CN116837192B - Superfine crystal high temperature carburized bearing steel and manufacturing method thereof - Google Patents

Superfine crystal high temperature carburized bearing steel and manufacturing method thereof Download PDF

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CN116837192B
CN116837192B CN202311111334.1A CN202311111334A CN116837192B CN 116837192 B CN116837192 B CN 116837192B CN 202311111334 A CN202311111334 A CN 202311111334A CN 116837192 B CN116837192 B CN 116837192B
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bearing steel
forging
temperature
ultra
heat
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CN116837192A (en
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武雪婷
吴志伟
陈文雄
郎东
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Chengdu Advanced Metal Materials Industry Technology Research Institute Co Ltd
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Chengdu Advanced Metal Materials Industry Technology Research Institute Co Ltd
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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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/58—Roll-force control; Roll-gap control
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
    • 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
    • B21C37/02—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of sheets
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • B21J5/002—Hybrid process, e.g. forging following casting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • B21J5/06—Methods for forging, hammering, or pressing; Special equipment or accessories therefor for performing particular operations
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • B21J5/06—Methods for forging, hammering, or pressing; Special equipment or accessories therefor for performing particular operations
    • B21J5/08—Upsetting
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/03—Amorphous or microcrystalline structure

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  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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Abstract

The invention belongs to the technical field of material processing, and discloses ultra-fine grain high-temperature carburized bearing steel and a manufacturing method thereof, wherein the method comprises the steps of adopting double vacuum melting to prepare an ingot; homogenizing the cast ingot; forging the homogenized cast ingot to obtain a forging; and (5) carrying out multi-pass critical zone rolling on the forging piece to obtain the bearing steel. According to the invention, by controlling the smelting and homogenizing processes and adopting the modes of upsetting and pulling and critical zone controlled rolling and cooling, the grain refinement of the high-temperature bearing steel is realized, and the superfine grain structure with the grain size less than or equal to 2 mu m is obtained, so that the method has important significance in improving the toughness of the material and refining the heat treatment structure of the subsequent carburization treatment.

Description

Superfine crystal high temperature carburized bearing steel and manufacturing method thereof
Technical Field
The invention belongs to the technical field of material processing, and particularly relates to ultra-fine grain high-temperature carburized bearing steel and a manufacturing method thereof.
Background
With the rapid development of the aviation industry in China, high-end parts for aviation become key factors for restricting the development of the high-end parts, and higher requirements are also put forward for raw materials for the parts. In order to meet the complex and severe working environment of the aviation bearing, various bearing materials are developed at home and abroad, wherein M50NiL steel is the preferred material of the engine bearing under the high-temperature service condition at present due to higher toughness, good hardenability and higher high-temperature hardness, and is widely applied to the manufacture of aerospace high-end part equipment.
The M50NiL steel has low carbon content and good carburization performance, and surface hardening is mainly realized by means of surface carburization and the like, so that the steel is novel surface hardening type high-temperature high-strength bearing steel. Because the aeroengine bearing is in high-rotation speed, heavy-load and high-temperature working environment for a long time, the aeroengine bearing is required to have high surface hardness, and the core part is required to have high strength and high toughness. However, the main problem of the existing high-temperature bearing steel is that the coarse grains not only reduce the toughness of the material, but also cause the situation of quenching deformation and cracking, in addition, the coarse grains also cause the bearing steel material to form net-shaped carbide in the carburization process, and the existence of the net-shaped carbide in the bearing steel is extremely easy to cause crack initiation and promote crack growth, so that the service life of the bearing is greatly reduced. Therefore, the grain refinement of the M50NiL steel has important significance for improving the toughness and the service life of the bearing.
In order to ensure that the bearing steel has excellent comprehensive mechanical properties, the microstructure control of the bearing steel is mostly concentrated on the refinement of the structure, and mainly comprises the refinement of carbide particles and crystal grains. While tissue refinement is currently achieved primarily by control of the thermal process. The invention discloses a long-life railway bearing steel and a preparation method thereof, and discloses a long-life railway bearing steel and a preparation method thereof, the invention mainly provides a processing method of a low-alloy bearing steel, and the production flow mainly relates to forging, carburizing treatment, primary quenching, tempering and isothermal quenching, and is not suitable for bearing steel with higher alloy content. The invention relates to CN114351053A ultra-fine grain high-toughness wear-resistant steel and a manufacturing method thereof, and the invention also aims at a manufacturing method of low alloy steel, and no related report is found on the manufacturing method of ultra-fine grain high-alloy high-temperature bearing steel at present.
