CN108315664B - Preparation method of thread rolling plate material - Google Patents

Preparation method of thread rolling plate material Download PDF

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CN108315664B
CN108315664B CN201810387252.2A CN201810387252A CN108315664B CN 108315664 B CN108315664 B CN 108315664B CN 201810387252 A CN201810387252 A CN 201810387252A CN 108315664 B CN108315664 B CN 108315664B
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carbide
thread rolling
plate material
rolling plate
electroslag ingot
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CN108315664A (en
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邵青立
尤晓东
李小明
朱长青
谢志斌
李栋
李海山
孙宗林
张巍
胡春波
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HEYE SPECIAL STEEL CO LTD
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt

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Abstract

The invention provides a thread rolling plate material, which comprises the following chemical components in percentage by mass: c: 1.04-1.10%, W: 1.20-1.60%, Mo: 9.40-9.80%, Cr: 3.50-4.10%, V: 1.10-1.40%, 3.00-3.50% of Co, and the balance of iron and impurities; the carbide composition of the thread rolling plate material is MC carbide and M6C carbide, wherein the type of MC carbide is VC. The high-molybdenum high-speed rigid carbide disclosed by the invention has fine granularity and excellent impact toughness, thermoplasticity and machinability; the thread rolling plate processed by the thread rolling plate material has stable quality in the using process, and the service life of the thread rolling plate reaches 15 ten thousand times.

Description

Preparation method of thread rolling plate material
Technical Field
The invention relates to high-speed steel, in particular to a thread rolling die material. Meanwhile, the invention also relates to a preparation method of the thread rolling plate material.
Background
The thread rolling die is a thread tool commonly used for machining screw threads and bolt threads by standard fasteners, the machining principle is cold extrusion forming, and the thread rolling die has the advantages of high production efficiency, low machining cost, high precision and strength of machined threads, good surface quality and the like, so the thread rolling die is widely applied.
With the rapid development of the automobile and aviation industries in China, the requirements for high-strength screws are correspondingly improved, the performance grade of screw bolts reaches 8.8-12.9 grades, even reaches more than 12.9 grades, the thread rolling plates made of Cr12MoV, DC53 and other materials commonly used in the market at present cannot meet the production requirements, a large amount of thread rolling plate materials (more than 6000 tons) need to be imported every year, and the thread rolling plate materials need to be upgraded and replaced urgently.
Disclosure of Invention
In view of the above, the present invention aims to provide a screw plate material to obtain a screw plate material with fine carbide grain size and excellent impact toughness, thermoplasticity and machinability.
In order to achieve the purpose, the technical scheme of the invention is realized as follows:
the chemical components of the thread rolling plate material comprise the following components in percentage by mass: c: 1.04-1.10%, W: 1.20-1.60%, Mo: 9.40-9.80%, Cr: 3.50-4.10%, V: 1.10-1.40%, 3.00-3.50% of Co, and the balance of iron; the carbide composition of the thread rolling plate material is MC carbide and M6C carbide, wherein the type of MC carbide is VC.
The invention adopts the design principles of high Mo, low W, low V and Co, comprehensively considers the combination of carbide structure, wear resistance and toughness of steel, and adopts a special process flow, thereby leading the steel to have excellent impact toughness, thermoplasticity, wear resistance and machinability.
The function of the C element: the C element is one of the composition elements of the carbide, and part of the C element is dissolved in the matrix in a solid mode, so that the strength of the matrix is improved. The content of C is not less than 1.04 percent to ensure that alloy elements can fully participate in the precipitation of carbide, and when the content of C is less than 1.04 percent, the number of the carbide is correspondingly reduced, so that the wear resistance and the cutting performance of the steel are reduced. The maximum content of C is not more than 1.10% to ensure the uniformity and impact toughness of the steel, and when the content of C is more than 1.10, excessive carbides are formed, so that the distribution nonuniformity of the carbides is increased, and the plasticity and toughness of the steel are reduced. The maximum combination of wear resistance, uniformity and impact toughness can be obtained within the range of 1.04-1.10% of the C content.
