CN113564469B - High-carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending property and production method thereof - Google Patents
High-carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending property and production method thereof Download PDFInfo
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- 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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- 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
- B22D11/16—Controlling or regulating processes or operations
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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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
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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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
- 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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Abstract
The invention relates to a high-carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending property and a production method thereof, wherein the steel plate comprises the following chemical components: 0.60 to 1.0 percent of C, less than or equal to 0.1 percent of Si, 0.4 to 1.5 percent of Mn, 0.0005 to 0.05 percent of Ca, 0.01 to 0.5 percent of Re0.06 percent of Al, less than or equal to 0.05 percent of Mg, more than or equal to 0.3 percent of Ca/S, more than or equal to 1 percent of Ca/Mg, more than or equal to 0.02 percent of Ca/Re, 0.1 to 1.0 percent of Sn, less than or equal to 0.020 percent of P, less than or equal to 0.015 percent of S, and the balance of Fe and inevitable impurities. The cutting tool steel produced by the invention has low Si content, smooth surface, no crystal boundary oxidation layer and decarburized layer, tensile strength of 700 MPa-800 MPa, yield ratio of less than 50%, no cracking after 180-degree bending, excellent bending performance, surface hardness of no need of heat treatment of more than 48HRC and excellent wear resistance.
Description
Technical Field
The invention relates to the technical field of cutting tool steel production, in particular to high-carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending performance and a production method thereof.
Background
The conventional cutting tool steel is not suitable for bending parts with complicated shapes because the carbon content is high, the hot rolled structure mainly comprises pearlite, the brittleness is high, and the cutting tool steel cracks after being bent at a small angle. With the development of times, the cutting tool steel has wider and higher application and higher performance requirements, and not only the use hardness of the cutting tool steel is required to be more than 42HRC after heat treatment, but also the processed shape is more and more complex. In order to meet the bending processing requirements of some complex parts, cold-rolled annealed cutting tool steel is generally adopted as a raw material, the bending use requirements can be met through multi-pass annealing and cold rolling, and the production cost is high. The composition and structure of the hot rolled plate are main factors influencing the bending performance and the service hardness of the hot rolled plate, the surface oxidation and decarburization are also one of the main factors influencing the hardness and the bending performance of the hot rolled plate, and the production efficiency is low because the decarburization layer is deep and the grinding amount is large. At present, the surface decarburized layer depth of the high carbon blade steel is generally controlled to about 2.0% of the plate thickness, and the optimum level of the full thickness specification does not exceed 1.0% of the plate thickness, and the control becomes difficult as the plate thickness becomes larger.
On the other hand, the oil fume generated by heat treatment quenching seriously pollutes the environment and the heating energy consumption is large.
In order to adapt to the development of times, meet the requirements of cutting tool steel on processing parts with complex shapes, reduce the surface grinding amount, improve the production efficiency and reduce the cost, the cutting tool steel with high surface hardness, which has excellent bending performance, low cost, low depth of decarburized layer or no surface oxidation and decarburization, needs to be developed urgently to replace heat treatment steel.
The Chinese invention patent with the publication number of CN104745786B discloses a method for producing thin tool steel by a CSP line without spheroidizing annealing, which relates to a method for producing a thin tool steel plate with the thickness of 1-2.5mm, and can not meet the use requirement of a thick tool steel plate; the production process comprises the steps of rolling at low temperature, coiling at low temperature near the martensite transformation temperature through rapid cooling, and tempering to obtain the tempered sorbite with reduced hardness, wherein the production process has extremely high requirements on the capability of a coiler on one hand, and martensite transformation occurs in the coiling process, so that the martensite is extremely brittle and easy to break, and the high-temperature tempering treatment at 550-700 ℃ is performed after coiling, so that the cost is high. In the technical proposal, the decarburizing depth is controlled not to exceed 1 percent of the plate thickness.
The Chinese patent with publication number CN103173598B discloses a process for manufacturing an annealing-free medium and high carbon steel plate, and the Chinese patent application with publication number CN102417959A discloses a process for producing an annealing-free hot rolled S45C plate strip, which adopts a two-phase region or a ferrite region to roll at low temperature and high pressure, coils at high temperature and stacks to obtain 60% of ferrite and partial spheroidized pearlite, and softens to reduce the hardness of the steel plate to 80-85 HRB. The steel plate obtained by the process has large ferrite amount and large blocks, can be used only by quenching and tempering, has low hardness after heat treatment, and can not meet the use requirements of high-end cutting tool steel.
The Chinese patent with the publication number of CN100482406C discloses a method for manufacturing a cutting tool steel plate with three layers of composite cutting edges, and the Chinese patent with the publication number of CN100462192C discloses a method for manufacturing a cutting tool steel plate with double composite cutting edges.
