CN113083936A - High-carbon chromium bearing steel wire rod with diameter less than or equal to 10mm and capable of meeting large-area-reduction-rate hot rolling straight pulling and production method thereof - Google Patents
High-carbon chromium bearing steel wire rod with diameter less than or equal to 10mm and capable of meeting large-area-reduction-rate hot rolling straight pulling and production method thereof Download PDFInfo
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- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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Abstract
The invention relates to a high-carbon chromium bearing steel wire rod with the diameter less than or equal to 10mm and meeting the requirement of hot rolling straight pulling with large reduction ratio and a production method thereof, and the production flow is as follows: KR molten iron treatment, converter smelting, LF refining, RH refining, continuous casting of a bloom, blooming by primary rolling, heating, controlled rolling and slow cooling. By using a large-compression-ratio cogging to control the core performance of the base metal blank, under the condition of obtaining a high-quality base metal blank, a high linear speed (the speed is about 90-110 m/s) controlled rolling and cooling continuous production process is adopted, so that a hot-rolled bearing steel wire rod obtains a pre-spheroidized structure, the tensile strength of the wire rod is 1150-1300 MPa, the reduction of area is 25-45%, the net shape of carbide is less than or equal to 2.0 grade, finally, the bearing steel wire rod with low strength, high plasticity and obviously improved net-shaped carbide can be directly drawn with a large reduction ratio (more than or equal to 60%), the later spheroidizing annealing time is shortened, the energy is saved, the environment is protected, the service life of a rolling body is prolonged, and a large amount of.
Description
Technical Field
The invention belongs to a production method of alloy steel wires, and particularly relates to a production method of a high-carbon chromium bearing steel wire.
Background
High carbon chromium bearing steel is one of the most widely used bearing steels, the most common steel grade for the manufacture of bearings and bearing parts. The bearing steel belongs to hypereutectoid steel due to the high carbon content, the hot rolled wire produced according to the current normal rolling process generally has high strength of about 1300MPa to 1500MPa, the low plastic section shrinkage is only 5 percent to 10 percent, the wire cannot adapt to the drawing with large reduction ratio, the tissues are all reticular carbide and lamellar pearlite, the deformation resistance is large, and therefore, the subsequent plastic processing of the hot rolled wire of the bearing steel needs spheroidizing annealing treatment to soften the material. The net-shaped carbide of the bearing steel is excessive secondary carbide which is precipitated along the boundaries of austenite grains and distributed in a net shape, the existence of the net-shaped carbide reduces the binding force of a metal matrix, increases the brittleness of the steel, reduces the mechanical property of the bearing steel, and shortens the service life of the bearing steel, so the net-shaped carbide of the bearing steel must be strictly controlled.
At present, researchers have more control over the net-shaped carbide of a bearing steel hot-rolled wire rod, but basically aim at products with phi specification larger than 10mm, the control is only limited to metallographic phase, and the net-shaped improvement of the carbide is not studied by microscopic scanning of an electron microscope; there have been few studies on the development of hot rolled materials that can be directly drawn and serve subsequent processes by shortening the time for subsequent spheroidizing annealing.
The patent application number CN01113948.X discloses a high-carbon chromium bearing steel wire rod for direct drawing and a manufacturing method thereof, the production process comprises an electric furnace and die casting production blank, the produced bearing steel wire rod has high nitrogen content, the strength of the wire rod produced according to the process is more than 1350MPa, the structure of the wire rod is flaky pearlite and sorbite, the wire rod is easy to cause high wire drawing hardening coefficient during the subsequent drawing, the speed is slow and the wire is easy to break during the drawing with large area reduction rate, the adopted die casting production blank mode has the defects of serious pollution and low production efficiency, and the wire rod is gradually not suitable for the clean production requirement of industrial development.
The patent application No. 200910062664.X discloses a method for reducing net-shaped grade of bearing steel wire rod carbide, wherein the final rolling temperature is controlled to be 920-990 ℃, the spinning temperature is controlled to be 760-820 ℃, then air cooling is adopted to control wire rod cooling, although the process can control the net shape of the carbide, the tissue pre-spheroidizing can not be achieved, the plasticity and the strength of a hot-rolled wire rod are reduced, and the cost of the subsequent drawing and spheroidizing process is inconvenient to reduce.