Function of element W: 1) a certain amount of primary carbides which are difficult to dissolve are formed, so that the steel can be quenched at high temperature close to the melting point, and the wear resistance of the steel is improved; 2) forming a sufficient amount of secondary carbides, obtaining high-W martensite through high-temperature solution quenching, which is a main factor for obtaining secondary hardening and red hardness after tempering; 3) since W is a strong carbide-forming element, the eutectic carbide precipitated at one time during solidification is mainly a coarse skeletal network M6C is not easy to crush uniformly through deformation processing and is unfavorable for the plasticity of steel, so that the content of the W element is 1.20-1.60%. The content of W element is not less than 1.20% to form a sufficient amount of carbide. The maximum content of the element W is not higher than 1.60% to ensure the thermoplasticity of the steel.
Function of Mo element: is equivalent to the main action of W element. However, in the case of non-equilibrium cooling, the carbide formed by the Mo element undergoes a phase change to generate M in a metastable state2C carbide, M in the form of a sheet, sector2C is cooled after solidification, forged, heated and thermally insulated to decompose into fine M6C + MC, and makes it easy to distribute uniformly, increases the toughness of the steel and improves the thermoplasticity of the steel.
The function of the V element: the V element is a strong carbide forming element, and is combined with the C element in the steel to form high-hardness and high-strength MC carbide, which is a decisive organization factor of the wear resistance of the steel. The dissolved V element can greatly enhance the secondary hardening of the steel, and the retained carbide VC can greatly enhance the wear resistance of the steel. However, the high content of element V reduces the workability of the product to some extent. Therefore, the content of the V element is 1.10-1.40%. The content of V element is not less than 1.10% to ensure the formation of a sufficient amount of MC carbide, and when the content of V is less than 1.10%, the amount of MC carbide is correspondingly reduced, so that the wear resistance and machinability of the steel are deteriorated. The maximum content of V is not more than 1.40% to ensure the workability of the steel.
Function of Co element: 1) promoting M in the heat treatment process6C carbide is fully precipitated, and the high-speed steel has enough hardness; 2) restraining devicePrecipitation of MC carbide and M6The growth of C carbide further refines the granularity of the carbide, thereby increasing the toughness of the steel. The content of Co element designed by the invention is 3.00-3.50%. The content of Co element is not less than 3.00% to ensure the full precipitation of carbide.
Function of Cr element: the Cr element can promote the precipitation of carbide, and meanwhile, part of the Cr element is dissolved in the matrix in a solid mode and mainly acts on improving the hardenability and the tempering hardness of the steel. The content of Cr element in the invention is 3.50-4.10%.
Further, the chemical components of the thread rolling plate material comprise the following components in percentage by mass: c: 1.04-1.06%; w: 1.40-1.60%; mo: 9.60-9.80%; cr: 3.50-3.70%; v: 1.30-1.40% of Co, 3.00-3.20% of Co, the balance of iron and the balance of iron.
Furthermore, the volume fraction of the MC carbide is 23-28%, the size of the MC carbide with the volume fraction of at least 12-15% is less than or equal to 4 μm, and the maximum size of the MC carbide is not more than 15 μm.
Further, said M6The type of C carbide is (Mo, W)6(C、N)。
Further, said M6The volume fraction of C carbide is 6-9%, and at least 5% of the volume fraction of M6MC of C carbide is less than or equal to 8 μ M in size, M6The maximum size of C carbide is not more than 18 μm.
The invention also provides a preparation method of the thread rolling plate material, so as to prepare the thread rolling plate material.
