CN115198172A - Steel for automobile tool sleeve and preparation method thereof - Google Patents

Steel for automobile tool sleeve and preparation method thereof Download PDF

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Publication number
CN115198172A
CN115198172A CN202210662028.6A CN202210662028A CN115198172A CN 115198172 A CN115198172 A CN 115198172A CN 202210662028 A CN202210662028 A CN 202210662028A CN 115198172 A CN115198172 A CN 115198172A
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equal
steel
less
tool sleeve
automobile
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Inventor
相楠
杨锋功
张立良
韩进雷
焦力隆
黄胜永
李宁
彭业亮
李绍杰
戴观文
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Shijiazhuang Iron and Steel Co Ltd
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Shijiazhuang Iron and Steel Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21C7/072—Treatment with gases
    • 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
    • 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
    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

A steel for an automobile tool sleeve and a preparation method thereof belong to the technical field of metallurgy. The steel for the sleeve comprises the following chemical components in percentage by weight: 0.27-0.33%, si is less than or equal to 0.10%, mn: 0.7-1.0%, P is less than or equal to 0.025%, S is less than or equal to 0.02%, cr: 0.3-0.5%, mo is less than or equal to 0.05%, ni is less than or equal to 0.20%, al: 0.01-0.035%, cu is less than or equal to 0.25%, B:0.001 to 0.003%, ti:0.02 to 0.05%, V:0.10 to 0.15%, nb: 0.005-0.1%, less than or equal to 10ppm of O, less than or equal to 80ppm of N, and the balance of iron and inevitable impurities. The preparation method comprises the working procedures of electric furnace smelting, LF refining, RH vacuum refining, continuous casting, heating and rolling. The decarburized layer on the surface of the steel for the sleeve is less than or equal to 0.8D%, and the hardness after quenching is more than or equal to 56HRC.