In order to solve the above problems, it is necessary to provide an ultra-fine grain high temperature carburized bearing steel and a method of manufacturing the same.
Disclosure of Invention
In order to overcome the defects of the prior art, the invention aims to provide the ultra-fine grain high-temperature carburized bearing steel and the manufacturing method thereof, wherein the high-temperature bearing steel grain refinement is realized by controlling the smelting and homogenizing process and adopting a mode of upsetting and pulling and critical zone controlled rolling and controlled cooling, so that an ultra-fine grain structure with the grain size less than or equal to 2 mu m is obtained, and the toughness of the material and the subsequent carburization treatment heat treatment structure refinement are improved.
In order to achieve the above purpose, the present invention provides the following technical solutions:
a preparation method of ultra-fine grain high temperature carburized bearing steel comprises the following steps:
preparing an ingot by adopting double vacuum smelting;
homogenizing the cast ingot;
forging the homogenized cast ingot to obtain a forging;
carrying out multi-pass critical zone rolling on the forging to obtain bearing steel;
wherein the bearing steel comprises the following chemical components in percentage by weight: c:0.10-0.16%, cr:3.50-4.80%, mo:3.80-5.00%, ni:3.00-3.90%, V:0.90-1.60%, mn:0.12-0.45%, si:0.10-0.28%, and the balance of Fe and impurities.
In some embodiments of the invention, dual vacuum melting is used to make ingots comprising:
and adopting vacuum induction melting and vacuum consumable melting to prepare cast ingots.
In some embodiments of the invention, the process parameters of the homogenization treatment include: the heating temperature is 1100-1200 ℃, and the heat preservation time is more than or equal to 24 hours.
In some embodiments of the invention, forging the homogenized ingot comprises:
the ingot is subjected to multiple upsetting deformation, the upsetting temperature is 850-1050 ℃, the first heat deformation amount is 40-55%, the second heat deformation amount is 60-75%, the third heat deformation amount is 40-55%, the fourth heat deformation amount is 15-30%, and the heat preservation time is more than or equal to 0.5 hour after each heat.
In some embodiments of the invention, the process parameters of critical zone rolling include: the rolling temperature is 750-900 ℃, the deformation amount of each pass is 7-20%, the furnace is returned to keep the temperature for 10-30min after each pass of deformation, and then the next pass of rolling is carried out, and the total deformation amount is controlled to be 60-80%.
In some embodiments of the present invention, after subjecting the forging to multi-pass critical section rolling, the method includes:
and cooling the rolled forging to room temperature in an ultra-fast cooling mode to obtain the bearing steel.
On the other hand, the invention also discloses the ultra-fine grain high-temperature carburized bearing steel, which is manufactured by adopting the method.
In some embodiments of the invention, the bearing steel comprises the following chemical components in percentage by weight: c:0.10-0.16%, cr:3.50-4.80%, mo:3.80-5.00%, ni:3.00-3.90%, V:0.90-1.60%, mn:0.12-0.45%, si:0.10-0.28%, and the balance of Fe and impurities.
In some embodiments of the invention, the bearing steel has an average grain size of 2 μm or less.
The invention has the technical effects and advantages that:
1. according to the invention, by controlling the smelting and homogenizing processes and adopting the modes of upsetting and pulling and critical zone controlled rolling and cooling, the grain refinement of the high-temperature bearing steel is realized, and the superfine grain structure with the grain size less than or equal to 2 mu m is obtained, so that the method has important significance in improving the toughness of the material and refining the heat treatment structure of the subsequent carburization treatment.
2. According to the forging method, the ingot is subjected to upsetting deformation for multiple times, so that the ingot is fully forged, the blank is ensured to reach the size required by forging forming, the ingot blank is fully deformed, and the phenomenon of uneven structures such as coarse crystals, mixed crystals and the like of the forging is prevented.