In order to achieve the purpose, the technical scheme of the invention is realized as follows:
a preparation method of a thread rolling plate material comprises the following steps:
(1) preparing an electroslag ingot: refining the raw materials to obtain an electrode rod with phi 350-380 mm; annealing the electrode bar and then carrying out electroslag remelting to obtain an electroslag ingot with the diameter of phi 400 mm;
(2) cogging:
a. and (3) electroslag ingot homogenization treatment: homogenizing the electroslag ingot with the diameter of phi 400 mm; and cooling the electroslag ingot subjected to homogenization treatment along with the furnace to obtain an electroslag ingot with the diameter of 400 mm.
b. Cogging: and c, forging the electroslag ingot with the diameter of 400mm in the step a into a round billet with the diameter of 135 mm.
c. Forming materials: and forging the round billet with the diameter of 135mm into a material to obtain a forged material with the diameter of 50 mm.
Further, the electroslag ingot homogenization treatment comprises the following steps:
a first step: putting the electroslag ingot into a heating furnace, heating to 850 ℃ at the speed of 90-100 ℃/h, and preserving heat for 3 h; a second step: heating the electroslag ingot to 1070 ℃ at the speed of 90-100 ℃/h, and preserving the temperature for 1.5 h; a third step: heating the electroslag ingot to 1180 ℃ at the speed of 90-100 ℃/h, and preserving heat for 8.0 h; a fourth step: rapidly cooling the electroslag ingot to 900 ℃ at the speed of 200-; a fifth step: heating the electroslag ingot to 1130 ℃ at the speed of 100-.
Further, the cogging in the step b is combined fast forging and finish forging.
Further, performing fast forging on the electroslag ingot obtained in the step a to obtain a round billet with phi of 240 mm; and carrying out precision forging on the round billet with the diameter phi of 240mm to obtain the round billet with the diameter phi of 135 mm.
Furthermore, the carbide flows to the parallel tooth directions during the material forming in the step C.
Compared with the prior art, the invention has the following advantages:
(1) by adopting the technical scheme of the invention, the obtained thread rolling plate material has fine carbide granularity, and has excellent impact toughness, thermoplastic hardness and machinability;
(2) the thread rolling plate processed by the thread rolling plate material has stable quality in the using process, and the service life of the thread rolling plate reaches 15 ten thousand times.
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this specification, illustrate an embodiment of the invention and, together with the description, serve to explain the invention and not to limit the invention. In the drawings:
FIG. 1 is a photograph of carbide non-uniformity of the die material of example 1.3 of the present invention.
Detailed Description
It should be noted that the embodiments and features of the embodiments may be combined with each other without conflict.
The present invention will be described in detail below with reference to the embodiments with reference to the attached drawings.
The design concept of the invention is to prepare the thread rolling plate material by adopting the design principles of high C, high V and W and adopting the injection molding process.
Through the arrangement of the integral design concept, the alloy elements can be promoted to participate in the nucleation and the refinement of carbide under the spray forming process, so that the steel has excellent wear resistance and toughness.
Based on the overall design concept as above, the following examples relate to a thread rolling plate material and a method for preparing the same. To provide a detailed description of some specific applications of the above design concepts.
Example 1
This example relates to a set of thread rolling plate materials having the chemical composition shown in table 1.1:
table 1.1 the thread rolling material of example 1 has the chemical composition as shown in table 1.1:
Figure GDA0002270538040000051
the preparation method comprises the following steps:
the method comprises the steps of preparing an electroslag ingot by a special electroslag process → homogenizing the electroslag ingot → upsetting and drawing the high-speed steel electroslag ingot, and performing quick forging and finish forging combined cogging → changing the finished product process of a metal flow line.
(1) Preparation of electroslag ingot
The raw materials consisting of the mass fraction are refined outside a furnace to obtain an electrode rod with phi 350-. Wherein the annealing temperature is 800 ℃, the temperature is kept for 2h, and then the product is cooled to 700 ℃ at the speed of 10 ℃/s and is cooled along with the furnace. The electroslag process introduces an R value concept, wherein R is voltage/current, and the R value is controlled to be 8.5-9.5 during remelting. Meanwhile, the shape of the electrode conical head is kept flat, so that molten drops are refined and dropped on the edge area of the electrode, the temperature difference between the center and the edge of the metal molten pool is reduced, the steel ingot molten pool is shallow and flat, and the center structure is improved.
