CN115011872A - Manufacturing method of cold-drawn round steel bar for high-dimensional stability hydraulic valve core - Google Patents
Manufacturing method of cold-drawn round steel bar for high-dimensional stability hydraulic valve core Download PDFInfo
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/0056—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00 using cored wires
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/04—Removing impurities by adding a treating agent
- C21C7/06—Deoxidising, e.g. killing
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/10—Handling in a vacuum
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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Abstract
The invention relates to a method for manufacturing a cold-drawn round steel bar for a high-dimensional stability hydraulic valve core, wherein the diameter range of a hot-rolled wire rod in the method is 5.5-25 mm. The production process flow comprises the following steps: converter or electric furnace smelting, LF refining, RH or VD degassing, continuous casting, blank surface treatment, high-temperature wire rolling and spinning, controlled cooling and cold drawing. The cold-drawn round steel rod for the hydraulic valve core produced by the invention has excellent dimensional stability in the subsequent machining and surface heat treatment processes, and can cancel the normalizing process of the hot-rolled wire rod and avoid surface decarburization caused by the normalizing process. The whole process comprehensively achieves low cost and high quality production of hot rolled wire rods and cold drawn round steel rods for the hydraulic valve core, and achieves the purposes of energy conservation and consumption reduction.
Description
Technical Field
The present invention relates to a method for manufacturing round steel, and more particularly to a method for manufacturing a round steel rod suitable for cold drawing.
Background
In a hydraulic valve, the movement of the control mechanism needs to be achieved by controlling the movement of the hydraulic spool. The hydraulic valve core does continuous linear reciprocating motion in the hydraulic valve. This requires excellent concentricity and surface wear resistance of the hydraulic valve spool. The production process of the hydraulic valve core comprises the following steps: machining by a core-moving machine, namely, carburizing or nitriding, surface heat treatment and surface fine grinding. Because the hydraulic valve core is usually a slender part with a complex shape, the phenomenon of size fluctuation or over-standard bending degree is easy to occur in the carburized or nitrided surface heat treatment process, and the part is scrapped in processing. At present, the common method for solving the problem is to carry out off-line normalizing on the steel for the hydraulic valve core before machining, the off-line normalizing can increase the decarburization on the surface of cold-drawn round steel, the amount of cuttings on the surface of the round steel needs to be increased correspondingly after the normalizing, and the off-line normalizing is energy waste, so that the production cost of the steel bar for the hydraulic valve core is increased.
Therefore, the cold-drawn round steel bar for the hydraulic valve core with higher dimensional stability is developed, and the heat treatment of off-line normalizing can be saved.
Disclosure of Invention
The invention aims to provide a manufacturing method of a cold-drawn round steel bar for a high-dimensional stability hydraulic valve core, which is used for improving the dimensional stability of the round steel bar after carburization or nitriding surface heat treatment, realizing low-cost and high-quality production of a hot-rolled wire rod and a cold-drawn round steel bar for the hydraulic valve core and achieving the purposes of energy conservation and consumption reduction.
The technical scheme adopted by the invention for solving the problems is as follows: a manufacturing method of a hot-rolled wire rod for a high-dimensional stability hydraulic valve core comprises the following steps:
step one, designing element components: the weight percentage of C: 0.13-0.18%, Si: 0.15-0.35%, Mn: 0.60-0.90%, P: less than or equal to 0.030 percent, S: 0.015-0.020%, Cr: 0.90-1.20%, Mo: 0.15-0.25%, Al 0.030-0.040%, N: 0.0060% -0.0200%, the rest is Fe and inevitable impurity elements;
step two, smelting molten steel: smelting molten steel according to the element components in the step one, wherein the smelting comprises primary smelting, refining and vacuum degassing;
step three, casting: casting the molten steel in the step two into a steel billet;
step four, rolling a steel billet: the method comprises a heating process and a rolling process, wherein a small amount of AlN begins to be separated out in the heating process, the temperature of a temperature equalizing section is controlled to be 1000-1200 ℃, and the heating time of the temperature equalizing section is within the range of 30-50min, so that the growth of AlN particles is prevented; heating a steel billet, descaling by high-pressure water, rolling, wherein the rolling comprises rough rolling, intermediate rolling, pre-finish rolling and finish rolling, the rough rolling temperature is controlled to be 1000 ℃ plus 900 ℃, the intermediate rolling temperature and the pre-finish rolling temperature are controlled to be 950 ℃ plus 900 ℃, the spinning temperature is controlled to be 950 ℃ plus 900 ℃, and the specification of a wire rod is 5.5-25 mm;
step five, cooling after rolling: the rolled wire rod is quickly cooled and passes through a high-temperature area at a cooling speed of 1.5-6 ℃/s, the surface of the wire rod is controlled not to generate a full decarburized layer, the depth of the total decarburized layer is controlled within 0.7 percent D, and D represents the diameter of the wire rod; and (3) starting slow cooling when the temperature is reduced to 700-.
