homogenizing treatment, the heating time is 2 hours;
further, in the S6 hot forging, the temperature is 1170-1190 ℃;
further, in the S7 hot rolling, the alloy can be completely recrystallized in the deformation process through hot rolling; initial rolling temperature: 1000-1150 ℃ and finishing temperature: 950-1050 ℃; the highest rolling speed is less than or equal to 80m/s, and the cooling speed after rolling is 0.15-0.35 ℃/s;
further, in the S7 hot rolling, the initial rolling temperature: 1050-1100 ℃, finishing temperature: 980-1030 ℃; the highest rolling speed is less than or equal to 68m/s, and the cooling speed after rolling is 0.22 ℃/s;
further, in the S7 hot rolling, the initial rolling temperature: 1060 ℃, finishing temperature: 1000 ℃; the highest rolling speed is less than or equal to 68m/s, and the cooling speed after rolling is 0.22 ℃/s.
Further, the S8 hot rolled wire rod has the following sizePreferably +.>
Further, in the S9 cold drawing, three stages are included:
cold drawing in the first stage, namely, continuously cold drawing the hot rolled wire rod in the first stage through 3-5 wire drawing dies in the room temperature environment, wherein the true strain epsilon of the wire rod is less than or equal to 1.5, the deformation of each pass is 18-25%, and the deformation of the last pass in the first stage is the largest;
cold drawing in the second stage, wherein the true strain epsilon=1.5-2.5 of the wire rod, and the deformation of each pass is between 12-18%;
cold drawing in the third stage, wherein the true strain epsilon=2.5-3.0 of the wire rod, the deformation of each pass is 10-15%, and the deformation of each pass is from large to small;
further, the invar drawing rate is set to 1 to 5mm/s, preferably 2mm/s.
Further, in the S9 cold drawing, the diameter size after cold drawingPreferably phi 1.42mm.
Further, in the S9 cold drawing, the total true strain amount epsilon=2.5 to 3.5, preferably epsilon=3.0.
And carrying out multi-pass cold drawing on the invar alloy wire rod on a single-step drawing machine, adopting a dry drawing method, and lubricating by using MoS2 lubricating oil to obtain invar alloy wires with different strain amounts. In order to ensure that the plastic deformation of the metal is uniform in the wire drawing process, the metal wire is drawn perpendicular to a drawing die. The drawing speed and the compression rate per pass will have a significant impact on the structure and performance of the cold drawn invar wire. Therefore, the drawing rate of the invar alloy is set in the range of 1-5mm/s, and the compression rate of each pass is below 25%, so that the surface temperature of the steel wire is controlled to be not more than 50 ℃ during drawing. Before drawing, the invar alloy wire rod should be sanded to remove surface oxide skin so as to ensure the surface quality of the invar alloy after drawing. The cold drawing mill is schematically shown in fig. 5.
The component design of the invention takes the two aspects of mechanical property and thermal expansion coefficient into consideration. The function of selecting proper Cu as the strengthening element of the invar alloy: (1) the Cu element is added into the invar alloy, so that the Curie temperature of the alloy can be effectively improved, the heat-resistant temperature range of the alloy is enlarged, and the thermal expansion coefficient in the heat-resistant temperature range is reduced; (2) as invar alloy for the cable conductive core material, cu element is added, so that the conductivity of the cable can be further improved; (3) the Cu element can replace a part of Ag, mo and other elements playing a role in solid solution strengthening, and a certain amount of nano precipitated phase can be precipitated in the subsequent drawing process of the wire rod, so that the strength of the alloy is improved on the premise of reducing the cost of alloy raw materials. . Although different strengthening elements have been used in the prior art to maintain a lower thermal expansion coefficient, the combination and percentage of different elements are difficult in the art to achieve both mechanical properties and thermal expansion coefficient, and in particular, different component designs are adapted to a suitable preparation process.
The preparation process of the invention prepares the wire rod through the technological paths of fine grain strengthening, including homogenization treatment, hot forging and technological parameter adjustment in hot rolling, and reduces the existing grain size from 9.5 mu m to 1.7 mu m at the lowest, thereby providing an excellent intermediate product for the performance strengthening of invar alloy.
