CN114150217B - High-purity non-quenched and tempered round steel and preparation method thereof - Google Patents
High-purity non-quenched and tempered round steel and preparation method thereof Download PDFInfo
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/10—Supplying or treating molten metal
- B22D11/11—Treating the molten metal
- B22D11/114—Treating the molten metal by using agitating or vibrating means
- B22D11/115—Treating the molten metal by using agitating or vibrating means by using magnetic fields
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
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- B22D11/1206—Accessories for subsequent treating or working cast stock in situ for plastic shaping of strands
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- 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
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- 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
- 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
- C22C33/06—Making ferrous alloys by melting using master 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
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- 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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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
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Abstract
The invention discloses a preparation method of high-purity non-quenched and tempered round steel, which comprises the steps of EAF smelting, LF refining, VD vacuum, continuous casting, casting blank, heating for dephosphorization and rolling; the LF refining process comprises the steps of feeding aluminum wires into molten steel, and feeding calcium iron wires after the aluminum content of the molten steel is not less than 0.015%; after vacuum breaking in the VD vacuum treatment, blowing in argon for 15-20 min, and then feeding a calcium iron wire again; the continuous casting process uses an electromagnetic stirring soft reduction process. The non-quenched and tempered round steel sulfide segregation and banded structure distribution prepared by the method are obviously superior to those of common non-quenched and tempered steel, so that the quality of the round steel is improved, and meanwhile, the cost of waste steel and the manufacturing cost of parts due to unqualified flaw detection of parts forged by the round steel are reduced.
Description
Technical Field
The invention relates to round steel and a preparation method thereof, in particular to high-purity non-quenched and tempered round steel and a preparation method thereof.
Background
The non-quenched and tempered hot-rolled round steel is a medium-carbon low-alloy structural steel, has equivalent comprehensive mechanical properties to quenched and tempered heat-treated steel materials such as 40Cr, 42CrMo and the like in a cold control state after hot rolling or hot forging, has relatively simple production process and relatively strong deformation resistance, and is therefore commonly used for manufacturing automobile security parts such as crankshafts and the like. However, after the non-quenched and tempered round steel forged crankshaft in mass production is machined, defects are usually found at the forging parting plane on the inner side of the crankshaft connecting rod neck through fluorescent flaw detection, so that the finished crankshaft product is scrapped. But the strip structure and sulfide accumulation in the core of the bar of the non-quenched and tempered round steel are the main reasons for exceeding the standard of the fluorescent flaw detection of the crankshaft.
Disclosure of Invention
The invention aims to: the invention aims to provide non-quenched and tempered round steel with high purity and low probability of occurrence of defects; another object of the invention is to provide a method for manufacturing the round steel.
The technical scheme is as follows: the high-purity non-quenched and tempered round steel comprises the following chemical components in percentage by weight: 0.34 to 0.50 percent of C, 0.15 to 0.80 percent of Si, 0.10 to 0.30 percent of Cr, 0.50 to 1.65 percent of Mn, 0.005 to 0.075 percent of S, 0.005 to 0.040 percent of Al, 0.01 to 0.20 percent of V, 0.010 to 0.040 percent of Ti, 0.0100 to 0.0250 percent of N, and the balance of Fe and unavoidable impurities.
The invention relates to a preparation method of high-purity non-quenched and tempered round steel, which comprises the steps of EAF smelting, LF refining, VD vacuum, continuous casting, casting blank, heating for dephosphorization and rolling; the LF refining process is characterized by comprising the steps of feeding aluminum wires into molten steel, and feeding calcium iron wires after the aluminum content of the molten steel is not less than 0.015%; after vacuum breaking in the VD vacuum treatment, blowing in argon for 15-20 min, and feeding the calcium iron wire again; the continuous casting process uses an electromagnetic stirring soft reduction process.
Furthermore, the EAF smelting process adopts synthetic slag, silicon-manganese alloy and aluminum for pre-deoxidation during tapping.
Further, in the LF refining process, after aluminum wires are fed, the aluminum content is not lower than 0.015%, and the molten steel can be fully deoxidized and deoxidized, wherein the white slag time is not less than 30min, the nitrogen blowing time is 30min, and after refining and deoxidizing, ca iron wires are fed for carrying out denaturation treatment on inclusions, wherein the feeding amount of the Ca iron wires is 0.5-1.5 m/t.