Preferably, in the second step, the primary smelting is converter or electric furnace smelting, and during tapping, slag charge, alloy blocks and a deoxidizer are added along the steel flow; refining is LF refining, and nitrogen is added into molten steel to supplement nitrogen to the molten steel after the refining is finished or close to the refining is finished; nitrogen was used as the lift gas or low blow gas for vacuum degassing.
Preferably, a continuous casting process is adopted in the third step, the molten steel in the second step is transferred to a tundish to be cast into a continuous casting blank, the superheat degree of the molten steel is controlled at 15-40 ℃, argon is adopted for protection in the whole continuous casting process to prevent the molten steel from contacting oxygen, and the continuous casting blank is subjected to flame cutting and then is subjected to stack cooling or lower slow cooling pit cooling.
Preferably, in the fourth step, the heating is carried out by adopting a stepping heating furnace, the temperature of the preheating section of the heating furnace is controlled to be less than or equal to 650 ℃, the temperature of the heating and temperature-equalizing section of the heating furnace is controlled to be 1000-1200 ℃, and the total heating time is controlled to be 90-160 min.
Preferably, in the fifth step, the rolled wire rod is cooled in a stelmor cooling line, 4-6 heat-insulating covers are opened at the front section of the heat-insulating cover of the cooling line, the rear heat-insulating cover is closed completely, the speed of a roller way is 0.15-0.3m/s, the air quantity is opened by more than 20% by the first 4-6 fans to carry out quick cooling, the residence time of the wire rod in a high-temperature state is shortened to control decarburization, the wire rod enters the heat-insulating cover to carry out slow cooling after the quick cooling is finished, and austenite is decomposed into ferrite and pearlite in the slow cooling process and is accompanied with the generation of point-like carbides.
The cold-drawn round steel rod is obtained by cold-drawing the wire rod obtained by the method, the drawing reduction rate is set to be 5% -15%, the preferable rate is 8%, straightening is carried out after drawing, and the bending run-out of the whole cold-drawn round steel rod is controlled within 0.3 mm/m. For better cold drawing, the hot rolled wire rod is pickled and lubricated before drawing.
The characteristics that this application has include:
(1) the addition of a certain amount of sulfur to steel can improve the cutting performance of steel, but the upper limit of the sulfur content is limited, and excessive sulfur content easily increases the brittleness of the material, which is not favorable for drawing. In addition, aluminum and nitrogen are added into the steel in a certain proportion, AlN precipitates are formed in the rolling process, austenite crystal boundaries are pinned, and therefore the hydraulic valve core can be effectively prevented from being coarse in crystal grains in the surface heat treatment process, and the size deformation of parts is reduced.
(2) The final structure of the wire rod is ferrite + lamellar pearlite + a small amount of punctate carbide, is similar to an equilibrium structure, and the structure is formed by decomposing austenite into ferrite + pearlite structure in the slow cooling process in the cover. The formation of the point-like carbides remains during the heating of austenite, and also precipitates at individual points during the subsequent cooling. Its presence has no effect on the performance of the wire rod.
(3) According to the method, a high-temperature rolling process is adopted, AlN is separated out during high-temperature rolling, the stability of austenite is improved, the decomposition potential energy behind the austenite is increased, unstable structures such as bainite are prevented from being generated, the internal stress is reduced, and the decomposed structures tend to be in a balanced state as much as possible.
(4) The hot-rolled wire rod can improve the processability and the dimensional stability after carburization or nitriding heat treatment in a further hydraulic valve core processing procedure of a round steel plate obtained by cold drawing.
Compared with the prior art, the invention has the advantages that: the Al and N elements are added into the existing steel, and the control of high-temperature rolling, high-temperature spinning and fast-first-then-slow cooling process is combined. By adopting the high-temperature rolling and high-temperature spinning processes, the wire rod can obtain uniform austenite grains with the actual austenite grain size of 5-6 grades after rolling. And the combination of a blank heating process and a cooling process of firstly fast and secondly slow after wire rod spinning ensures that Al and N added in steel can form fine and dispersed AlN particles to pin the original austenite grain boundary. The stable austenite grain size of the hydraulic valve core in the carburizing heat treatment is ensured. The metallographic structure of the wire rod is consistent with that after the normalizing heat treatment, and the additional decarburization brought by the offline heat treatment can be reduced compared with that of the offline normalizing heat treatment. Not only can the off-line normalizing be cancelled, but also the cold-drawn round steel surface peeling process can be cancelled, and the size and the bending deformation of the hydraulic valve core in the machining and surface heat treatment processes can be ensured.
Drawings
FIG. 1 is a microstructure of a hot rolled wire rod according to an example of the present invention, which shows an equilibrium state of ferrite and pearlite and a point carbide.