3. According to the invention, the forging is subjected to multi-pass critical zone rolling, the rolling temperature is controlled to be 750-900 ℃, so that the forging is deformed in the range of 750-900 ℃ to dynamically recrystallize to form fine recrystallized grains, an ultrafine grain structure is obtained, the cracking risk caused by the too low rolling temperature is avoided, and the recrystallized grains grow in the deformation process due to the too high rolling temperature.
Additional features and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention. The objectives and other advantages of the invention may be realized and attained by the structure particularly pointed out in the written description and claims hereof as well as the appended drawings.
Drawings
FIG. 1 is a flow chart of a method for manufacturing ultra-fine grain high temperature carburized bearing steel in accordance with the present invention;
FIG. 2 is a grain structure diagram of the bearing steel prepared in example 1;
FIG. 3 is a grain structure diagram of the bearing steel prepared in example 2;
fig. 4 is a grain structure diagram of the bearing steel prepared in the comparative example.
Detailed Description
The following description of the embodiments of the present invention will be made clearly and completely with reference to the accompanying drawings, in which it is apparent that the embodiments described are only some embodiments of the present invention, but not all embodiments. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention.
As shown in fig. 1, the present invention provides a method for manufacturing ultra-fine grain high temperature carburized bearing steel, comprising:
preparing an ingot by adopting double vacuum smelting;
homogenizing the cast ingot;
forging the homogenized cast ingot to obtain a forging;
carrying out multi-pass critical zone rolling on the forging to obtain bearing steel;
wherein the bearing steel comprises the following chemical components in percentage by weight: c:0.10-0.16%, cr:3.50-4.80%, mo:3.80-5.00%, ni:3.00-3.90%, V:0.90-1.60%, mn:0.12-0.45%, si:0.10-0.28%, and the balance of Fe and impurities.
In some embodiments of the invention, dual vacuum melting is used to make ingots comprising:
vacuum Induction Melting (VIM) and vacuum consumable melting (VAR) are carried out on the cast ingot, and S, P, gas, five harmful impurity elements and the like in steel are controlled at extremely low levels through a double-vacuum smelting technology, so that the small size, small quantity and uniform distribution of the impurities are ensured.
In some embodiments of the invention, the process parameters of the homogenization treatment include: the heating temperature is 1100-1200 ℃, the heat preservation time is more than or equal to 24 hours, and the purpose of heat preservation at the temperature is to reduce primary carbide formed in the solidification process of the material as much as possible and precipitate equal micro segregation, so that the components of the cast ingot are uniform, and the influence of the primary carbide on subsequent hot working is eliminated.
In some embodiments of the invention, forging the homogenized ingot comprises:
the ingot is subjected to multiple upsetting deformation, the upsetting temperature is 850-1050 ℃, the first heat deformation amount is 40-55%, the second heat deformation amount is 60-75%, the third heat deformation amount is 40-55%, the fourth heat deformation amount is 15-30%, and the heat preservation time is more than or equal to 0.5 hour after each heat.
The ingot can be fully forged through by upsetting for a plurality of times, the ingot is ensured to reach the size required by forging forming, the ingot is fully deformed, and the phenomenon of uneven structures such as coarse crystals, mixed crystals and the like of the forging is prevented.
In some embodiments of the invention, the process parameters of critical zone rolling include: the rolling temperature is 750-900 ℃, the deformation amount of each pass is 7-20%, the furnace is returned to keep the temperature for 10-30min after each pass of deformation, and then the next pass of rolling is carried out, and the total deformation amount is controlled to be 60-80%.
It should be noted that, too low rolling temperature has cracking risk, too high rolling temperature can cause the recrystallization grain to grow in the deformation process, by controlling the rolling temperature to 750-900 ℃ and adopting critical zone rolling, the forging deforms in the range of 750-900 ℃ and can dynamically recrystallize to form fine recrystallization grains, thereby obtaining the ultra-fine grain structure.
In some embodiments of the present invention, after subjecting the forging to multi-pass critical section rolling, the method includes:
and cooling the rolled forging to room temperature in an ultra-fast cooling mode to obtain the bearing steel.
On the other hand, the invention also discloses the ultra-fine grain high-temperature carburized bearing steel, which is manufactured by adopting the method.