Chinese patent publication No. CN103757546B discloses a "high alloy cutting tool steel for wood working machinery rotary cutter blades and its hot working process", in which the cutting tool steel has high content of Cr, V, W, Mo and other alloys, and is subjected to two times of quenching treatment, the process is complex, and the cost is high.
Chinese patent application publication No. CN110499479A discloses "a steel for high-strength bolting belt with excellent plating performance and a manufacturing method thereof", chinese patent application publication No. CN110499447A discloses "a steel for plating bolting belt buckle and a manufacturing method thereof", and chinese patent application publication No. CN111206179A discloses "a steel for high fatigue life plating plate hook and a manufacturing method thereof", wherein the surface quality of the steel plate is mainly controlled by rolling and cooling, and the surface decarburization depth is not more than 1.5% of the plate thickness, thereby improving the plating performance. The hardness of the hot rolled plate is below 100HRB, and the hardness of the hot rolled plate can reach the hardness above 37HRC required by use only by a plurality of heat treatment processes such as quenching, tempering and the like, so that the cost is high and the efficiency is low.
Chinese patent application publication No. CN105177430A discloses "an alloy tool steel and a production method thereof", relating to a medium carbon tool steel, which contains: 0.5 percent of C, 0.2 percent of Si, 0.5 percent of Mn, 5.0 percent of Cr, 2.3 percent of Mo, 0.5 percent of V, less than or equal to 0.003 percent of S and less than or equal to 0.02 percent of P, more alloys such as Cr, Mo, V and the like are added into the alloy tool steel, electroslag remelting and casting ingot casting are needed for smelting, the yield is low, a plurality of heat treatment procedures such as softening annealing, spheroidizing annealing, quenching, tempering and the like are needed, the cost is high, and the alloy tool steel is not suitable for processing and manufacturing various tools with complex shapes.
Chinese patent with publication No. CN103506380B discloses a production method for reducing the thickness of a decarburized layer of high-carbon spring strip steel, which adopts a method of controlling the heating temperature, the atmosphere in a furnace, the rolling reduction rate of a single pass and the cooling speed to control the depth of the decarburized layer of the spring steel of 2.5-3.55mm not to exceed 0.02 mm. The method is not suitable for thicker steel plates, and the requirements on the atmosphere and temperature sectional control precision in the heating furnace are high, so that the operation is difficult.
The steel grade and the production method in the technical scheme do not refer to bending performance, have certain defects, and cannot meet the use requirement of bending and high-surface-hardness cutting tool steel.
Disclosure of Invention
The invention provides high-carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending property and a production method thereof, which overcome the problems that the surface of the existing cutting tool steel is seriously decarbonized and oxidized and is not suitable for bending, the produced cutting tool steel has low Si content, smooth surface, no crystal boundary oxide layer and decarburized layer, the tensile strength of 700 MPa-800 MPa, the yield ratio of less than 50 percent, no cracking during 180-degree bending, excellent bending property, no need of heat treatment, the surface hardness of more than 48HRC, excellent wear resistance, high production efficiency and low cost.
In order to achieve the purpose, the invention adopts the following technical scheme:
the high-carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending performance comprises the following chemical components in percentage by weight: 0.60 to 1.0 percent of C, less than or equal to 0.1 percent of Si, 0.4 to 1.5 percent of Mn, 0.0005 to 0.05 percent of Ca, 0.01 to 0.5 percent of Re, less than or equal to 0.06 percent of Al, less than or equal to 0.05 percent of Mg, more than or equal to 0.3 percent of Ca/S, more than or equal to 1 percent of Ca/Mg, more than or equal to 0.02 percent of Ca/Re, 0.1 to 1.0 percent of Sn, less than or equal to 0.020 percent of P, less than or equal to 0.015 percent of S, and the balance of Fe and inevitable impurities.
The structure of the steel plate is a sorbite structure with 100 percent of spheroidization rate, the tensile strength is 700 MPa-800 MPa, the yield ratio is less than or equal to 50 percent, and the steel plate does not crack when bent at 180 degrees.
The surface of the steel plate is distributed with a ReSnC hardening particle layer with the diameter not more than 20nm in a dispersing way, the depth of the hardening particle layer is not less than 10% of the thickness of the steel plate, the depths of a grain boundary oxidation layer and a decarburized layer are both 0mm, the surface hardness after annealing is more than 48HRC, and the wear rate is not more than 30 mg/km.