Further, by combining with a cold drawing process, the pass deformation and the true strain of the wire rod are regulated through three-stage treatment, the wire rod with the diameter of phi 6.5mm and the tensile strength of more than or equal to 700MPa is cold drawn to prepare a core material with the diameter of phi 1.42mm and the strength of more than 1300MPa, and the thermal expansion coefficient of the core material at the room temperature of-200 ℃ is as low as 1.5x10 -6 The number of turns is 33-45 per DEG C, has high tensile strength and torsion performance, and has obvious advantages when being applied to the double-capacity conductive cable.
The invention has the technical effects that: by adding 0.10-0.60% of specific strengthening element Cu, the fine-grain strengthening preparation process can lead the average grain diameter of the wire rod to be less than 2 mu m, the tensile strength to be 700Mpa, the microhardness to be more than 170HV and the thermal expansion coefficient to be 2.50 multiplied by 10 at 200 DEG C -6 The obtained hot rolled wire rod has uniform particle size and small average particle size and is used as an intermediate productThe performance can be optimized for the wire rod used for preparing the double-capacity conductive cable.
Furthermore, the Invar_V_Cu hot rolled wire rod is matched with the cold drawing process, so that the strength of the Invar alloy wire rod can reach more than 1300MPa, and the minimum thermal expansion coefficient of the Invar alloy wire rod at room temperature-200 ℃ reaches 1.5X10 -6 And the number of turns can reach 33-45 at the same time. Through carrying out scientific ratio to the wire drawing mould, the phenomenon of broken wire should not take place when drawing, the yield is higher, can realize stable, batch production, guarantees to obtain the high torsional properties core material of invar alloy, possesses better thermal expansion performance simultaneously.
Drawings
FIG. 1 is a process flow for preparing a high torsional property invar alloy core material;
FIG. 2 shows GRC plots and grain sizes for different alloyed invar alloys in hot rolled state for examples 1-3;
FIG. 3 comparison of grain size for the invar alloy of example 3 and comparative example 1;
FIG. 4 mechanical properties of cold drawn invar alloys of examples 1-3; FIG. (a) is a plot of tensile strength versus amount of pullout strain ε; FIG. (b) shows the relationship between the micro Vickers hardness and the drawing strain amount ε;
fig. 5 is a schematic diagram of a cold drawing die.
Detailed Description
The present invention will now be described more fully hereinafter with reference to the accompanying drawings, in which some, but not all embodiments of the invention are shown, to illustrate, but not to limit the invention.
Example 1
The preparation process of the Invar alloy Invar_Nb_Mo wire rod comprises the following steps:
s1, adopting the composition design of the embodiment 1in the table 1;
s2, batching;
s3, smelting: the invar alloy is smelted into square ingots by a vacuum induction furnace, and the head and the tail of the square ingots are cut off to form obvious shrinkage cavity parts;
s4, planing: the planing machine is adopted to carry out planing treatment on the side surface to remove the defects of surface shrinkage cavity, oxide skin and the like, so that the influence of the surface defects on the subsequent hot forging and hot rolling process is reduced;
s5, homogenizing: before hot forging, the cast ingot is placed in a furnace to be heated for 2 hours so as to homogenize the structure;
s6, hot forging: hot forging is carried out within the range of 1170-1190 ℃, if the temperature is reduced to below 900 ℃ in the hot forging process, the hot forging process should be carried out again for heating, the surface is polished after the hot forging, and the surface oxide film is removed until no obvious defect exists, and the next hot rolling stage can be carried out;
s, hot rolling: hot rolling means rolling the metal above the recrystallization temperature, the initial rolling temperature is 1060 ℃, and the final rolling temperature is 1000 ℃; the highest rolling speed is less than or equal to 68m/s, and the cooling speed after rolling is 0.22 ℃/s;
s8, obtaining a hot rolled wire rod, wherein the wire rod has the size of
Example 2
The preparation process of the invar_V wire rod comprises the following steps: the composition design, proportioning, smelting, planing, homogenization treatment, hot forging, hot rolling and obtaining a hot rolled wire rod are adopted in the embodiment 2 in the table 1; the other processes are the same.
Example 3
The preparation process of the Invar alloy Invar_V_Cu wire rod comprises the following steps: the composition design, proportioning, smelting, planing, homogenization treatment, hot forging, hot rolling and obtaining a hot rolled wire rod in example 3in Table 1 are adopted; the other processes are the same.
Example 4
A preparation process of an invar alloy wire rod comprises the following steps: the hot rolled wire rod was obtained by using the composition design, proportioning, smelting, planing, homogenization treatment, hot forging, hot rolling of example 4 in table 1; the other processes are the same.