In some embodiments of the invention, the bearing steel comprises the following chemical components in percentage by weight: c:0.10-0.16%, cr:3.50-4.80%, mo:3.80-5.00%, ni:3.00-3.90%, V:0.90-1.60%, mn:0.12-0.45%, si:0.10-0.28%, and the balance of Fe and impurities.
In some embodiments of the invention, the bearing steel has an average grain size of 2 μm or less.
In order to better illustrate the present scheme, the following examples and comparative examples are provided.
Example 1
S1: the ingot casting, ingot mold, 225mm was produced using a Vacuum Induction (VIM) +vacuum consumable (VAR) double vacuum melting process. When Vacuum Induction (VIM) smelting is performed, the vacuum degree is kept to be less than or equal to 5Pa, the melting period time is more than or equal to 3 hours, the furnace burden is refined for 15 minutes to 30 minutes after being completely melted, and the tapping temperature is 1540 ℃ to 1560 ℃. When vacuum is consumed (VAR), keeping the vacuum degree less than or equal to 1Pa, controlling the melting speed to be 1.2 kg/min-2.0 kg/min in the arc-stabilizing stage, and cooling by circulating water after the melting is finished for more than or equal to 6 hours;
s2: homogenizing the cast ingot, and preserving the temperature of the cast ingot at 1100 ℃ for 24 hours;
s3: carrying out multi-pass upsetting on the homogenized cast ingot, wherein the upsetting temperature is 850-1050 ℃, the first heat deformation is 40-45%, the second heat deformation is 65-70%, the third heat deformation is 40-45%, the fourth heat deformation is 15-20%, the furnace returning heat is carried out after each heat, the heat preservation time is 0.5 hour, and the total deformation is controlled to be 75-90%, so that a forging piece is obtained;
s4: the forging is rolled by adopting critical area rolling, the rolling temperature is 900 ℃, three times of rolling are adopted, the deformation amount of the first time is 17-20%, the deformation amount of the second time is 12-17%, the deformation amount of the third time is 7-15%, the rolling is carried out for 10min after each time of deformation, the total deformation amount is 60%, the rolling is cooled to room temperature by adopting an ultra-fast cooling mode after the rolling is finished, an ultra-fast cooling device is arranged at the outlet of a finishing mill group and consists of a plurality of water spraying pillows which are formed by densely arranging spray nozzles, the water supply pressure is increased, the water outlets with high density are arranged, the impact force of water flow on an air film is increased, the high-efficiency heat exchange between fresh water and the surface of a hot steel plate in unit time is realized, the cooling speed is more than or equal to 100 ℃/s, and the grain structure diagram of the obtained bearing steel is shown in figure 2, and the average grain size is less than or equal to 1.4 mu m.
The bearing steel comprises the following chemical components in percentage by weight: c:0.14%, cr:4.10%, mo:4.20%, ni:3.36%, V:1.10%, mn:0.23%, si:0.18%, the balance being Fe and unavoidable impurities.
Example 2
S1: the ingot casting, ingot mold, 225mm was produced using a Vacuum Induction (VIM) +vacuum consumable (VAR) double vacuum melting process. When Vacuum Induction (VIM) smelting is performed, the vacuum degree is kept to be less than or equal to 5Pa, the melting period time is more than or equal to 3 hours, the furnace burden is refined for 15 minutes to 30 minutes after being completely melted, and the tapping temperature is 1540 ℃ to 1560 ℃. When vacuum is consumed (VAR), keeping the vacuum degree less than or equal to 1Pa, controlling the melting speed to be 1.2 kg/min-2.0 kg/min in the arc-stabilizing stage, and cooling by circulating water after the melting is finished for more than or equal to 6 hours;
s2: homogenizing the cast ingot, and preserving the temperature of the cast ingot at 1100 ℃ for 48 hours;
s3: carrying out multi-pass upsetting on the homogenized cast ingot, wherein the upsetting temperature is 850-1050 ℃, the first heat deformation is 40-45%, the second heat deformation is 65-75%, the third heat deformation is 45-50%, the fourth heat deformation is 20-30%, the furnace returning heat is carried out after each heat, the heat preservation time is 0.5 hour, and the total deformation is controlled to be 80-95%, so that a forging piece is obtained;
s4: the forging is rolled by adopting critical area rolling, rolling temperature is 800 ℃, four passes of rolling are adopted, the deformation amount of the first pass is 17-20%, the deformation amount of the second pass is 12-17%, the deformation amount of the third pass is 7-15%, the rolling is carried out for 15min after each pass of deformation, the total deformation amount is 70%, the rolling is cooled to room temperature by adopting an ultra-fast cooling mode after the rolling is finished, an ultra-fast cooling device is arranged at the outlet of a finishing mill group and consists of a plurality of water spraying pillows which are formed by densely arranging spray nozzles, water supply pressure is increased, water outlets with high density are arranged, the impact force of water flow on a gas film is increased, the surface of a new water and a hot steel plate in unit time is subjected to high-efficiency heat exchange, the cooling speed is more than or equal to 100 ℃/s, and the grain structure diagram of the obtained bearing steel is shown in figure 3, and the average grain size is less than or equal to 1.9 mu m.