A production method of high-carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending property comprises the following steps of smelting, continuous casting, casting blank treatment, rolling and cooling, wherein the production method comprises the following steps:
1) smelting process;
deoxidizing by using an Al deoxidizer, adding Ca for treatment after the oxygen content in the steel is less than or equal to 0.0020% during refining, adding other alloys along the wall of the tundish after the Ca treatment is carried out for at least 5 minutes, adding Re-Mg alloy firstly, and adding Sn alloy finally;
2) a continuous casting process;
blowing argon for 5-8 minutes in the tundish, and controlling the degree of superheat of pouring to be less than or equal to 25 ℃; the continuous casting adopts a pressing process and crystallizer electromagnetic stirring, a stirring coil is made of pure carbon materials, electromagnetic stirring is carried out for 1-3 minutes, and the current intensity is over 1000A; the rolling reduction is 10 mm-30 mm; the continuous casting speed is 1.0-1.4 m/min;
3) a casting blank treatment process;
the casting blank is subjected to off-line slow cooling for more than 72 hours, the casting blank is sent to a stepping heating furnace for heating before rolling, the inside of the stepping heating furnace adopts reducing atmosphere, the temperature of the casting blank in a preheating section is more than 500 ℃, the heating temperature of a heating section is 1200-1350 ℃, and the total time of the furnace is 2-4 hours;
4) a rolling process;
the rolling process comprises three procedures of rough rolling, finish rolling and third rolling:
a) the first pass reduction rate of rough rolling is more than or equal to 50 percent;
b) the finish rolling adopts a continuous rolling mode of not less than 6 passes, the total rolling reduction rate is not less than 80 percent, the first pass rolling reduction rate is not less than 30 percent, the rolling speed is not less than 25m/s, the initial rolling temperature is 1100-1150 ℃, and the finishing temperature is 900-950 ℃;
c) after finish rolling, the steel plate enters laminar cooling and is quenched at the cooling speed of more than or equal to 25 ℃/s, and is cooled to 500-680 ℃ and then enters a double-vertical-roller four-horizontal-roller mill for continuous two-pass rolling, wherein the upper and lower reduction rate is 10-20%, and the side pressure reduction rate is 5-20%;
5) a cooling process;
after the third rolling, the steel plate directly enters an induction annealing unit for annealing, the cooling speed is 20-50 ℃/h, and the steel plate is cooled to below 200 ℃ for air cooling.
The smelting process comprises the processes of converter smelting and electric furnace refining, and the thickness of the continuous casting billet is 170-250 mm.
In the casting blank treatment process, the temperature of a preheating section is above 500 ℃ before a casting blank is fed into a heating section of a stepping heating furnace.
And descaling by adopting high-pressure water before rough rolling, finish rolling and third rolling, wherein the high-pressure water pressure is not less than 30 MPa.
Compared with the prior art, the invention has the beneficial effects that:
1) re and Sn are added, an electromagnetic stirring, continuous casting reduction and three-time controlled rolling technology is utilized, a ReSnC hardened particle layer with the dispersion distribution diameter not more than 20nm is formed below the surface of the steel plate, the depth of the hardened particle layer is not less than 10% of the thickness of the steel plate, the depths of a surface grain boundary oxidation layer and a decarburized layer are both 0mm, the surface hardness after annealing is more than 48HRC, the wear rate is not more than 30mg/km, the wear resistance is excellent, the steel is replaced by heat treatment, the cost is low, the energy is saved, and the consumption is reduced;
2) re and Mg are utilized to control the interval between the carburized pieces of the hot rolled plate, and the steel plate is not required to be acid-washed and cold-rolled for three times, and is only subjected to one-time online continuous annealing to obtain a spheroidized sorbite structure with 100 percent of spheroidization rate, wherein the tensile strength is 700 MPa-800 MPa, the yield ratio is below 50 percent, the spheroidized sorbite structure is not cracked when bent at 180 degrees, and the bending property and the punch forming property are excellent;
3) the toughness and plasticity and the formability of the steel plate are good, the surface has high hardness and good wear resistance, and the toughness of the steel plate are well matched;
4) the surface is smooth and clean, no crystal boundary oxidation layer or decarburized layer exists, and the electroplating qualified rate is 100 percent after the sand throwing process is omitted;
5) the inclusions in the steel are denatured by adding Ca, Re and Mg, so that various nonmetallic inclusions in the steel do not exceed 1.0 level;
6) ca and Sn are used for improving the fluidity of the molten steel, the yield of Re reaches more than 60 percent, and the yield of Mg reaches more than 40 percent;
7) the steel plate is not heated before annealing, parts are not subjected to heat treatment, sand throwing is not needed before electroplating, energy is saved, consumption is reduced, and cost is low.
Drawings
FIG. 1 is a structural morphology (1000 times) of spheroidized sorbite of a steel plate according to example 3 of the present invention.
FIG. 2 is a (1000 times) topographical view of the hardened particle layer under the surface of the steel sheet of example 3 of the present invention.
FIG. 3 is a (500-fold) topographical view of comparative example 1.