Further, at the end of LF, the Al content is 0.010-0.020% and the S content is 0.010-0.085%.
Further, in the VD vacuum treatment, nitrogen is blown in at an early stage and argon is blown in at a later stage, and stirring is performed, and it is necessary to treat the wafer for 12 to 20 minutes at a vacuum of less than 0.5 torr to reduce the content of oxygen element. Argon is blown into the molten steel for 15-20 min after vacuum breaking, and in the process of soft blowing of the argon, the molten steel is in contact with oxygen in the atmosphere to form impurities, so that Ca iron wires are needed to be fed again to carry out denaturation treatment on the impurities. The feeding amount of the Ca iron wire added for the second time is 0.5-1.5 m/t.
Further, the superheat degree of the continuous casting process is 15-30 ℃, and the pulling speed is 0.48m/min. Under the conditions of relatively fixed superheat degree, drawing speed and cooling, the solidification speed of the continuous casting blank is from the outside to the inside, and the structure is relatively stable.
Further, the frequency of the electromagnetic stirring is (300-350) +/-5A multiplied by 2HZ, and the expansion of the columnar crystal area can be reduced by the electromagnetic stirring; the reduction of the solidification tail end is 8-20 mm, so that the solid substances at the front edge of the columnar crystal can be crushed and mixed with the molten steel at the core part, and microcomponent segregation and sulfide aggregation caused by partial crystallization at the core part can be reduced.
The beneficial effects are that: compared with the prior art, the invention has the remarkable advantages that: 1. improving the purity of steel: the round steel manufactured by the method has the average length-width ratio of the center part in sulfide segregation not more than 5, has no obvious banded distribution, and has purity higher than that of the conventional non-quenched and tempered steel; 2. the manufacturing cost is reduced: as the purity of the steel is improved, the prepared steel has high core quality, the fluorescent flaw detection failure rate of the crankshaft part is reduced, and the production cost is reduced.
Detailed Description
The technical scheme of the invention is further described below.
Example 1
The high-purity non-quenched and tempered round steel prepared by the embodiment comprises the following components in parts by weight: 0.46% of C, 0.23% of Si, 0.14% of Cr, 1.10% of Mn, 0.015% of S, 0.020% of Al, 0.08% of V, 0.015% of Ti, 0.0120% of N and the balance of Fe and unavoidable impurities.
The manufacturing of this embodiment includes the following steps: EAF smelting, LF refining, VD vacuum treatment, continuous casting electromagnetic stirring soft reduction process, casting blank slow cooling, casting blank inspection, continuous casting blank heating, descaling, rolling, straightening, grinding and flaw detection, and the specific parameters are as follows:
in the EAF smelting process, controlling the end point carbon of an electric furnace to be 0.1%, controlling the end point phosphorus to be 0.07%, controlling the tapping oxygen content to be 250ppm, and then carrying out a pre-deoxidation procedure on molten steel, wherein synthetic slag, silicon-manganese alloy and aluminum are arranged in a tapping ladle; in the LF refining process, aluminum wires and aluminum particles are fed to ensure that the Al content of molten steel is 0.031%, argon is blown and stirred in the whole process, the white slag time is 32min, and nitrogen is blown for 30 min; the Al content is 0.020% and the S content is 0.018% at the end stage of the LF refining process, and 0.9m/tCa iron wire is fed before the vacuum process to denature the inclusions; in the VD vacuum procedure, nitrogen is blown in earlier stage and then is switched to argon stirring, and the mixture is treated for 15min under the vacuum degree of 0.4 torr so as to finely adjust the contents of Al, N and Ti; blowing in argon for 17min after breaking vacuum, feeding 0.6m/t Ca iron wire to carry out denaturation treatment on the impurities again; in the continuous casting process, the superheat degree is 27 ℃, and the pulling speed is 0.48m/min; the molten steel is subjected to an electromagnetic stirring light pressing process, the electromagnetic stirring speed is 345A multiplied by 2Hz, and the pressing amount of the solidification tail end is 18mm. The test results of the round steel obtained are shown in tables 1 to 4.