The bearing steel comprises the following chemical components in percentage by weight: c:0.14%, cr:4.10%, mo:4.20%, ni:3.36%, V:1.10%, mn:0.23%, si:0.18%, the balance being Fe and unavoidable impurities.
Comparative example
S1: the ingot casting, ingot mold, 225mm was produced using a Vacuum Induction (VIM) +vacuum consumable (VAR) double vacuum melting process.
S2: homogenizing the cast ingot, and preserving the temperature of the cast ingot at 1100 ℃ for 48 hours;
s3: and (3) carrying out multi-pass forging on the homogenized cast ingot, wherein the deformation of each pass is controlled to be 7% -20%, the total deformation of forging is 80% -90%, and the grain structure diagram of the obtained bearing steel is shown in figure 4, and the average grain size is less than or equal to 88 mu m.
The bearing steel comprises the following chemical components in percentage by weight: 0.12% of C, 3.96% of Cr, 4.22% of Mo, 3.53% of Ni, 1.09% of V, 0.16% of Mn, si:0.27% of Fe and the balance of unavoidable impurities.
In summary, the average grain size of the bearing steel manufactured by the comparative example is less than or equal to 88 mu m, and the method realizes the grain refinement of the high-temperature bearing steel, obtains an ultrafine grain structure with the grain size less than or equal to 2 mu m, and has important significance for improving the toughness of the material and refining the structure of the heat treatment of the subsequent carburization treatment.
Finally, it should be noted that: the foregoing description is only illustrative of the preferred embodiments of the present invention, and although the present invention has been described in detail with reference to the foregoing embodiments, it will be apparent to those skilled in the art that modifications may be made to the embodiments described, or equivalents may be substituted for elements thereof, and any modifications, equivalents, improvements or changes may be made without departing from the spirit and principles of the present invention.

Claims (5)

1. The preparation method of the ultra-fine grain high temperature carburized bearing steel is characterized by comprising the following steps:
preparing an ingot by adopting double vacuum smelting;
homogenizing the cast ingot;
forging the homogenized cast ingot to obtain a forging;
carrying out multi-pass critical zone rolling on the forging to obtain bearing steel;
the bearing steel comprises the following chemical components in percentage by weight: c:0.10-0.16%, cr:3.50-4.80%, mo:3.80-5.00%, ni:3.00-3.90%, V:0.90-1.60%, mn:0.12-0.45%, si:0.10-0.28%, and the balance of Fe and impurities;
the technological parameters of the homogenization treatment comprise: the heating temperature is 1100-1200 ℃, and the heat preservation time is more than or equal to 24 hours;
the forging of the homogenized cast ingot comprises the following steps:
carrying out repeated upsetting deformation on the cast ingot, wherein the upsetting temperature is 850-1050 ℃, the deformation amount of the first heat is 40-55%, the deformation amount of the second heat is 60-75%, the deformation amount of the third heat is 40-55%, the deformation amount of the fourth heat is 15-30%, and the heat preservation time is more than or equal to 0.5 hours after each heat is returned to the furnace;
the process parameters of critical zone rolling comprise: the rolling temperature is 750-900 ℃, the deformation amount of each pass is 7-20%, the furnace is returned to keep the temperature for 10-30min after each pass of deformation, and then the next pass of rolling is carried out, and the total deformation amount is controlled to be 60-80%;
after the forging is rolled in a multi-pass critical zone, the method comprises the following steps:
and cooling the rolled forging to room temperature in an ultra-fast cooling mode to obtain the bearing steel.