The cost of continuous casting production blank for replacing die casting production blank is lower, the pollution and energy consumption in the production process are also lower, the method for gradually replacing the traditional method depending on die casting production by continuous casting tends to be great, and meanwhile, the whole benefits brought by the whole process and subsequent processing of the product are inevitable, so that the research on the production process of the low-strength high-plasticity excellent-net bearing steel wire rod which is more economic and environment-friendly and is beneficial to the subsequent processing is necessary.
Disclosure of Invention
The invention aims to provide a high-carbon chromium bearing steel wire rod with low strength, high plasticity and good net-shaped carbide and a production method thereof, wherein the performance of the wire rod can be used for direct drawing, and the subsequent spheroidizing annealing time can be shortened. The efficiency of the whole process including wire rod production, wire rod drawing and spheroidizing annealing is improved, and the production cost and the product quality are also improved.
The high-carbon chromium bearing steel wire rod produced by the method has a net shape less than 2.0 grade (evaluated according to GB/T18254), the product can be directly drawn after hot rolling without annealing and drawing, the surface reduction rate of the product can reach more than 60 percent, the service life of the product is prolonged, and the competitiveness of the bearing steel hot rolling wire rod is improved.
The technical scheme adopted by the invention is as follows: a manufacturing process of a high-carbon chromium bearing steel wire rod with the diameter less than or equal to 10mm and meeting the requirement of hot rolling and straight pulling with large reduction ratio comprises the following steps: KR molten iron treatment, converter smelting, LF refining, RH refining, continuous casting of a bloom, blooming by primary rolling, heating, controlled rolling and slow cooling. The method comprises the following specific steps:
(1) smelting molten steel: the process comprises the steps of KR molten iron treatment, converter smelting, LF refining and RH vacuum degassing in sequence, wherein the molten steel comprises the following chemical components in percentage by mass: 0.95-1.0%, Si: 0.15-0.30%, Mn: 0.25-0.45%, P: less than or equal to 0.015 percent, S: less than or equal to 0.008 percent, Al: 0.025-0.045%, Cr: 1.35-1.50%, N: less than or equal to 25ppm, less than or equal to 1.2ppm of H, and the balance of Fe and inevitable impurities;
(2) continuous casting: adopting a continuous casting process to cast the molten steel into a specification of 300 x 340mm2～390*510mm2The continuous casting slab of (1);
(3) initial rolling: cogging and rolling the continuous casting billet into a specification of 140 x 140mm2～175*175mm2The intermediate blank is used as a base material blank, and the base material blank with the low power center porosity of less than or equal to 1.0, the general porosity of less than or equal to 1.0, the ingot type segregation of less than or equal to 1.0 and the center segregation of less than or equal to 1.0(GB/T18254) is obtained through the large compression ratio from the continuous casting blank to the base material blank；
(4) Heating: heating the base material blank at 970 +/-50 ℃ for more than or equal to 60 min;
(5) controlling rolling: firstly, rolling a base material blank into a final wire rod finished product phi through finish rolling, placing the final wire rod finished product phi with the specification of about 1-2 mm (such as a final wire rod with the specification of phi 7mm, wherein the specification of the final wire rod is about phi 8-9 mm), controlling the initial rolling temperature to be 860-plus 1050 ℃, performing finish rolling in an austenite phase region, performing water cooling after finish rolling, cooling a steel billet to 750-plus 820 ℃, then, rolling the steel billet into a wire rod with the phi being less than or equal to 10mm, wherein the rolling phase region for reducing and sizing is austenite plus cementite, a carbide particle can be separated out in the rolling process, performing water cooling again after reducing and sizing, reducing the temperature of the wire rod to 700-800 ℃, spinning to obtain a continuous coil, and a carbide particle can be oozed out in the tissue in the spinning process;
(6) air cooling: air cooling the wire rod after spinning, wherein the air cooling time is controlled to be 10-45 s;
(7) cooling in a heat preservation cover: after air cooling, the temperature of the wire rod is controlled at 600-550 ℃, the wire rod is cooled to 350-550 ℃ and then is taken out of the heat-preservation cover, the austenite precipitates cementite and pearlite structures, and carbide particles formed in the spinning process grow into small balls, so that the pre-spheroidizing effect is achieved;
(8) and (3) directly feeding the wire rods into a slow cooling box after the wire rods are coiled, wherein the slow cooling speed of the slow cooling box is 5-30 ℃/h, and cooling to below 200 ℃.