Example 2
The high-purity non-quenched and tempered round steel prepared by the embodiment comprises the following components in parts by weight: 0.38% of C, 0.65% of Si, 0.15% of Cr, 1.43% of Mn, 0.025% of S, 0.020% of Al, 0.11% of V, 0.020% of Ti, 0.0180% of N, and the balance of Fe and unavoidable impurities.
The manufacturing of this embodiment includes the following steps: EAF smelting, LF refining, VD vacuum treatment, continuous casting electromagnetic stirring soft reduction process, casting blank slow cooling, casting blank inspection, continuous casting blank heating, descaling, rolling, straightening, grinding and flaw detection, and the specific parameters are as follows:
in the EAF smelting process, controlling the end point carbon of an electric furnace to be 0.09%, controlling the end point phosphorus to be 0.09%, controlling the tapping oxygen content to be 280ppm, and then carrying out a pre-deoxidation procedure on molten steel, wherein synthetic slag, silicon-manganese alloy and aluminum are arranged in a tapping ladle; in the LF refining process, aluminum wires and aluminum particles are fed to ensure that the Al content of molten steel is 0.028 percent, argon is blown and stirred in the whole process, the white slag time is 37 minutes, and nitrogen is blown for 30 minutes; the Al content is 0.020% and the S content is 0.031% at the end stage of the LF refining process, and 1.0m/tCa iron wire is fed before the vacuum process to denature the inclusions; in the VD vacuum procedure, nitrogen is blown in earlier stage and then is switched to argon stirring, and the mixture is treated for 13min under the vacuum degree of 0.4 torr so as to finely adjust the contents of Al, N and Ti; blowing in argon for 17min after breaking vacuum, feeding 0.7m/t Ca iron wire, and carrying out denaturation treatment on the impurities again; in the continuous casting process, the superheat degree is 20 ℃ and the pulling speed is 0.48m/min; after the molten steel is subjected to an electromagnetic stirring light pressing process, the electromagnetic stirring speed is 330A multiplied by 2Hz, and the pressing amount of the solidification tail end is 12mm. The test results of the round steel obtained are shown in tables 1 to 4.
Example 3
The high-purity non-quenched and tempered round steel prepared by the embodiment comprises the following components in parts by weight: 0.38% of C, 0.58% of Si, 0.20% of Cr, 1.48% of Mn, 0.045% of S, 0.010% of Al, 0.005% of V, 0.018% of Ti, 0.0160% of N, and the balance of Fe and unavoidable impurities.
The manufacturing of this embodiment includes the following steps: EAF smelting, LF refining, VD vacuum treatment, continuous casting electromagnetic stirring soft reduction process, casting blank slow cooling, casting blank inspection, continuous casting blank heating, descaling, rolling, straightening, grinding and flaw detection, and the specific parameters are as follows:
in the EAF smelting process, controlling the end point carbon of an electric furnace to be 0.08%, controlling the end point phosphorus to be 0.08%, controlling the tapping oxygen content to be 230ppm, and then carrying out a pre-deoxidation procedure on molten steel, wherein synthetic slag, silicon-manganese alloy and aluminum are arranged in a tapping ladle; in the LF refining process, aluminum wires and aluminum particles are fed to ensure that the Al content of molten steel is 0.017 percent, argon is blown and stirred in the whole process, the white slag time is 32min, and nitrogen is blown for 30 min; the Al content is 0.013% and the S content is 0.048% at the end stage of the LF refining process, and 1.4m/tCa iron wire is fed before the vacuum process to denature the inclusions; in the VD vacuum procedure, nitrogen is blown in earlier stage and then is switched to argon stirring, and the mixture is treated for 18min under the vacuum degree of 0.4 torr so as to finely adjust the contents of Al, N and Ti; blowing in argon for 18min after breaking vacuum, feeding 0.9m/t Ca iron wire, and carrying out denaturation treatment on the impurities again; in the continuous casting process, the superheat degree is 18 ℃ and the pulling speed is 0.48m/min; after the molten steel is subjected to an electromagnetic stirring light pressing process, the electromagnetic stirring speed is 340A multiplied by 2Hz, and the pressing amount of the solidification tail end is 16mm. The test results of the round steel obtained are shown in tables 1 to 4.