Detailed Description
The following further illustrates embodiments of the invention:
the invention relates to high-carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending performance, which comprises the following chemical components in percentage by weight: 0.60 to 1.0 percent of C, less than or equal to 0.1 percent of Si, 0.4 to 1.5 percent of Mn, 0.0005 to 0.05 percent of Ca, 0.01 to 0.5 percent of Re, less than or equal to 0.06 percent of Al, less than or equal to 0.05 percent of Mg, more than or equal to 0.3 percent of Ca/S, more than or equal to 1 percent of Ca/Mg, more than or equal to 0.02 percent of Ca/Re, 0.1 to 1.0 percent of Sn, less than or equal to 0.020 percent of P, less than or equal to 0.015 percent of S, and the balance of Fe and inevitable impurities.
The structure of the steel plate is a sorbite structure with 100 percent of spheroidization rate, the tensile strength is 700 MPa-800 MPa, the yield ratio is less than or equal to 50 percent, and the steel plate does not crack when bent at 180 degrees.
The surface of the steel plate is distributed with a ReSnC hardening particle layer with the diameter not more than 20nm in a dispersing way, the depth of the hardening particle layer is not less than 10% of the thickness of the steel plate, the depths of a grain boundary oxidation layer and a decarburized layer are both 0mm, the surface hardness after annealing is more than 48HRC, and the wear rate is not more than 30 mg/km.
A production method of high-carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending property comprises the following steps of smelting, continuous casting, casting blank treatment, rolling and cooling, wherein the production method comprises the following steps:
1) smelting process;
deoxidizing by using an Al deoxidizer, adding Ca for treatment after the oxygen content in the steel is less than or equal to 0.0020% during refining, adding other alloys along the wall of the tundish after the Ca treatment is carried out for at least 5 minutes, adding Re-Mg alloy firstly, and adding Sn alloy finally;
2) a continuous casting process;
blowing argon for 5-8 minutes in the tundish, and controlling the degree of superheat of pouring to be less than or equal to 25 ℃; the continuous casting adopts a pressing process and crystallizer electromagnetic stirring, a stirring coil is made of pure carbon materials, electromagnetic stirring is carried out for 1-3 minutes, and the current intensity is over 1000A; the rolling reduction is 10 mm-30 mm; the continuous casting speed is 1.0-1.4 m/min;
3) a casting blank treatment process;
the casting blank is subjected to off-line slow cooling for more than 72 hours, the casting blank is sent to a stepping heating furnace for heating before rolling, the inside of the stepping heating furnace adopts reducing atmosphere, the temperature of the casting blank in a preheating section is more than 500 ℃, the heating temperature of a heating section is 1200-1350 ℃, and the total time of the furnace is 2-4 hours;
4) a rolling process;
the rolling process comprises three procedures of rough rolling, finish rolling and third rolling:
a) the first pass reduction rate of rough rolling is more than or equal to 50 percent;
b) the finish rolling adopts a continuous rolling mode of not less than 6 passes, the total rolling reduction rate is not less than 80 percent, the first pass rolling reduction rate is not less than 30 percent, the rolling speed is not less than 25m/s, the initial rolling temperature is 1100-1150 ℃, and the finishing temperature is 900-950 ℃;
c) after finish rolling, the steel plate enters laminar cooling and is quenched at the cooling speed of more than or equal to 25 ℃/s, and is cooled to 500-680 ℃ and then enters a double-vertical-roller four-horizontal-roller mill for continuous two-pass rolling, wherein the upper and lower reduction rate is 10-20%, and the side pressure reduction rate is 5-20%;
5) a cooling process;
after the third rolling, the steel plate directly enters an induction annealing unit for annealing, the cooling speed is 20-50 ℃/h, and the steel plate is cooled to below 200 ℃ for air cooling.
The smelting process comprises the processes of converter smelting and electric furnace refining, and the thickness of the continuous casting billet is 170-250 mm.
In the casting blank treatment process, the temperature of a preheating section is above 500 ℃ before a casting blank is fed into a heating section of a stepping heating furnace.
And descaling by adopting high-pressure water before rough rolling, finish rolling and third rolling, wherein the high-pressure water pressure is not less than 30 MPa.
The action mechanism of each alloy component in the cutting tool steel is as follows, wherein the percentage symbol% represents the weight percentage;
c is a main solid solution strengthening element in steel, sufficient C is needed in the steel to improve the strength and the hardness, if the content of C is lower than 0.60%, the strength and the hardness of a steel plate are difficult to guarantee, and if the content of C is higher than 1.0%, the strength of a hot rolled plate is too high, the toughness and the plasticity of the steel are deteriorated, the yield ratio is influenced, and the formability is poor. Therefore, the content of C is controlled to be 0.60-1.0 percent.
Mn is relatively cheap, is a good deoxidizer and desulfurizer, and is an essential element for ensuring the strength and toughness of steel. The manganese and the iron can be infinitely dissolved to form a solid solution, so that the hardness and the strength of the steel are improved, and the influence on the plasticity is relatively small. Mn and S are combined to form MnS, so that the influence of hot cracks caused by FeS formed at the grain boundary on the hot formability of the cutter steel is avoided. Meanwhile, Mn is also a good deoxidizer and can increase hardenability. The steel has low Mn content, can not meet the requirement of high strength and hardness, and the Mn content is too high, segregation is serious, the welding performance and formability are influenced, and the production cost is increased, so the Mn content is controlled to be 0.4-1.5 percent by comprehensively considering the factors of cost, performance requirement and the like.