The production method is characterized in that:
(1) after finishing the finish rolling, water cooling is set, the temperature is cooled to 750-820 ℃, the temperature is an austenite and cementite two-phase region, carbide particles can be separated out during reducing and sizing rolling, and the early-stage pre-spheroidizing effect is achieved.
(2) The reducing sizing mill rolling is used for finally controlling the dimensional precision of the wire rod, and carrying out water penetration cooling again, controlling the spinning temperature to be 700-800 ℃, and controlling the spinning temperature to be in a two-phase region so as to ensure that carbide is continuously precipitated in the spinning process.
(3) And before entering the heat-preservation cover, the temperature is quickly cooled to the cover entering temperature through air cooling, and the air cooling has the function of quickly crossing a secondary carbide precipitation temperature interval to prevent the exceeding of the carbide at the center of the tissue.
(4) Because the front spinning temperature is in a two-phase region, carbide particles can seep out, and the carbide particles gradually grow into small balls by controlling the slow cooling temperature region in the heat-insulating cover, thereby achieving the pre-spheroidizing effect.
(5) After the product is rolled, the product is cooled in a slow cooling box, so that an artificial aging effect is achieved, the plasticity of the material can be improved, and support is provided for the following large-area-reduction-rate drawing.
Compared with the prior art, the application has the advantages that: the high-carbon chromium bearing steel is produced by continuous casting, cogging with large compression ratio controls the core performance of a base metal blank, and under the condition of obtaining a high-quality base metal blank, a continuous production process of rolling and cooling control with high linear speed (the speed is about 90-110 m/s) is carried out, so that a bearing steel wire rod in a hot rolling state obtains a pre-spheroidized structure, the tensile strength of the wire rod is 1150-1300 MPa, the reduction of area is 25-45%, the reticulation of carbide is less than or equal to 2.0 grade, and finally the bearing steel wire rod with low strength, high plasticity and obviously improved reticulation carbide can be directly drawn with large reduction ratio (more than or equal to 60%), the subsequent spheroidizing annealing time is shortened, energy is saved, the environment is protected, the service life of a rolling body is prolonged, and a large amount.
The structure of the final product is disordered lamellar pearlite and cementite irregularly distributed therein, which is particulate carbide produced as a result of pre-spheroidization.
One key point of the production method is that the controlled rolling and controlled cooling process is rolling in a region close to two phases (austenite + cementite), so that the precipitation amount of carbide in an austenite grain boundary is reduced, and carbide particles (carbide-shaped core particles) with cores in the austenite grain boundary are increased, namely secondary carbide precipitation of the austenite grain boundary is reduced, and carbide particles in an austenite tissue are increased; and the steel wire rod enters the heat preservation cover for slow cooling to gradually grow up by utilizing the carbide particles of the residual heat part, so that the tissue pre-spheroidization is achieved, the strength of the wire rod is finally reduced, the plasticity is improved, the direct drawing production of the hot rolled material with large reduction ratio can be realized, the carbide reticulation is controlled, and the fatigue life of the product is prolonged.
Drawings
FIG. 1 is a hot rolled net carbide (500X) gold phase diagram of the wire rod of the present invention;
FIG. 2 is a hot rolled pre-spheroidized structure (2000X) SEM image of the wire rod of the present invention;
FIG. 3 is a SEM image of a hot rolled pre-spheroidized structure (5000X) of the wire rod of the present invention.
Detailed Description
The present invention will be described in further detail below with reference to the attached drawings, which are illustrative and are not to be construed as limiting the invention. The description of the present embodiment is corresponding to the accompanying drawings, and the description related to the orientation is also based on the description of the accompanying drawings, and should not be construed as limiting the scope of the present invention.