Example 5
A preparation process of an invar alloy wire rod comprises the following steps: the hot rolled wire rod was obtained by using the composition design, proportioning, smelting, planing, homogenization treatment, hot forging, hot rolling of example 5 in table 1; the other processes are the same.
Example 6
A preparation process of an invar alloy wire rod comprises the following steps: the composition design, proportioning, smelting, planing, homogenization treatment, hot forging, hot rolling and obtaining a hot rolled wire rod are adopted in the embodiment 6in the table 1; the other processes are the same.
Comparative example 1
The composition design of example 2 of patent CN 114807765B was used as comparative example 1, and the preparation process of example 3 was used, wherein in S7 hot rolling, the initial rolling temperature: 1040 ℃, finishing temperature: 910 deg.c;
in S7 hot rolling, the highest rolling speed is less than or equal to 88m/S, and the cooling speed after rolling is 0.40 ℃/S; s8, in the hot rolled wire rod obtained in the step S, the wire rod size is
The composition designs and performance parameters of examples 1-6 and comparative example 1 are shown in tables 1 and 2 below.
TABLE 1 composition design for examples 1-6 and comparative example 1
Table 2 performance parameters of examples 1-6 and comparative example 1
As shown in table 2, the invar wire rod containing Cu element example 3invar_v_cu and example 6invar_mo_cu had the smallest average grain size of 2 μm or less compared to other Cu-free examples; the tensile strength is higher and reaches more than 700 MPa; invar embodiments containing Cu have lower coefficients of thermal expansion.
The grain size GRC plots for examples 1-3 are shown in FIG. 2; the grain size GRC graphs of example 3 and comparative example 1 are shown in FIG. 3. Example 3 the grain size of comparative example 1 was 9.76 μm and the grain size was not uniform, whereas the finish rolling temperature, the maximum rolling speed, and the cooling speed after rolling employed in example 3 enabled obtaining a uniform and stable invar wire rod having an average grain size of 1.7 μm.
Effect example 1 mechanical properties of cold drawn invar alloys examples 1-3
As shown in fig. 4, it can be seen from the graph (a) that the thermal expansion properties of the alloyed Invar alloys of examples 1 to 3 all increased with increasing drawing strain amount epsilon, and the invar_nb_mo alloy had the greatest tensile strength at different drawing strain amounts. Considering that the performance of the hot rolled wire rod of Invar_V_Mo alloy is lower than that of the other two alloyed Invar alloy wires, it is demonstrated that Invar_Nb_Mo alloy has a higher work hardening rate, thereby making the tensile strength increase rate larger. The Invar_V alloy and Invar_V_Cu alloy have near tensile strength when undeformed, and after drawing the Invar_V_Cu alloy has higher tensile strength than the Invar_V alloy, indicating that the Invar_V_Cu alloy has a more pronounced work hardening rate than the Invar_V alloy.
As can be seen from the graph (b), although the invar_nb_mo alloy has the greatest tensile strength at different amounts of drawing strain, the elongation is always lower than the other two alloys at different amounts of strain, with the example 3invar_v_cu alloy having the highest elongation at different amounts of drawing strain. In summary, the elongation of the example 3Invar_V_Cu alloy is optimal, while having a stable tensile strength.
Effect example 2 thermal expansion Properties of Cold drawn invar alloys examples 1-3
Table 3 shows the thermal expansion properties of the drawing strain amounts epsilon=0.81 and epsilon=2.14 alloyed invar. When the drawing strain amount epsilon=0.81, the invar_nb_mo alloy has a significantly low thermal expansion coefficient in the temperature range of room temperature-200 ℃ of 1.55, and the invar_v alloy and the invar_v_cu alloy have thermal expansion coefficients close to, but significantly higher than, the thermal expansion coefficients of the invar_nb_mo alloy. As can be seen from table 3, invar alloys of three alloying components all have a very pronounced low thermal expansion effect when the drawing strain amount epsilon=2.14, with invar_v_cu alloys having the lowest thermal expansion coefficient of 0.48 and invar_v alloys having the highest thermal expansion coefficient of 1.22 at the temperature range of room temperature to 200 ℃. Considering the thermal expansion properties under the drawing strain amounts epsilon=0.81 and epsilon=2.14 in combination, the thermal expansion properties of invar_v_cu of example 3 are more excellent.