(2) And cogging the steel
a. Homogenization treatment of electroslag ingot
The high-temperature homogenization treatment process comprises 5 steps in total, and the specific steps and parameters are as follows:
a first step: placing the electroslag ingot into a heating furnace, heating to 850 ℃, and preserving heat for 3 hours; wherein, the heating rates of the examples 1.1 to 1.4 are respectively 90, 98, 95 and 100 ℃/h;
a second step: keeping the temperature of the electroslag ingot at 1070 ℃ for 1.5 h; wherein, the heating rates of the examples 1.1 to 1.4 are respectively 98, 96, 100 and 90 ℃/h;
a third step: heating the electroslag ingot to 1180 ℃, and preserving heat for 8.0 hours; wherein, the heating rates of the examples 1.1 to 1.4 are respectively 92, 90, 94 and 100 ℃/h;
a fourth step: rapidly cooling the electroslag ingot to 900 ℃, and preserving heat for 3.0 h; wherein, the heating rates of the examples 1.1 to 1.4 are 215, 230, 250 and 245 ℃/h respectively;
a fifth step: heating the electroslag ingot to 1130 ℃, and preserving heat for 4 hours; wherein, the heating rates of the examples 1.1 to 1.4 are respectively 120, 100, 110 and 110 ℃/h;
and cooling the electroslag ingot subjected to homogenization treatment along with the furnace to obtain an electroslag ingot with the diameter of 400 mm.
b. Quick forging and finish forging combined cogging
Preheating an electroslag ingot with the diameter of 400mm to 200 ℃, placing the electroslag ingot on a hammer anvil, clamping the electroslag ingot by the hammer anvil, and preheating for 0.5 h;
keeping the temperature at 950 ℃ for 1h, and fully crushing an electroslag ingot by using a rapid forging machine to obtain an intermediate blank; keeping the temperature of the intermediate billet at 950 ℃ for 1h, upsetting by using a quick forging machine, respectively pressing down two ends for three times during upsetting, and respectively controlling the deformation of the three times to be 10%, 25% and 10%, thereby ensuring the full crushing of carbide; immediately tempering and not drawing out after upsetting is finished, effectively avoiding the generation of surface and internal defects, heating the blank to 850 ℃, and preserving heat for 4 hours to obtain a round blank with the diameter of 240 mm.
And (3) keeping the temperature of the obtained 240 mm-phi round billet at 900 ℃ for 2h, and upsetting by using a precision forging machine, wherein the upsetting amount is 35%, so that the full crushing of carbides is ensured, the surface and internal quality is ensured, and the 135 mm-phi round billet is obtained.
In the upsetting process, the anvil width ratio W/H is controlled to be 0.8-1.0, and the material width ratio B/H is controlled to be 0.9-1.2, so that surface and internal defects are avoided.
The high-speed steel ingot upsetting is extremely careful because the alloy content is high, the plasticity is poor, the steel ingot cogging process generally adopts the drawing-out, the upsetting is easy to generate surface defects such as folding, transverse cracking and the like, and the drawing-out is not noticed a little and is easy to generate internal cracking defects, and the upsetting process of the high-speed steel ingot improves the material quality and ensures the surface and internal quality.
c. Finished product
B, forging the round blank with the diameter of 135mm in the step b into a material by using an electro-hydraulic hammer: the forging heating temperature was controlled at 750 ℃ to obtain a forged material having a diameter of 50 mm.
In order to increase the practicability of the electro-hydraulic hammer in the field of the screw plate, according to the use characteristics of the screw plate, upsetting can be used for redirection production during electro-hydraulic hammer forming, the flow direction of carbide is changed, the flow direction is enabled to be parallel to the tooth direction, and the service life is prolonged.