Example 1
The specification of the master batch rolled wire rod of the embodiment is phi 5.5mm, and the chemical components are C: 0.95%, Si: 0.25%, Mn: 0.35%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, Al: 0.032%, Cr: 1.42%, N: 22ppm, less than or equal to 1.0ppm of H, and the balance of Fe and inevitable impurities. The center of the master batch of the rolling blank is loosened by 1.0 at low power, the general looseness is 1.0, the ingot type segregation is 1.0, the center segregation is 1.0, and the compression ratio from the continuous casting blank to the rolling master blank is 11.3. The controlled rolling and controlled cooling temperature is as follows: the initial rolling temperature is 860-870 ℃, the final rolling temperature (the temperature of the reducing sizing mill) is 755-765 ℃, the spinning temperature is 735-745 ℃, the temperature of the hot rolled steel wire is 680-690 ℃ through air cooling, the temperature of the hot rolled steel wire is 470-490 ℃ through the hot rolled steel wire, the hot rolled steel wire is rapidly coiled into a slow cooling box and is cooled to 180-190 ℃.
Table 1 example 1 test results:
| sample (I) | Network carbide | Strength MPa | The flour shrinks% |
| Sample 1 | 1.0 | 1168 | 41 |
| Sample 2 | 1.0 | 1174 | 40 |
| Sample 3 | 1.0 | 1176 | 40 |
| Sample 4 | 1.0 | 1186 | 39 |
Drawing production:
after hot rolling the raw material coating, the raw material is directly drawn for 3 times, the drawing process is 5.5mm phi to 4.3mm phi to 3.6mm phi to 3.0mm phi, and the total area reduction rate is 70.25%.
Example 2
The specification of the rolled wire rod of the master batch in the embodiment is phi 6.5mm, and the chemical components are C: 0.96%, Si: 0.26%, Mn: 0.32%, P: less than or equal to 0.012 percent, S: less than or equal to 0.002%, Al: 0.035%, Cr: 1.44%, N: 23ppm, less than or equal to 1.0ppm of H, and the balance of Fe and inevitable impurities. The master batch of the rolling blank is generally loose by 1.0, ingot segregation is 1.0, center segregation is 1.0, and the compression ratio from the continuous casting blank to the rolling master blank is 11.3. The initial rolling temperature is 870-880 ℃, the final rolling temperature is 755-765 ℃, the spinning temperature is 740-750 ℃, the temperature of the spinning is 670-680 ℃ in a heat preservation cover, the temperature of the spinning is 490-510 ℃ after the spinning is out of the heat preservation cover, the spinning is rapidly coiled and enters a slow cooling box, and the spinning is cooled to 170-180 DEG C
Table 2 example 2 test results:
| sample (I) | Network carbide | Strength MPa | The flour shrinks% |
| Sample 1 | 1.0 | 1202 | 36 |
| Sample 2 | 1.0 | 1196 | 36 |
| Sample 3 | 1.0 | 1187 | 38 |
| Sample 4 | 1.0 | 1193 | 37 |
Drawing production:
after hot rolling the raw material coating, the raw material is directly drawn for 3 times, the drawing process is phi 6.5 mm-phi 5.4 mm-phi 4.6mm-4.0mm, and the total area reduction rate is 62.13%.
The two implementation cases are all some contract orders, and the physicochemical indexes are good through inspection, so that the requirements of post-pass processing are met.
In addition to the above embodiments, the present invention also includes other embodiments, and any technical solutions formed by equivalent transformation or equivalent replacement should fall within the scope of the claims of the present invention.
Claims (6)
1. A production method of a high-carbon chromium bearing steel wire rod with the diameter less than or equal to 10mm and meeting the requirement of hot rolling and straight pulling with large reduction ratio comprises the following production processes: KR molten iron treatment, converter smelting, LF refining, RH refining, continuous casting of a bloom, blooming by primary rolling, heating, controlled rolling and slow cooling.