Si is one of common elements in steel and is used as a reducing agent and a deoxidizing agent in the steelmaking process, and the yield strength and the ductile-brittle transition temperature of the steel can be improved by the solid-solution Si; the content of Si in the common cutting tool steel is 0.17-0.37 percent, but Si is as little as possible in the invention, and Si deoxidation is not used in smelting. According to the invention, the surface of the cutting tool steel can be subjected to decarburization oxidation by Si, a loose oxidation layer is formed, and microcrack defects such as grain boundary oxidation exist in the oxidation layer, so that the surface hardness and the fatigue performance are seriously influenced. According to the invention, Si is controlled to be less than or equal to 0.1%, the cost is low, and the oxidation and decarburization of the steel surface can be avoided, so that the surface quality is improved, and the polishing amount is reduced.
Al is used as a deoxidizing and nitrogen-fixing agent in steelmaking, so that crystal grains are refined, the aging of steel is inhibited, the toughness of the steel at low temperature is improved, and the brittle transition temperature of the steel can be particularly reduced; al can also improve the oxidation resistance of the steel and improve the corrosion resistance to hydrogen sulfide. The Al content exceeds 0.06 percent, and the Al easily forms large-particle oxide inclusion with oxygen in steel, thereby influencing the fatigue performance.
Ca is used as a microalloying element, so that the corrosion resistance, the wear resistance, the high temperature resistance and the low temperature resistance of the steel are improved, and the impact toughness, the fatigue strength, the plasticity and the welding performance of the steel are improved; the cold heading property, the shock resistance, the hardness and the contact endurance strength of the steel are improved. The cutting tool steel has high carbon content, the molten steel has poor fluidity, and the inclusion is not easy to float upwards. The invention adds calcium into the steel, can change the components, the quantity and the form of the non-metallic inclusions, quickens the flow of the molten steel, promotes the inclusions to float sufficiently, improves the purity of the steel, ensures that various non-metallic inclusions in the finished steel do not exceed 1.0 grade, improves the surface smoothness of the steel, eliminates the anisotropy of the structure, improves the hydrogen induced crack resistance and the lamellar tearing resistance, and prolongs the service life of the tool. The Ca content is controlled to be 0.0005-0.05 percent, and the Ca/S is more than or equal to 0.3, so as to ensure that the Ca inclusion denaturation treatment is sufficient. The Ca inclusion denaturation has a great relation with the sulfur content, and the Ca/S ratio is controlled to be more than or equal to 0.3 so as to ensure that the Ca inclusion denaturation is sufficient. In addition, the yield of Re can be improved by more than 60% by adding calcium, the yield of Mg can be improved by more than 40%, and the utilization rate of rare earth and magnesium can be effectively improved.
Magnesium is a very active metal element, which has strong affinity with oxygen, nitrogen, and sulfur. Therefore, magnesium is a good deoxidizer and desulfurizer in steel smelting. However, because magnesium is too active, it is not easy to control during smelting, and it is very easy to form inclusions with oxygen, nitrogen, etc. to affect the purity of steel. The invention adopts a unique refining and Re-Mg smelting technology to strictly and accurately control steelThe content of Mg in the alloy is determined by the coaction of Ca and Mg to generate CaO, MgO and Al2O3And CaO, MgO and MnS composite inclusions, which have low melting point and are easy to solidify, float and remove in molten steel, avoid the problem of nozzle nodulation in the continuous casting process, reduce the inclusion content in the molten steel and control the inclusion level in steel not to exceed 1.0 level. The invention limits Ca/Mg to be more than or equal to 1 so as to ensure that enough Ca and Mg form CaO, MgO and Al2O3And CaO, MgO and MnS composite inclusion, and the yield of Mg is more than 40 percent. The other main function of Mg is to generate Re-MgC by the combined action of the Mg and Re2、Re-Mg2C3And the interval between the carbide sheet layers in the hot rolled plate structure is controlled to be 0.15-0.3 mu m, the annealing spheroidization rate is high, and 180-degree bending without cracking is realized.