Table 3 thermal expansion properties of the invar alloys of examples 1-3 at drawing strain amounts epsilon=0.81 and epsilon=2.14
Example 7
A core material was prepared by the cold drawing process of example 7 of table 4 using the invar_v_cu alloy wire rod of example 3 as a raw material.
Example 8
A core material was prepared by the cold drawing process of example 8 of table 4 using the invar_v_cu alloy wire rod of example 3 as a raw material.
Example 9
A core material was prepared by the cold drawing process of example 9 of table 4 using the invar_v_cu alloy wire rod of example 3 as a raw material.
Example 10
A core material was prepared by the cold drawing process of example 7 of table 4 using the invar_nb_mo alloy wire rod of example 1 as a raw material.
Example 11
A core material was prepared by the cold drawing process of example 7 of table 4 using the invar_v alloy wire rod of example 2 as a raw material.
Comparative example 2
A core material was prepared by the cold drawing process of comparative example 2 of table 4 using the invar_v_cu alloy wire rod of example 3 as a raw material.
Comparative example 3
A core material was prepared by the cold drawing process of comparative example 3 of table 4 using the invar_v_cu alloy wire rod of example 3 as a raw material.
Comparative example 4
A core material was prepared by the cold drawing process of comparative example 4 of table 4 using the invar_v_cu alloy wire rod of example 3 as a raw material.
Effect example 3 comparative effects from different drawing processes using the alloy wires invar_v_cu alloy wire rods of examples 1 to 3 as raw materials are shown in table 4.
TABLE 4 comparative process performance of examples 7-9 and comparative examples 2-4
Conclusion: the second stage and the third stage of comparative example 2 have larger pass deformation amount to cause yarn breakage; the first stage pass deformation of comparative example 3 is smaller, and the number of turns is smaller; the third stage of the comparative example 4 has smaller pass deformation and smaller tensile strength, and the conditions of broken wires, poor torsion performance, lower tensile strength and the like of the prepared wires in the comparative examples 2-4 are obvious due to unreasonable pass deformation setting. Meanwhile, examples 7 to 9 can obtain a wire rod having a tensile strength of 1300MPa or more and a number of turns of 33 to 45 by adjusting the deformation amount of the 3-stage drawing pass, etc., and the diameter size ranges fromWithin the inner part. Therefore, by reasonably setting the pass deformation and matching with three-stage cold drawing, the invar alloy wire rod with high tensile strength, good torsion performance and lower thermal expansion coefficient can be obtained.
Effect example 4 torsional properties of invar core materials of examples 7, 10, and 11
The different alloy cores of examples 7, 10 and 11 were subjected to torsion test according to GB/T239.1-2012 method for unidirectional torsion test of metal wire, and the results are shown in Table 5, wherein the torsion turns of the alloy of example 10Invar_Nb_Mo are 14 turns, the torsion turns of the alloy of example 11Invar_V are 30 turns, and the torsion turns of the alloy of example 7Invar_V_Cu are 38 turns. It is known that the Invar_V_Cu alloy has the best torsion performance after three-stage cold drawing.
Table 5 torsional properties of the cold drawn invar alloys of examples 7, 10, 11
| Examples | Ingredient labeling | Number of turns |
| 7 | Invar_V_Cu | 38 |
| 10 | Invar_Nb_Mo | 14 |
| 11 | Invar_V | 30 |
It is to be understood that the above examples are illustrative of the present invention and are not to be construed as limiting the embodiments, and that obvious variations or modifications from the described embodiments are intended to be within the scope of the invention.
Claims (10)
1. An invar alloy core material with high torsion performance comprises the following components in percentage by weight: c:0.18 to 0.30 percent; mn:0.15 to 0.50 percent; si: less than or equal to 0.30 percent; ni:35.0 to 38.0 percent; cu:0.10 to 0.60 percent; the material also comprises one or more strengthening elements, and the weight percentages are as follows: mo:1.40 to 2.00 percent; nb:0.05 to 0.60 percent; v:0.80 to 1.20 percent; in addition, the balance being Fe and unavoidable impurities.
2. The invar core material of claim 1, comprising the following components in weight percent: c:0.20 to 0.28 percent; mn:0.25 to 0.40 percent; si: less than or equal to 0.20 percent; ni:36.0 to 37.8 percent; cu:0.30 to 0.50 percent, and one or more strengthening elements selected from the following components in percentage by weight: mo:1.60 to 1.80 percent; nb:0.10 to 0.30 percent; v:0.90 to 0.98 percent; in addition, the balance being Fe and unavoidable impurities.