Description

Steel for automobile tool sleeve and preparation method thereof
Technical Field
The invention belongs to the technical field of metallurgy, and particularly relates to steel for an automobile tool sleeve and a preparation method thereof.
Background
The hand tool steel is applied to various aspects in life, including wrenches, pliers, screwdrivers, sleeves and the like, is used very frequently, and is required to have economy and durability, so that the hand tool steel is required to have high processing efficiency, and the surface of the hand tool steel has certain hardness which reaches 56HRC and ensures the wear resistance of the hand tool steel. According to the production process of the automobile tool sleeve: cutting-cold extrusion-turning-quenching-tempering and the like, and the working procedures of cutting-cold extrusion-turning-quenching-tempering and the like need to have good cold heading performance, ensure the formability, have good processing performance in the cutting processing process, and simultaneously have excellent hardenability and ensure the hardness after heat treatment. The hardenability of the steel for the automobile tool sleeve used in China at present can not meet the hardness requirement after heat treatment, the surface decarburization is serious, and the surface hardness can not be ensured.
Disclosure of Invention
In order to solve the technical problems, the invention provides steel for an automobile tool sleeve and a preparation method thereof, and the technical scheme adopted by the invention is as follows:
the steel for the automobile tool sleeve comprises the following chemical components in percentage by mass: c: 0.27-0.33%, si is less than or equal to 0.10%, mn: 0.70-1.00%, P is less than or equal to 0.025%, S is less than or equal to 0.020%, cr: 0.30-0.50%, mo is less than or equal to 0.05%, ni is less than or equal to 0.20%, al: 0.010-0.035%, cu is less than or equal to 0.25%, B:0.0010 to 0.0030%, ti:0.020 to 0.050%, V:0.10 to 0.15%, nb: 0.005-0.1%, less than or equal to 10ppm of O, less than or equal to 80ppm of N, and the balance of Fe and inevitable impurities;
wherein the contents of the four elements of C, V, mo and Ti have the following relationship:
A=Cwt%/(0.2Vwt%+0.063Mowt%+0.25Tiwt%)，5≤A≤15。
the diameter D of the steel for the sleeve is 5-25 mm, the thickness of a surface decarburized layer is less than or equal to 0.8D%, and the hardness after quenching is more than or equal to 56HRC.
The hot rolled structure of the steel for the sleeve is ferrite and pearlite.
The functional mechanism of each component of the invention is as follows:
c: carbon mainly forms interstitial solid solution in steel to enhance the strength of a matrix, and when the carbon content is low, the quenching hardness is low, so that the wear resistance is poor; when the carbon content is 0.27 to 0.33%, the tensile strength is high and the carbon content is set to 0.27 to 0.33% because of its ideal mechanical properties.
Mn: manganese and iron form a solid solution, so that the hardness and strength of ferrite and austenite in the steel are improved; and simultaneously is a carbide forming element which enters cementite to replace a part of iron atoms. Manganese plays a role in refining pearlite due to the fact that the critical transformation temperature is reduced in steel; indirectly plays a role in improving the strength of the pearlite steel; manganese is second only to nickel in its ability to stabilize the austenitic structure, and also strongly increases the hardenability of the steel. Manganese is an element that strongly increases hardenability and is inexpensive. The manganese content of the same type steel in the national standard is 1.3-1.40%, the steel has good toughness after solution treatment, and when the steel is deformed by impact, a surface layer is strengthened due to deformation, so that the steel has high wear resistance. Manganese and sulfur form MnS with a high melting point, and the hot brittleness phenomenon caused by FeS can be prevented. Manganese has a tendency to increase the coarsening of the steel grains and susceptibility to temper embrittlement. Considering that the track link has a complex shape and the manganese content is high to easily cause heat treatment cracks, the manganese content is properly reduced and finally set to 0.70-1.00%.
B: boron is another important element in steel. Boron can improve the hardenability of the material, and a proper amount of boron can improve the yield strength, tensile strength, fatigue strength and wear resistance of the material. Manganese and boron in the steel are added simultaneously, so that the wear resistance of the material can be improved; the high manganese steel is easy to crack and short in service life, the hardness of the material can be improved by about 50HRC under the action of low impact load by adding the boron element, and the service life can be prolonged by about 2 times. Therefore, the set content of B is 0.0010% to 0.0030%.
Cr: chromium increases the strength and hardness of the material, increases hardenability by slowing the rate of austenite decomposition, and forms chromium-containing carbides on carburized surfaces to improve wear resistance. The heat strength of the steel is also improved, chromium is a main alloy element of the stainless acid-resistant steel and the heat-resistant steel, and the set content of Cr is 0.30-0.50%.
Mo: molybdenum is a strong carbide forming element and has the function of reducing an austenite phase region, the hardenability of a material can be improved by adding the Mo element, the wear resistance of steel is improved, but bainite structures exist in the material due to the addition of the Mo element, the hot rolling state hardness is increased, the subsequent processing is not facilitated, and therefore, the content of Mo is controlled to be less than or equal to 0.05%.
Si: silicon can be dissolved in ferrite and austenite to improve the hardness and strength of steel, and has the effect of being second to phosphorus and stronger than elements such as manganese, nickel, chromium, tungsten, molybdenum, vanadium and the like. However, the high silicon content in the steel can significantly reduce the plasticity and toughness of the steel, increase the decarburization sensitivity, cause serious surface decarburization, and reduce the surface hardness after heat treatment, so that the set content of Si is less than or equal to 0.10%.
S: the segregation of sulfur in steel is serious, impurities are easy to form, and the improvement of the purity of molten steel is not facilitated; at high temperatures, it reduces the plasticity of the steel and is a harmful element. It exists in the form of FeS with a lower melting point; feS alone has a melting point of only 1190 c, while the eutectic temperature for eutectic formation with iron in steel is lower, only 988 c. As the steel solidifies, iron sulfide collects at the primary grain boundaries; when the steel is rolled at 1100-1200 ℃, feS on grain boundaries is melted, and the bonding force among grains is greatly weakened, so that the hot brittleness phenomenon of the steel is caused. The set content of S is less than or equal to 0.020%.
P: phosphorus is one of the harmful impurities in steel. Steel containing more phosphorus, which is severely segregated and easily brittle when used at room temperature or lower, is called cold brittle; the plasticity and the toughness of the steel are obviously reduced. Phosphorus is a harmful element and should be strictly controlled, and the set content of P is less than or equal to 0.025 percent.