The rare earth elements can improve the oxidation resistance and corrosion resistance of the steel and improve the high-temperature strength. The invention utilizes Re, Mg and C to generate Re-MgC2、Re-Mg2C3The interval between the carbide sheet layers in the hot rolled plate structure is controlled to be 0.15-0.3 mu m, the annealing spheroidization rate is high, and 180-degree bending without cracking is realized. In addition, RE can improve the fluidity of steel and improve the surface smoothness of the steel plate. Re also enables Al2O3Oxides such as MnS and sulfide inclusions become fine and dispersed spherical inclusions, so that the harmfulness of the inclusions is eliminated, and the fatigue performance is improved. The Ca/Re is more than or equal to 0.02, which can ensure that enough Ca can improve the yield of the rare earth and play a role in coarsening and controlling the interlayer spacing of the sorbite and annealing to easily obtain a spheroidized structure. The casting blank has the advantages that the high-content Re on the surface of the casting blank also cooperates with Sn to generate a ReSnC granular phase which is pinned in grains and at a grain boundary, so that the surface hardness is improved, and the surface oxidation and decarburization are inhibited.
P and S are both inevitable harmful impurities in steel, and their presence seriously deteriorates the toughness of steel, so that measures are taken to reduce the contents of P and S in steel as much as possible while taking into consideration the economical efficiency thereof. The invention limits the highest P content to 0.020% and the highest S content to 0.015%. In the present invention, since sulfur exists in the form of FeS and MnS in steel, Mn is high and MnS tends to be formed, and although the melting point is high and hot embrittlement can be avoided, MnS can be elongated in the machine direction during deformation by machining, and plasticity, toughness and fatigue strength of steel are significantly reduced, Ca, Mg and Re are added to steel to perform inclusion modification treatment.
Tin is considered as a harmful impurity element in steel, is easy to cause hot brittleness and temper brittleness of the steel, causes cracking, influences the quality of steel products such as welding performance and the like, and is one of five harms of steel. However, tin improves the wear resistance of steel and the fluidity of molten steel. Good fluidity of molten steel, full floating of inclusions, good purity of steel, smooth surface and no oxidation. The cutting tool steel has high carbon content, is easy to segregate to separate out graphite, and influences the service performance. Therefore, a certain amount of tin is added into the steel, so that the graphitization precipitation of the high-carbon steel can be effectively prevented, and the comprehensive properties such as strength, wear resistance and the like are improved. In addition to strengthening the steel matrix, Sn dissolved in the steel can also generate SnC hard phases with C, and the SnC hard phases block the deformation of cementite in sorbite during the third rolling, so that the cementite is more easily broken. On the other hand, the casting blank disclosed by the invention has the combined action of higher Sn and Re content on the surface, generates a ReSnC granular phase which is pinned in grains and in a grain boundary, improves the surface hardness, inhibits surface oxidation and decarburization, enables the depth of a surface grain boundary oxidation layer and a decarburized layer to be 0mm, realizes 100% of electroplating qualified rate after omitting a sand throwing process, has the surface hardness still higher than 48HRC, does not need heat treatment, and is low in cost and low in energy consumption.
The key process for producing the cutting tool steel comprises the following steps:
1. smelting process;
(1) the tool steel plate is formed by casting molten steel after smelting in a converter and refining in an electric furnace into a continuous casting blank and then rolling the continuous casting blank, wherein the thickness of the continuous casting blank is 170-250 mm.
(2) Deoxidizing by using an Al deoxidizer, adding Ca for treatment after the oxygen content in the steel is less than or equal to 0.0020% during refining, adding other alloys along the wall of the tundish after the Ca treatment is carried out for at least 5 minutes, adding Re-Mg alloy firstly, and adding Sn alloy finally;
(3) the argon blowing time of the tundish is 5-8 minutes, so that impurities are fully floated, and the casting superheat degree is less than or equal to 25 ℃.
(4) Under the condition of continuous casting pressure, electromagnetically stirring with a crystallizer, wherein a stirring coil is made of pure carbon material, electromagnetically stirring for 1-3 minutes, and the current intensity is more than 1000A; the rolling reduction is 10 mm-30 mm;
(5) the continuous casting speed is 1.0 m/min-1.4 m/min.
2. A casting blank treatment process;
(1) the casting blank is inserted into a slow cooling pit for slow cooling for more than 72 hours, and the casting blank is heated by a stepping heating furnace before rolling, wherein the temperature of the preheating section of the heating furnace is required to be more than 500 ℃;
(2) the step-type heating furnace adopts reducing atmosphere, the heating temperature of the casting blank in the heating section is 1200-1350 ℃, and the total time in the furnace is 2-4 hours.