Table 1: low power detection result
| Examples | General porosity | Center porosity | Ingot segregation |
| 1 | 0.5 | 0.5 | 0.5 |
| 2 | 0.5 | 0.5 | 0 |
| 3 | 0.5 | 0.5 | 0.5 |
Table 2: round steel core area inclusion detection results
Table 3: core band tissue detection results
| Examples | Band tissue (level) | Pearlite bandwidth (micron) |
| 1 | 2 | 17 |
| 2 | 1 | - |
| 3 | 2 | 14 |
Table 4: mechanical property detection result
| Examples | Yield strength (Mpa) | Tensile strength (MPa) | Impact work (%) |
| 1 | 645 | 940 | 12 |
| 2 | 590 | 905 | 24 |
| 3 | 570 | 886 | 13 |
As shown in tables 1 to 4, the round steel core regions of examples 1 to 3 were fine and dispersed in sulfide distribution, and the band structure was slight, and after forging deformation, the bar core was qualified for fluorescent flaw detection, and the use requirements of crankshafts were satisfied.
Claims (7)
1. A preparation method of high-purity non-quenched and tempered round steel comprises the steps of EAF smelting, LF refining, VD vacuum, continuous casting, casting blank, heating for dephosphorization and rolling; the LF refining process is characterized by comprising the steps of feeding aluminum wires into molten steel, and feeding calcium iron wires after the aluminum content of the molten steel is not less than 0.015%; after vacuum breaking in the VD vacuum treatment, blowing in argon for 15-20 min, and then feeding a calcium iron wire again; the continuous casting process uses an electromagnetic stirring soft reduction process; the prepared round steel comprises the following chemical components in percentage by weight: 0.34 to 0.50 percent of C, 0.15 to 0.80 percent of Si, 0.10 to 0.30 percent of Cr, 0.50 to 1.65 percent of Mn, 0.005 to 0.075 percent of S, 0.005 to 0.040 percent of Al, 0.01 to 0.20 percent of V, 0.010 to 0.040 percent of Ti, 0.0100 to 0.0250 percent of N, and the balance of Fe and unavoidable impurities, wherein the average length-width ratio of the core of the round steel in sulfide segregation is not more than 5, and the round steel has no obvious strip-shaped distribution.
2. The method for producing a high purity non-quenched and tempered round steel according to claim 1, wherein the EAF smelting step uses synthetic slag, a silicomanganese alloy, and pre-deoxidizing with aluminum during tapping.
3. The method for preparing high purity non-quenched and tempered round steel according to claim 1, wherein in the LF refining process, the white slag time is not less than 30min, and the feeding amount of ca wire is 0.5-1.5 m/t.
4. The method for preparing high-purity non-quenched and tempered round steel according to claim 1, wherein the final stage of the LF refining process has an Al content of 0.010% to 0.020%.
5. The method for producing high purity non-quenched and tempered round steel according to claim 1, wherein the feeding amount of the re-fed calcium-iron wire after the vacuum treatment is 0.5 to 1.5m/t.
6. The method for producing high purity non-quenched and tempered round steel according to claim 1, wherein the degree of superheat in the continuous casting process is 15 to 30 ℃ and the drawing speed is 0.48m/min.
7. The method for producing a high purity non-quenched and tempered round steel according to claim 1, wherein the frequency of electromagnetic stirring is (300-350) ±5ax2hz and the solidification end reduction is 8 to 20mm.
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| CN114959420A (en) * | 2022-05-30 | 2022-08-30 | 江苏联峰能源装备有限公司 | Preparation method of non-quenched and tempered steel for cylinder of plastic molding machine for producing round billet |
| CN115341134A (en) * | 2022-09-02 | 2022-11-15 | 南京钢铁股份有限公司 | Production method of wire rod for high-sulfur aluminum-containing rack |
| CN115652205B (en) * | 2022-11-03 | 2023-12-29 | 宝武杰富意特殊钢有限公司 | Non-quenched and tempered crankshaft steel not easy to crack and surface quality control method |
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