Detailed Description
The present invention is further described in detail with reference to the following examples, which are illustrative and should not be construed as limiting the technical solutions of the present application.
Example 1
The embodiment relates to a method for producing a cold-drawn round steel bar for a high-dimensional stability hydraulic valve core, which comprises the following steps of: c: 0.15%, Si: 0.22%, Mn: 0.75%, P: less than or equal to 0.013%, S: less than or equal to 0.016 percent, Cr: 1.05%, Mo: 0.18%, Al 0.03%, N: 0.0120 percent, and the balance of Fe and inevitable impurity elements. The diameter of the wire rod is 12mm, and the process flow is as follows: the main raw materials are sequentially subjected to converter smelting, LF + RH external refining, refining and feeding a nitrogen increasing line, and nitrogen is used as lifting gas. And casting the molten steel into a continuous casting blank by adopting 15-30 ℃ low superheat degree whole-process argon protection, and performing surface treatment after the blank is slowly cooled to remove surface defects. After treatment, the blank is heated to 1150 ℃ in a heating furnace, the total heating time is 120min, the blank is discharged from the furnace, the rolling temperature is 980 ℃, the middle rolling temperature is 920 ℃, the pre-finishing rolling temperature is 930 ℃, the finishing rolling temperature is 930 ℃, and the spinning temperature is 930 ℃. Stelmor is cooled, the speed of a roller way is set to be 0.15m/s, 4 heat preservation covers at the front section are opened, the air quantity of a fan is all opened to 20%, the heat preservation cover at the rear section is completely closed, the temperature of the wire rod entering the heat preservation cover is 780 ℃, and the temperature of the wire rod exiting the heat preservation cover is 480 ℃. And (5) cooling by stelmor, collecting, taking off the production line, and cooling by air. After the combined drawing and uncoiling and straightening, the drawing reduction rate is 8 percent. The bending run-out of the whole cold-drawn round steel bar can be controlled within 0.3 mm/m.
Example 2
The embodiment relates to a method for producing a cold-drawn round steel bar for a high-dimensional stability hydraulic valve core, which comprises the following steps of: c: 0.16%, Si: 0.20%, Mn: 0.75%, P: less than or equal to 0.013%, S: less than or equal to 0.018%, Cr: 1.05%, Mo: 0.18%, Al 0.035%, N: 0.0180 percent, and the balance of Fe and inevitable impurity elements. The diameter of the wire rod is 14mm, and the process flow is as follows: the main raw materials are sequentially subjected to converter smelting, LF + RH furnace number refining, refining and feeding a nitrogen increasing line, and nitrogen is used as lifting gas. And casting the molten steel into a continuous casting blank by adopting 15-30 ℃ low superheat degree whole-process argon protection, carrying out surface treatment after the blank is slowly cooled, and peeling to remove surface defects. After treatment, the blank is heated to 1180 ℃ in a heating furnace, the blank is taken out of the furnace after the total heating time is 120min, the temperature of a soaking section is kept for 20min, the rolling temperature is 1000 ℃, the middle rolling temperature is 940 ℃, the pre-finish rolling temperature is 930 ℃, the finish rolling temperature is 950 ℃, and the spinning temperature is 940 ℃.
Cooling on a stelmor cooling line, wherein the speed of a roller way is 0.20m/s, the front 5 heat-preserving covers are opened, the air volume of a fan is 20%, the temperature of the wire rod entering the heat-preserving cover is 790 ℃, and the temperature of the wire rod exiting the heat-preserving cover is 500 ℃. And (5) cooling the collected wire rods by stelmor, and taking the wire rods off the line for air cooling. After the combined drawing and uncoiling and straightening, the drawing reduction rate is 10 percent. The bending run-out of the whole cold-drawn round steel bar is within 0.3 mm/m.
TABLE 1 mechanical Properties of wire rods of examples 1 and 2
| Tensile strength MPa | Hardness HV1 | |
| Example 1 | 613 | 191 |
| Example 2 | 640 | 200 |
Comparative example with off-line normalization
Chemical composition C of hot-rolled wire rod: 0.16%, Si: 0.24%, Mn: 0.79%, P: less than or equal to 0.018%, S: less than or equal to 0.016%, Cr: 1.13%, Mo: 0.17%, Al 0.020%, N: 0.0050%, and the balance of Fe and inevitable impurity elements. The diameter of the wire rod is 12mm, and the process flow is as follows: and performing similar smelting continuous casting, and performing surface treatment after slowly cooling the blank. After treatment, the blank is heated to 1100 ℃ in a heating furnace at 1020 ℃ and the temperature is kept for 160min at 120 ℃ and the blank is taken out of the furnace at the rolling start temperature of 920 +/-30 ℃, the middle rolling temperature of 900 +/-30 ℃, the pre-finish rolling temperature of 880 +/-20 ℃, the finish rolling temperature of 880 +/-20 ℃ and the spinning temperature of 860 +/-10 ℃. The wire rod is uncoiled into a rod after off-line normalizing, and the surface of the rod is delivered after peeling or straightening by turning (removing a surface decarburized layer generated by normalizing).