3. Invar alloy core material according to claim 2, comprising the following components in weight percent: c:0.20 to 0.28 percent; mn:0.25 to 0.40 percent; si: less than or equal to 0.20 percent; ni:36.0 to 37.8 percent; v:0.90 to 0.98 percent; cu:0.30 to 0.50 percent; the balance of Fe and unavoidable impurities; preferably, the invar alloy comprises the following components in percentage by weight: c:0.24%; mn:0.31%; si:0.17%; ni:37.5%; v:0.96%; cu:0.32%; the balance being Fe and unavoidable impurities.
4. Invar alloy core material according to claim 2, comprising the following components in weight percent: c:0.20 to 0.28 percent; mn:0.25 to 0.40 percent; si: less than or equal to 0.20 percent; ni:36.0 to 37.8 percent; mo:1.60 to 1.80 percent; cu:0.30 to 0.50 percent; the balance of Fe and unavoidable impurities; preferably, the invar alloy comprises the following components in percentage by weight: c:0.23%; mn:0.30%; si:0.13%; ni:37.1%; mo:1.7%; cu:0.5%; the balance being Fe and unavoidable impurities.
5. A process for preparing invar core material according to claim 1, comprising the steps of: component design, proportioning, smelting, planing, homogenization treatment, hot forging, hot rolling wire rods and cold drawing.
6. A process for preparing an invar alloy core material according to claim 5, comprising the steps of:
s1, designing components;
s2, batching;
s3, smelting, namely smelting into square ingots by adopting a vacuum induction furnace, and cutting off parts with obvious shrinkage cavities at the head and the tail;
s4, planing, namely planing the side surface by adopting a planer to remove defects such as surface shrinkage cavities, oxide scales and the like, so that the influence of the surface defects on the subsequent hot forging and hot rolling processes is reduced;
s5, homogenizing treatment, namely placing the cast ingot into a furnace to heat for 2-5 hours before hot forging so as to homogenize the structure;
s6, hot forging, namely hot forging is carried out within the range of 1100-1200 ℃, and if the temperature is reduced to below 900 ℃ in the hot forging process, the furnace should be returned again for heating, the surface should be polished after hot forging, and the surface oxide film is removed until no obvious defect exists, and the next hot rolling stage can be carried out;
s7, hot rolling, namely rolling the metal above the recrystallization temperature;
s8, obtaining a hot rolled wire rod;
s9, cold drawing to obtain the core material.
7. The process for preparing invar alloy core material according to claim 6, wherein in the S7 hot rolling, the complete recrystallization of the alloy during the deformation process is ensured by the hot rolling; initial rolling temperature: 1000-1150 ℃ and finishing temperature: 950-1050 ℃, the highest rolling speed is less than or equal to 80m/s, and the cooling speed after rolling is 0.15-0.35 ℃/s; preferably, in the S7 hot rolling, the initial rolling temperature: 1050-1100 ℃, finishing temperature: 980-1030 ℃, the highest rolling speed is less than or equal to 68m/s, and the cooling speed after rolling is 0.22 ℃/s.
8. The process for preparing invar alloy core material according to claim 6, wherein the S9 cold drawing comprises three stages:
cold drawing in the first stage, namely, continuously cold drawing the alloy wire rod in the first stage through 3-5 wire drawing dies in the room temperature environment, wherein the true strain epsilon of the wire rod is less than or equal to 1.5, the deformation of each pass is 18-25%, and the deformation of the last pass in the first stage is the largest and is not more than 25%;
cold drawing in the second stage, wherein the true strain epsilon=1.5-2.5 of the wire rod, and the deformation of each pass is between 12-18%;
and in the third stage of cold drawing, the true strain epsilon=2.5-3.0 of the wire rod, the deformation of each pass is between 10-15%, and the deformation of each pass is from large to small.
9. A process for preparing a invar alloy core material according to claim 6, wherein in the S9 cold drawing, the invar alloy drawing rate is set to 1-5mm/S, preferably 2mm/S; further, in the S9 cold drawing, the diameter size after cold drawing is 1.0-2.0 phi/mm, preferably phi 1.42mm; in the cold drawing in step S9, the total true strain amount epsilon=2.5 to 3.5, preferably epsilon=3.0.
10. Invar wire with high torsion properties, produced by the manufacturing process according to any of claims 7-9.
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