Example 2
This example relates to the verification of the carbide content and grain size, the heat treatment hardness, and the impact toughness of the thread rolling plate material of example 1, wherein the carbide content and grain size were analyzed based on the structural image obtained by the scanning electron microscope.
Comparative analysis of the thread rolling material of examples 1.1, 1.2 and 1.3 with the purchased thread rolling material (alloy a) gave the following results:
table 2.1 comparison of the composition of examples 1.1, 1.2 and alloy A, B
Figure GDA0002270538040000071
Figure GDA0002270538040000081
Table 2.2 carbide content and grain size comparison of examples 1.1, 1.2 and 1.3 with alloy A, B
Figure GDA0002270538040000082
In table 2.2, the thread rolling plate materials obtained in examples 1.1 to 1.3 had carbide grain sizes of at least 80% volume fraction carbide size.
The carbide of the thread rolling die material of the present invention was analyzed, and the carbide composition thereof was MC carbide and M6C carbide, wherein the type of MC carbide is VC, the main components are V, Mo, C and a small amount of alloy elements such as Fe, Cr and the like, M6C carbide is (Mo, W)6(C, N). The size of carbide of the thread rolling plate material is 4 mu M, the size of the maximum MC carbide is not more than 15 mu M, and the volume fraction of the MC carbide is 23-28%, on one hand, because the carbide formed by Mo element is subjected to phase change, metastable M is generated2C carbide, M in the form of a sheet, sector2C is cooled after solidification, forged, heated and thermally insulated to decompose into fine M6C + MC, and makes it easy to distribute uniformly, therefore, further increase the impact toughness of the steel and improve its thermoplasticity; on the other hand, the precipitation of carbide in the heat treatment process is promoted by 3.00-3.50% of Co, and the grain size of the carbide is further refined. Therefore, the thread rolling die material has excellent impact toughness and thermoplasticity. M in the invention6The volume fraction of the C carbide is 6-9%, the size of the C carbide is 8 μm, and the size of the largest MC carbide is not more than 18 μm. Compared with the carbide granularity in the alloy A, the carbide granularity of the thread rolling plate material of the invention is smaller than that of the alloy A, and the fine MC carbide and M thereof6C carbide, which provides the example die plate material with excellent impact toughness and workability. FIG. 1 shows the carbide inhomogeneities of the thread rolling material described in example 1.3And (6) uniformity pictures. As can be seen from the figure, the unevenness of the carbide of the thread rolling plate material of the present embodiment<3, the uniformity is better, the uniform granularity refinement of the thread rolling plate is promoted, and the performance of the thread rolling plate material is further enhanced.
Table 2.3 heat treated hardness and impact toughness of examples 1.1, 1.2, and 1.3 versus alloy A, B:
Figure GDA0002270538040000091
as can be seen from Table 3, the hardness of the thread rolling plate material of the present invention reaches 75HRC through proper heat treatment, which can meet the requirements of the application field of the thread rolling plate material of the present invention. The impact toughness performance of the thread rolling plate material is compared, and the result shows that the impact toughness performance of the thread rolling plate material is superior to that of the alloy A.
The thread rolling plate material can be made into thread rolling plate materials, and the service life is an important standard for inspecting the thread rolling plate. The screw plate material of example 1.3 was selected for repeated use experiments. The result shows that the thread rolling plate material of the embodiment 1.3 has stable quality in the using process, the service life reaches 15 ten thousand times, the material requirement of a high-grade thread rolling plate can be met, and the material level of the high-grade thread rolling plate is basically reached.
In conclusion, the thread rolling plate material disclosed by the invention has the advantages that the carbide granularity is fine, and the hardness, the impact toughness, the thermoplasticity and the machinability are excellent; the thread rolling plate processed by the thread rolling plate material has stable quality and long service life in the using process.