(1) Smelting molten steel: the process comprises the steps of KR molten iron treatment, converter smelting, LF refining and RH vacuum degassing in sequence, wherein the molten steel comprises the following chemical components in percentage by mass: 0.95-1.0%, Si: 0.15-0.30%, Mn: 0.25-0.45%, P: less than or equal to 0.015 percent, S: less than or equal to 0.008 percent, Al: 0.025-0.045%, Cr: 1.35-1.50%, N: less than or equal to 25ppm, less than or equal to 1.2ppm of H, and the balance of Fe and inevitable impurities;
(2) continuous casting: adopting a continuous casting process to cast the molten steel into a specification of 300 x 340mm2～390*510mm2The continuous casting slab of (1);
(3) initial rolling: cogging and rolling the continuous casting billet into a specification of 140 x 140mm2～175*175mm2The intermediate billet of (2) using the intermediate billet as a base material billet;
(4) heating: heating the base material blank to 970 +/-50 ℃ and keeping the total heating time to be more than or equal to 60 min;
(5) controlling rolling: firstly, rolling a base material blank into a final wire rod finished product phi through finish rolling, placing the final wire rod finished product phi into a specification of about 1-2 mm, controlling the initial rolling temperature to be 860-doped 1050 ℃, carrying out finish rolling in an austenite phase region, cooling the steel billet through water after finish rolling to 750-doped 820 ℃, then, rolling the steel billet into a reducing sizing mill, rolling the product into a wire rod with phi being less than or equal to 10mm, wherein the rolling phase region of reducing sizing is austenite plus cementite, carrying out water cooling again after rolling, reducing the temperature of the wire rod to 700-800 ℃, spinning, and enabling the tissue to seep carbide particles in the spinning process;
(6) air cooling: air cooling the wire rod after spinning, wherein the air cooling time is controlled to be 10-45 s;
(7) cooling in a heat preservation cover: when the wire rod is put into the heat-preservation cover, the temperature of the wire rod is controlled to be 600-550 ℃, the wire rod is cooled to be 350-550 ℃, and the wire rod is taken out of the heat-preservation cover, and the mass point of carbide formed in the spinning process grows into small balls, so that the pre-spheroidizing effect is achieved;
(8) after wire rod is coiled, it is directly fed into slow cooling box, and cooled to below 200 deg.C.
2. The production method according to claim 1, characterized in that: and (3) adopting an austenite recrystallization zone for rolling in the initial rolling, wherein the heating temperature of the continuous casting billet is 1230 +/-100 ℃, the heating time is more than or equal to 7h, and then carrying out rough rolling to obtain a base metal blank.
3. The production method according to claim 1, characterized in that: in the step (5), the rolling speed of the wire rod is 90-110 m/s.
4. The production method according to claim 1, characterized in that: and (3) evaluating the base material blank after the initial rolling in the step (3) according to GB/T18254, wherein the low-power central porosity is less than or equal to 1.0, the general porosity is less than or equal to 1.0, the ingot type segregation is less than or equal to 1.0, and the central segregation is less than or equal to 1.0.
5. The production method according to claim 1, characterized in that: the hot-rolled wire rod obtained by the production method has a production specification of phi 4-10 mm.
6. The production method according to claim 1, characterized in that: the hot-rolled wire rod obtained by the production method has the tensile strength of 1150-1300 MPa, the reduction of area of 25-45% and the reticulation of carbide of less than or equal to 2.0 level, can be directly drawn with the reduction of area of more than or equal to 60%, and has a microstructure of disordered flaky pearlite and cementite which are distributed in the pearlite.
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| CN202110223594.2A CN113083936B (en) | 2021-02-25 | 2021-02-25 | High-carbon chromium bearing steel wire rod with diameter less than or equal to 10mm and capable of meeting large-area-reduction-rate hot rolling straight pulling and production method thereof |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114058818A (en) * | 2021-11-02 | 2022-02-18 | 河钢股份有限公司 | Rolling and heat treatment method of 55Ni40Cr3Al bearing steel |
| CN115976422A (en) * | 2023-03-21 | 2023-04-18 | 江苏永钢集团有限公司 | Flexible second phase production control method suitable for bearing steel and application thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN114058818A (en) * | 2021-11-02 | 2022-02-18 | 河钢股份有限公司 | Rolling and heat treatment method of 55Ni40Cr3Al bearing steel |
| CN115976422A (en) * | 2023-03-21 | 2023-04-18 | 江苏永钢集团有限公司 | Flexible second phase production control method suitable for bearing steel and application thereof |
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