Ti: titanium is a strong carbide and nitride forming element, and the nitride can grow austenite grains and improve the grain coarsening temperature. Ti has the main function of fixing nitrogen in boron steel, plays the role of effective boron and improves the hardenability of the material. The set content of Ti is 0.02-0.05%.
Al: aluminum is used as a strong deoxidizing element, on one hand, the aluminum is used as a deoxidizing agent in the smelting process to ensure the oxygen content in steel, and on the other hand, the aluminum is added to form AlN to play a role in refining grains. The set content of Al is 0.010-0.035%.
3238 Zxft 3238 micro-alloy element carbonitride such as V (C, N) Nb (C, N) is preferentially precipitated at grain boundaries, deformation zones, dislocation defects and the like, the grain boundaries are pinned, the grain size is refined, the recrystallization temperature of austenite can be improved, the recrystallization is strongly prevented, meanwhile, carbonitride of V, nb can be fully dissolved, and the precipitation strengthening effect is large, so that 0.10-0.15% of V and 0.005-0.1% of Nb are added, and the decarburization sensitivity is reduced.
Through the B-Ti-V-Nb microalloying design, the dissolution and precipitation of carbides are controlled under different conditions to form fine and dispersedly distributed carbonitrides, and the effects of grain refinement and precipitation strengthening are achieved. In addition, the decarburization sensitivity of the steel can be reduced by the Nb and V composite microalloying addition.
The preparation method of the steel for the automobile tool sleeve comprises the working procedures of electric furnace smelting, LF refining, RH vacuum refining, continuous casting, heating and rolling.
In the electric furnace smelting process, the content of C in molten steel is more than or equal to 0.05wt% and the content of P in the molten steel is less than or equal to 0.015wt% during tapping.
In the LF refining process, argon is blown in the whole refining process, the argon pressure is 0.3-1.8 MPa, and the flow is 20-80 NL/min.
In the RH vacuum refining process, the vacuum degree is less than or equal to 133Pa, the vacuum is maintained for 20-25 min, the Ti wire is added after the air is broken, then soft blowing is carried out for 3-5 min, then the CaSi wire and the FeB are added, and the total soft blowing time is more than or equal to 15min.
In the continuous casting process, the casting temperature is 1526-1536 ℃, and the casting speed is 1.2-1.4 m/min.
The heating procedure is carried out at the soaking temperature of 1070-1130 ℃ and the heating time in the furnace of less than or equal to 2.5h.
The rolling procedure has the initial rolling temperature of 900-1000 ℃ and the final rolling temperature of 900-950 ℃.
Adopt the produced beneficial effect of above-mentioned technical scheme to lie in: through the chemical composition design, the content of alloy elements V, mo and Ti of strong carbides and C in steel meets the requirement of A = Cwt%/(0.2 Vwt% +0.063Mo wt% +0.25 Tiwt%), A is between 5 and 15, and the carbides in the steel are ensured to be finely dispersed and distributed in the steel; adding alloy elements Cr, ti and B to improve hardenability, adding Ti to refine crystal grains on one hand and fix nitrogen on the other hand so as to play a role of effective B, adding a small amount of V element, dissolving and separating out under different conditions to form fine and dispersedly distributed carbonitride, playing a role in refining crystal grains and strengthening precipitation, controlling the content of Si element, reducing decarburization sensitivity and ensuring the surface hardness after quenching. Meanwhile, the low-power quality of the continuous casting billet is ensured by controlling the continuous casting process parameters, the low-power center porosity of the continuous casting billet is less than or equal to 0.5 level, the center segregation is 0 level, and the ingot type segregation is 0 level; controlling the heating and rolling process, controlling the thickness of the surface decarburized layer to be less than or equal to 0.8D%, ensuring that the surface hardness of the surface decarburized layer after the heat treatment process is not less than 56HRC, and simultaneously ensuring that the grain size is not less than 7 grades.
The method can effectively ensure the performance of the steel for the automobile tool sleeve and improve the performance and quality of the automobile tool sleeve through process control.
Detailed Description
The present invention will be described in further detail with reference to specific examples.
Examples 1 to 9
(1) Chemical components: the chemical composition and the mass percentage of the steel for the automobile tool sleeve of each example are shown in table 1.
Table 1: chemical composition of Steel for automotive tool Sleeve
Figure DEST_PATH_IMAGE001
(2) The preparation method of the steel for the automobile tool sleeve adopts the processes of electric furnace smelting, LF refining, RH vacuum refining, continuous casting, heating and rolling to produce the steel. The process of each procedure is as follows:
A. an electric furnace smelting process: the carbon content in the steel is more than or equal to 0.05wt percent, and the P content is less than or equal to 0.015wt percent.
B. An LF refining procedure: argon is blown in the whole refining process, the pressure of the argon is 0.3-1.8 MPa, and the flow is 20-80 NL/min.
C. RH vacuum refining process: the vacuum degree is less than or equal to 133Pa, and the vacuum is maintained for 20-25 min; the wire feeding and alloying after the RH breaking can improve the alloy yield: firstly adding Ti wire, then soft blowing for 3-5 minutes, and then adding CaSi wire and FeB to ensure that the chemical components meet the design requirements, and the total soft blowing time is more than or equal to 15min.
D. And (3) a continuous casting process: the pouring temperature is controlled to be 1526-1536 ℃, the pouring speed is controlled to be 1.2-1.4 m/min, and the macroscopic quality of the continuous casting billet can be well controlled.
E. A heating procedure: the soaking temperature is 1070-1130 ℃, the heating time in the furnace is less than or equal to 2.5 hours, so that the internal and external temperatures of the continuous casting billet are uniform, and the rolling temperature requirement is met.
F. A rolling procedure: the initial rolling temperature is 900-1000 ℃, and the final rolling temperature is 900-950 ℃.
Specific process parameters of the electric furnace smelting, LF refining and RH vacuum refining procedures are shown in Table 2; the specific process parameters for the continuous casting, heating and rolling sequences of each example are shown in table 3.
Table 2: specific process parameters of the refining process of each embodiment
Figure 982845DEST_PATH_IMAGE002
Table 3: specific process parameters of the preparation process of each example
Figure DEST_PATH_IMAGE003
(3) The results of testing the hot rolled decarburized layer of the steel for sleeves obtained in each example are shown in Table 4.
Table 4: macroscopic and decarburized layer test results
Figure 759040DEST_PATH_IMAGE004
(4) After the steel for hot-rolled automobile tool sleeves obtained in each example was made into a standard, quenching heat treatment (870 ± 10 ℃ C. For 1 to 2 hours) was performed, and the hardness and grain size were examined.
Table 5: quenching conditions, hardness and grain size after quenching in examples
Figure DEST_PATH_IMAGE005
After the steel for the automobile tool sleeve obtained by the method is quenched, the austenite grain size of the steel for the automobile tool sleeve is not less than 7 grades, and the hardness of the steel is not less than 56HRC.