2. The method for preparing ultra-fine grain high temperature carburized bearing steel according to claim 1, wherein the preparing of the ingot by double vacuum melting comprises:
and adopting vacuum induction melting and vacuum consumable melting to prepare cast ingots.
3. An ultra-fine grain high temperature carburized bearing steel produced by the method of any one of claims 1-2.
4. An ultra-fine grain high temperature carburized bearing steel according to claim 3, wherein the bearing steel comprises the following chemical components in weight percent: c:0.10-0.16%, cr:3.50-4.80%, mo:3.80-5.00%, ni:3.00-3.90%, V:0.90-1.60%, mn:0.12-0.45%, si:0.10-0.28%, and the balance of Fe and impurities.
5. An ultra-fine grain high temperature carburized bearing steel according to claim 3, wherein the bearing steel has an average grain size of 2 μm or less.
CN202311111334.1A 2023-08-31 2023-08-31 Superfine crystal high temperature carburized bearing steel and manufacturing method thereof Active CN116837192B (en)

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Citations (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103122433A (en) * 2013-01-31 2013-05-29 西安交通大学 Ultrahigh-carbon type bearing steel
KR101623661B1 (en) * 2014-12-31 2016-05-23 두산중공업 주식회사 Ultra thick steel plate and manufacturing method for offshore structure having ultra-high strength and high toughness
CN107099767A (en) * 2017-06-05 2017-08-29 长沙天和钻具机械有限公司 A kind of explosion drill bit Technology for Heating Processing
CN107974542A (en) * 2017-10-24 2018-05-01 昆明理工大学 A kind of grain refining preparation method of nickel-saving type two phase stainless steel
CN110423955A (en) * 2019-07-29 2019-11-08 中国航发北京航空材料研究院 The heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer and preparation method
CN110527911A (en) * 2019-09-16 2019-12-03 北京航空航天大学 Anti-corrosion gear-bearing steel of a kind of low-density high-strength height and preparation method thereof
CN111893381A (en) * 2020-07-18 2020-11-06 钢铁研究总院 High-nitrogen stainless bearing steel and preparation method thereof
CN111940522A (en) * 2020-05-19 2020-11-17 中国航发北京航空材料研究院 Method for processing high-strength cobalt-based GH6159 alloy cold-drawn material for aircraft engine fastener
CN112063921A (en) * 2020-08-10 2020-12-11 上海交通大学 Air-cooled hardened steel plate with ultrahigh-strength high-toughness ultrafine structure and preparation process thereof
CN113201698A (en) * 2021-04-30 2021-08-03 钢铁研究总院 High-temperature bearing steel and clean and uniform preparation method thereof
CN113564496A (en) * 2021-07-22 2021-10-29 中国铁道科学研究院集团有限公司金属及化学研究所 Long-life railway bearing steel and preparation method thereof
CN113718174A (en) * 2021-08-21 2021-11-30 钢铁研究总院 Double-refined high-strength-toughness long-life medium-high carbon bearing steel and preparation method thereof
EP3940089A1 (en) * 2020-07-16 2022-01-19 Central Iron & Steel Research Institute Carburizing bearing steel and preparation method thereof
CN114032470A (en) * 2022-01-07 2022-02-11 北京科技大学 Carburizing bearing steel and preparation method thereof
CN114318167A (en) * 2021-12-15 2022-04-12 中国航发北京航空材料研究院 Ultra-high strength and high toughness precipitation hardening type carburizing steel and preparation method thereof
CN114318168A (en) * 2021-12-15 2022-04-12 中国航发北京航空材料研究院 High-strength high-toughness carbonitriding steel and preparation method thereof
CN114351053A (en) * 2022-01-13 2022-04-15 鞍钢股份有限公司 Superfine crystal high-toughness wear-resistant steel and manufacturing method thereof
CN114393056A (en) * 2021-12-24 2022-04-26 西北工业大学 Aeronautical high-temperature alloy plate structure and shape control method