The above description is only for the purpose of illustrating the preferred embodiments of the present invention and is not to be construed as limiting the invention, and any modifications, equivalents, improvements and the like that fall within the spirit and principle of the present invention are intended to be included therein.

Claims (9)

1. A preparation method of a thread rolling plate material is characterized by comprising the following steps: the chemical components of the thread rolling plate material comprise the following components in percentage by mass: c: 1.04-1.10%, W: 1.20-1.60%, Mo: 9.40-9.80%, Cr: 3.50-4.10%, V: 1.10-1.40%, 3.00-3.50% of Co, and the balance of iron; the thread rolling plateThe carbide composition of the material is MC carbide and M6C carbide, wherein the type of MC carbide is VC; and the method for preparing the thread rolling plate material comprises the following steps:
(1) preparing an electroslag ingot: refining the raw materials to obtain an electrode rod with phi 350-380 mm; annealing the electrode bar and then carrying out electroslag remelting to obtain an electroslag ingot with the diameter of phi 400 mm;
(2) cogging:
a. and (3) electroslag ingot homogenization treatment: homogenizing the electroslag ingot with the diameter of phi 400 mm; cooling the electroslag ingot subjected to homogenization treatment along with a furnace to obtain an electroslag ingot with the diameter of phi 400 mm;
b. cogging: forging the electroslag ingot with the diameter of 400mm in the step a into a round billet with the diameter of 135 mm;
c. forming materials: and forging the round billet with the diameter of 135mm into a material to obtain a forged material with the diameter of 50 mm.
2. The method for preparing a thread rolling plate material according to claim 1, characterized in that: the chemical components of the thread rolling plate material comprise the following components in percentage by mass: c: 1.04-1.06%; w: 1.40-1.60%; mo: 9.60-9.80%; cr: 3.50-3.70%; v: 1.30-1.40%, 3.00-3.20% of Co, and the balance of iron.
3. The method for preparing a thread rolling plate material according to claim 1, characterized in that: the volume fraction of the MC carbide is 23-28%, the size of the MC carbide with the volume fraction of at least 12-15% is less than or equal to 4 μm, and the maximum size of the MC carbide is not more than 15 μm.
4. The method for preparing a thread rolling plate material according to claim 1, characterized in that: the M is6The type of C carbide is (Mo, W)6(C、N)。
5. Method for producing a thread rolling board material according to any one of claims 1-4, characterized in that: the M is6The volume fraction of C carbide is 6-9%, and at least 5% of the volume fraction of M6C carbide size less than or equal to 8 μ M, M6C carbideThe large size does not exceed 18 μm.
6. The method for preparing a thread rolling plate material according to claim 1, characterized in that: the electroslag ingot homogenization treatment comprises the following steps:
a first step: putting the electroslag ingot into a heating furnace, heating to 850 ℃ at the speed of 90-100 ℃/h, and preserving heat for 3 h; a second step: heating the electroslag ingot to 1070 ℃ at the speed of 90-100 ℃/h, and preserving the temperature for 1.5 h; a third step: heating the electroslag ingot to 1180 ℃ at the speed of 90-100 ℃/h, and preserving heat for 8.0 h; a fourth step: rapidly cooling the electroslag ingot to 900 ℃ at the speed of 200-; a fifth step: heating the electroslag ingot to 1130 ℃ at the speed of 100-.
7. A method for preparing a thread rolling plate material according to claim 1, characterized in that: and b, cogging in the step b is combined with quick forging and finish forging.
8. The method for preparing a thread rolling plate material according to claim 7, wherein: the quick forging and finish forging cogging comprises the following steps: b, performing fast forging on the electroslag ingot obtained in the step a to obtain a round billet with phi of 240 mm; and carrying out precision forging on the round billet with the diameter phi of 240mm to obtain the round billet with the diameter phi of 135 mm.
9. A method of producing a screw plate material according to any one of claims 6-8, characterized in that: and c, enabling the carbide to flow to the parallel tooth directions during the forming of the material.
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