Claims (7)

1. The steel for the automobile tool sleeve is characterized by comprising the following chemical components in percentage by mass: c: 0.27-0.33%, si is less than or equal to 0.10%, mn: 0.70-1.00%, P is less than or equal to 0.025%, S is less than or equal to 0.020%, cr: 0.30-0.50%, mo is less than or equal to 0.05%, ni is less than or equal to 0.20%, al: 0.010-0.035%, cu is less than or equal to 0.25%, B:0.0010 to 0.0030%, ti:0.020 to 0.050%, V:0.10 to 0.15%, nb: 0.005-0.1%, less than or equal to 10ppm of O, less than or equal to 80ppm of N, and the balance of Fe and inevitable impurities; wherein the contents of the four elements of C, V, mo and Ti have the following relationship:
A=Cwt%/(0.2Vwt%+0.063Mowt%+0.25Tiwt%)，5≤A≤15。
2. the steel for an automobile tool sleeve as claimed in claim 1, wherein the diameter D of the steel for a sleeve is 5 to 25mm, the thickness of the surface decarburized layer is not more than 0.8D%, and the hardness after quenching is not less than 56HRC.
3. The steel for an automobile tool sleeve as set forth in claim 1 or 2, characterized in that the hot rolled structure of the steel for a sleeve is ferrite and pearlite.
4. The method for producing the steel for the tool sleeve of the automobile according to any one of claims 1 to 3, wherein the production method comprises the steps of electric furnace smelting, LF refining, RH vacuum refining, continuous casting, heating, and rolling; in the continuous casting process, the casting temperature is 1526-1536 ℃, and the casting speed is 1.2-1.4 m/min;
in the heating procedure, the soaking temperature is 1070-1130 ℃, and the heating time in the furnace is less than or equal to 2.5h;
the rolling procedure has the initial rolling temperature of 900-1000 ℃ and the final rolling temperature of 900-950 ℃.
5. The method for preparing steel for an automobile tool sleeve according to claim 4, wherein in the electric furnace smelting process, the content of C in molten steel is more than or equal to 0.05wt% and the content of P in molten steel is less than or equal to 0.015wt% during tapping.
6. The method for preparing steel for an automobile tool sleeve according to claim 5, wherein in the LF refining process, argon is blown in the whole refining process, the argon pressure is 0.3-1.8 MPa, and the flow rate is 20-80 NL/min.
7. The method for preparing the steel for the automobile tool sleeve according to any one of claims 4 to 6, wherein in the RH vacuum refining process, the vacuum degree is less than or equal to 133Pa, the vacuum is maintained for 20 to 25 minutes, after the vacuum is broken, a Ti wire is firstly added, then soft blowing is carried out for 3 to 5 minutes, then a CaSi wire and FeB are added, and the total soft blowing time is more than or equal to 15 minutes.
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CN105088089A (en) * 2015-08-24 2015-11-25 武汉钢铁(集团)公司 Cold-rolled shifting fork steel member for automobile and producing method
CN109843456A (en) * 2016-10-21 2019-06-04 现代制铁株式会社 High intensity enhancing steel and its manufacturing method
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