CN114632901A (en) * 2022-03-18 2022-06-17 西安聚能高温合金材料科技有限公司 Preparation method of high-temperature alloy free forging bar blank for ultra-supercritical thermal power generating unit
CN114918271A (en) * 2022-03-18 2022-08-19 西安聚能高温合金材料科技有限公司 GH4169 high-temperature alloy hot-rolled bar billet and preparation method thereof
CN115449613A (en) * 2022-08-23 2022-12-09 成都先进金属材料产业技术研究院股份有限公司 Carburizing bearing steel and preparation method thereof
CN116065010A (en) * 2022-12-16 2023-05-05 成都先进金属材料产业技术研究院股份有限公司 Homogenization treatment method for ultra-high strength maraging steel

Patent Citations (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103122433A (en) * 2013-01-31 2013-05-29 西安交通大学 Ultrahigh-carbon type bearing steel
KR101623661B1 (en) * 2014-12-31 2016-05-23 두산중공업 주식회사 Ultra thick steel plate and manufacturing method for offshore structure having ultra-high strength and high toughness
CN107099767A (en) * 2017-06-05 2017-08-29 长沙天和钻具机械有限公司 A kind of explosion drill bit Technology for Heating Processing
CN107974542A (en) * 2017-10-24 2018-05-01 昆明理工大学 A kind of grain refining preparation method of nickel-saving type two phase stainless steel
CN110423955A (en) * 2019-07-29 2019-11-08 中国航发北京航空材料研究院 The heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer and preparation method
CN110527911A (en) * 2019-09-16 2019-12-03 北京航空航天大学 Anti-corrosion gear-bearing steel of a kind of low-density high-strength height and preparation method thereof
CN111940522A (en) * 2020-05-19 2020-11-17 中国航发北京航空材料研究院 Method for processing high-strength cobalt-based GH6159 alloy cold-drawn material for aircraft engine fastener
EP3940089A1 (en) * 2020-07-16 2022-01-19 Central Iron & Steel Research Institute Carburizing bearing steel and preparation method thereof
CN111893381A (en) * 2020-07-18 2020-11-06 钢铁研究总院 High-nitrogen stainless bearing steel and preparation method thereof
CN112063921A (en) * 2020-08-10 2020-12-11 上海交通大学 Air-cooled hardened steel plate with ultrahigh-strength high-toughness ultrafine structure and preparation process thereof
CN113201698A (en) * 2021-04-30 2021-08-03 钢铁研究总院 High-temperature bearing steel and clean and uniform preparation method thereof
CN113564496A (en) * 2021-07-22 2021-10-29 中国铁道科学研究院集团有限公司金属及化学研究所 Long-life railway bearing steel and preparation method thereof
CN113718174A (en) * 2021-08-21 2021-11-30 钢铁研究总院 Double-refined high-strength-toughness long-life medium-high carbon bearing steel and preparation method thereof
CN114318167A (en) * 2021-12-15 2022-04-12 中国航发北京航空材料研究院 Ultra-high strength and high toughness precipitation hardening type carburizing steel and preparation method thereof
CN114318168A (en) * 2021-12-15 2022-04-12 中国航发北京航空材料研究院 High-strength high-toughness carbonitriding steel and preparation method thereof
CN114393056A (en) * 2021-12-24 2022-04-26 西北工业大学 Aeronautical high-temperature alloy plate structure and shape control method
CN114032470A (en) * 2022-01-07 2022-02-11 北京科技大学 Carburizing bearing steel and preparation method thereof
CN114351053A (en) * 2022-01-13 2022-04-15 鞍钢股份有限公司 Superfine crystal high-toughness wear-resistant steel and manufacturing method thereof
CN114632901A (en) * 2022-03-18 2022-06-17 西安聚能高温合金材料科技有限公司 Preparation method of high-temperature alloy free forging bar blank for ultra-supercritical thermal power generating unit
CN114918271A (en) * 2022-03-18 2022-08-19 西安聚能高温合金材料科技有限公司 GH4169 high-temperature alloy hot-rolled bar billet and preparation method thereof
CN115449613A (en) * 2022-08-23 2022-12-09 成都先进金属材料产业技术研究院股份有限公司 Carburizing bearing steel and preparation method thereof
CN116065010A (en) * 2022-12-16 2023-05-05 成都先进金属材料产业技术研究院股份有限公司 Homogenization treatment method for ultra-high strength maraging steel

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