3. A rolling process;
the method comprises three processes of rough rolling, finish rolling and third rolling, wherein high-pressure water is adopted for descaling before the rough rolling, the finish rolling and the third rolling, and the high-pressure water pressure is not less than 30MPa, so that the surface quality of a steel plate is ensured;
(1) the rough rolling adopts the first rolling with a large reduction rate of more than or equal to 50 percent to fully break the coarse grains of the casting blank;
(2) the finish rolling adopts a continuous rolling mode of not less than 6 passes, the total rolling reduction rate is not less than 80 percent, the first pass rolling reduction rate is not less than 30 percent, the high-temperature rapid rolling is carried out, the rolling speed is not less than 25m/s, the initial rolling temperature is 1100-1150 ℃, and the finishing temperature is 900-950 ℃;
(3) after finish rolling, the steel plate enters laminar cooling and is quenched at the cooling speed of more than or equal to 25 ℃/s, and is cooled to 500-680 ℃ and then enters a double-vertical-roller four-horizontal-roller mill for continuous two-pass rolling, wherein the upper and lower reduction rate is 10-20%, and the side pressure reduction rate is 5-20%;
4. a cooling process;
after the third rolling, the steel plate directly enters an induction annealing unit for annealing, the cooling speed is 20 ℃/h-50 ℃/h, the steel plate is cooled to below 200 ℃ for air cooling, the room-temperature structure of the steel plate is spheroidized sorbite, and the spheroidization rate is 100%.
The cutting tool steel has high carbon, oxygen content is difficult to control, the molten steel has poor fluidity, and in order to improve the fluidity of the molten steel, the deoxidation is sufficient, Al deoxidizer is firstly used for deoxidation, after the oxygen content is less than or equal to 0.0020 percent, Ca is added for at least 5 minutes, and then Re-Mg alloy and Sn are added. Ca, Mg and Re in the components of the invention are all active elements, are difficult to control during smelting, and the adding sequence is very important. Al is generated in the steel after Al addition and deoxidation2O3Impurities, if the refractory material of the lining is poor, MgO. Al will be formed2O3And the melting point of the Al oxide inclusions is high, the Al oxide inclusions are not easy to solidify and float in steel, on one hand, the fluidity of molten steel is reduced, a pouring nozzle is blocked, on the other hand, the inclusions in the steel are increased, and the bending and fatigue properties of the steel are influenced. Adding Al for deoxidation, and then adding Ca for treatment, wherein the Ca can break the original long strip Al2O3 and MgO & Al2O3And MnS inclusions, which are wrapped outside the intermittent inclusions to generate spherical CaO, MgO, Al in a dispersed distribution2O3Or CaO. Al2O3And CaO & MnS composite oxides, the inclusions are refined and spheroidized, and the small-particle calcium aluminate composite inclusions have low melting point and are easy to solidify, float and remove in molten steel, so that the problem of nozzle nodulation in the continuous casting process is avoided, the inclusion content in the molten steel is reduced, and the inclusion level in the steel is ensured not to exceed 1.0 level. After Ca treatment for 5 minutes, the denatured inclusion floats sufficiently, after the molten steel is purified, Re-Mg and Sn alloy are added, the yield of Re and Mg is improved by redundant free Ca in the molten steel, the yield of Re is improved to more than 60% by Ca, and the yield of Mg is as high as more than 40%. Re and Mg in steel react with C to produce a series of carbides, such as Re-MgC2、Re-Mg2C3Further promoting hot rolling to form a fine sorbite structure with the sheet spacing of 0.15-0.5 mu m, and preparing for obtaining spheroidized sorbite to improve the bending performance.
Ca. Re can modify oxide and sulfide inclusions, and simultaneously can increase the fluidity of molten steel together with Sn, improve the floating speed of the inclusions, and promote the inclusions to fully float after modification treatment by blowing argon for 5-8 minutes in a tundish, thereby ensuring that various non-metal inclusions in the steel do not exceed 1.0 level of purity, saving nearly half time compared with common cutting tool steel, saving energy, reducing consumption and improving productivity.
The cutting tool steel has high carbon content, is easy to segregate to separate out graphite, and influences the service performance. Therefore, according to the invention, a certain amount of tin is added into steel, and meanwhile, the process that the superheat degree is less than or equal to 25 ℃ is controlled, so that the macrosegregation of the carbon of the casting blank is improved, the graphitization and precipitation of high-carbon steel are effectively prevented, and the comprehensive properties such as strength, wear resistance and the like are improved. Re, Mg and Sn added along the tundish wall at the later stage of smelting can improve the fluidity of steel, and Re and Sn are uniformly diffused under the action of electromagnetic stirring centrifugal force and are uniformly distributed near the tundish wall. The electromagnetic stirring coil is made of pure carbon materials, the current intensity is more than 1000A, the electromagnetic stirring is carried out for 1-3 minutes, the diffusion capacity of Re and Sn is strong, the continuous casting drawing speed is controlled to be 1.0-1.4 m/min, a layer of region with high Re and Sn content exists under the surface of a casting blank after continuous casting and drawing, the depth of the surface layer with high alloy content is not less than 15% of the thickness of the casting blank, and the content of Re and Sn in the surface layer is 5-8 times of the core content of the casting blank. When the casting blank is cooled to 900-1000 ℃, the reduction is 10-30 mm, high-content Re, Sn and C under the surface of the casting blank react under the action of external force deformation energy to generate ReSnC pinning at a surface grain boundary, so that the surface oxidation and decarburization are effectively inhibited, the electroplating qualification rate is improved, and the surface hardness is improved. The stirring current intensity is less than 1000A, the stirring time is less than 1 minute, the Re and Sn are not fully diffused, the depth of the ReSnC particle layer on the surface of the steel plate is 10 percent of the thickness of the steel plate, and the hardness is not enough. The stirring time is longer than 3 minutes, the alloy elements are seriously diffused, and the surface of the casting blank is easy to crack. The reduction less than 10mm does not provide sufficient phase transformation energy for generating ReSnC, and the casting blank cracks with the reduction more than 30 mm. The casting blank reduction temperature is too low or too high, which is not beneficial to the generation of ReSnC.