Although preferred embodiments of the present invention have been described in detail hereinabove, it should be clearly understood that modifications and variations of the present invention are possible to those skilled in the art. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (7)
1. A manufacturing method of a hot-rolled wire rod for a high-dimensional stability hydraulic valve core is characterized by comprising the following steps of: comprises the steps of (a) preparing a mixture of a plurality of raw materials,
step one, designing element components: the weight percentage of C: 0.13-0.18%, Si: 0.15-0.35%, Mn: 0.60-0.90%, P: less than or equal to 0.030%, S: 0.015-0.020%, Cr: 0.90-1.20%, Mo: 0.15-0.25%, Al 0.030-0.040%, N: 0.0060% -0.0200%, the rest is Fe and inevitable impurity elements;
step two, smelting molten steel: smelting molten steel according to the element components in the step one, wherein the smelting comprises primary smelting, refining and vacuum degassing;
step three, casting: casting the molten steel in the second step into a steel billet;
step four, rolling the steel billet: the method comprises a heating process and a rolling process, wherein a small amount of AlN begins to be separated out in the heating process, the temperature of a temperature equalizing section is controlled to be 1000-1200 ℃, and the heating time of the temperature equalizing section is within the range of 30-50min, so that the growth of AlN particles is prevented; heating a steel billet, descaling by high-pressure water, rolling, wherein the rolling comprises rough rolling, intermediate rolling, pre-finish rolling and finish rolling, the rough rolling temperature is controlled to be 1000 ℃ plus 900 ℃, the intermediate rolling temperature and the pre-finish rolling temperature are controlled to be 950 ℃ plus 900 ℃, the spinning temperature is controlled to be 950 ℃ plus 900 ℃, and the specification of a wire rod is 5.5-25 mm;
step five, cooling after rolling: the rolled wire rod is quickly cooled and passes through a high-temperature area at a cooling speed of 1.5-6 ℃/s, the surface of the wire rod is controlled not to generate a full decarburized layer, the depth of the total decarburized layer is controlled within 0.7 percent D, and D represents the diameter of the wire rod; and (3) starting slow cooling when the temperature is reduced to 700-.
2. The method of claim 1, wherein: in the second step, the primary smelting is converter or electric furnace smelting, and during tapping, slag charge, alloy blocks and deoxidizer are added along the steel flow; refining is LF refining, and nitrogen is added into molten steel to supplement nitrogen to the molten steel after the refining is finished or close to the refining is finished; nitrogen was used as the lift gas or low blow gas for vacuum degassing.
3. The method of claim 1, wherein: and step three, adopting a continuous casting process, transferring the molten steel in the step two to a tundish to cast the molten steel into a continuous casting blank, controlling the superheat degree of the molten steel at 15-40 ℃, adopting argon protection in the whole continuous casting process to prevent the molten steel from contacting oxygen, and cooling the continuous casting blank in a pile cooling mode or a lower slow cooling pit after flame cutting.
4. The method of claim 1, wherein: and step four, heating by adopting a stepping heating furnace, wherein the temperature of the preheating section of the heating furnace is controlled to be less than or equal to 650 ℃, the temperature of the heating and temperature-equalizing section of the heating furnace is controlled to be 1000-1200 ℃, and the total heating time is controlled to be 90-160 min.
5. The method of claim 1, wherein: and step five, cooling the rolled wire rod on a stelmor cooling line, opening 4-6 heat-insulating covers at the front section of the heat-insulating cover of the cooling line, fully closing the heat-insulating cover at the back, controlling decarburization by shortening the retention time of the wire rod in a high-temperature state and controlling decarburization by opening more than 20% of air volume by using the first 4-6 fans, entering the heat-insulating cover for slow cooling after the fast cooling is finished, and decomposing austenite into ferrite and pearlite in the slow cooling process accompanied with generation of point-like carbides.
6. The manufacturing method of the cold-drawn round steel bar for the high-dimensional stability hydraulic valve core is characterized by comprising the following steps of: the wire rod obtained by the method of claim 1 is subjected to cold drawing, the draw reduction rate is set to be 5% -15%, and the cold-drawn round steel rod is prepared.
7. The method of claim 6, wherein: the drawdown reduction rate was 8%.
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| CN115466838A (en) * | 2022-09-21 | 2022-12-13 | 河南中原特钢装备制造有限公司 | Cooling method for controlling steel precipitate for non-magnetic drill collar |
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| CN115011872B (en) | 2023-06-16 |
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