And after the casting blank is off-line, the casting blank is placed into a slow cooling pit for slow cooling for more than 72 hours, so that the tool steel casting blank with relatively high alloy content is prevented from cracking under the action of stress, and SnC particles are generated in the steel to prepare for crushing the carbide sheet for the third rolling. And the generation of ReSnC is promoted, the ReSnC is uniformly dispersed and distributed on the surface of a casting blank, and the depth of a surface hardening particle layer of the rolled steel plate is more than 10 percent of the thickness of the steel plate.
A step-by-step heating furnace is adopted for heating before rolling the casting blank, the temperature of a preheating section in front of a heating section of the heating furnace is more than 500 ℃, and the phenomenon that the temperature difference between the inside and the outside of the casting blank in the heating section is too large to generate internal stress and thermal stress cracking is prevented; the heating furnace adopts reducing atmosphere to resist the surface oxidation and decarburization of the casting blank. The heating temperature of the heating section is 1200-1350 ℃, the total time of the heating section is 2-4 hours, the uniform heating and the uniform composition of the casting blank are ensured, the segregation is reduced, and the bending performance is improved.
Coarse,Before finish rolling, multi-channel high-pressure water under the pressure of more than 30MPa is continuously adopted for descaling, the rolling speed is more than or equal to 25m/S, the descaling method is beneficial to removing the iron scale on the surface of the broken steel plate, no obvious crystal boundary oxidation and decarburization exist on the surface of the steel plate, the surface quality and the bending performance of the steel plate are improved, and the grinding amount is reduced; the first reduction rate of rough rolling is more than or equal to 50%, primary iron oxide scales on the surface of the casting blank are fully crushed, and meanwhile, coarse columnar grains of the casting blank are crushed to promote the formation of fine austenite. The finish rolling adopts 6-pass high-temperature fast rolling, the total reduction rate is more than or equal to 80 percent, the first-pass reduction rate is more than or equal to 30 percent, the rolling temperature is 1100-1150 ℃, the finishing temperature is 900-950 ℃, fine austenite grains are formed, and secondary oxidation and decarburization on the surface are avoided. Through the rolling with large reduction of rough rolling and finish rolling, Re-MgC is generated in the steel2、Re-Mg2C3The carbide provides sufficient phase transformation energy to obtain a sorbite structure with a chip spacing of 0.15-0.5 μm.
And (3) after finish rolling, descaling by using high-pressure water of more than 30MPa, and cleaning the surface of the scale. The steel plate is rapidly cooled to 500-680 ℃ at the cooling speed of more than or equal to 25 ℃/s, and is subjected to Re-MgC2、Re-Mg2C3Obtaining the sorbite structure with the sheet spacing of 0.15-0.5 mu m under the action of the carbide. In order to obtain a globularized sorbite structure easily after annealing, the steel plate is quickly cooled and then is immediately subjected to third rolling. The third rolling is continuously carried out for two times by adopting a rolling machine with two vertical rollers and four horizontal rollers, the upper and lower reduction rates are 10-20%, the side pressure reduction rate is 5-20%, the carbon sheet in the sorbite is completely cracked, the carbon diffusion is fast during annealing, and the globularization structure is obtained. The four-horizontal-roller mill is adopted for continuous two-pass rolling, the side pressure is provided, the carburated sheet is smashed in an all-round mode twice, the carburated sheet is smaller, and carbon is easier to diffuse. The rolling also provides phase transformation energy for a large amount of fine ReSnC particles generated under the surface of the steel plate, further promotes the generation of a large amount of fine ReSnC particles, the particles improve the surface hardness of the steel plate to be more than 48HRC, the particles are not decomposed during annealing, and the high surface hardness is still maintained. After the third rolling, a ReSnC hardened particle layer with the dispersion distribution diameter not more than 20nm is formed below the surface of the steel plate, the depth of the hardened particle layer is not less than 10% of the thickness of the steel plate, and simultaneously, the surface oxidation and decarburization are inhibited, so that the surface hardness of the steel plate does not need to be heat treated and is more than 48HRC, and the wear rate is not more than 30 mg/km.
The cooling speed is more than or equal to 25 ℃/s, the ReSnC under the surface of the steel plate does not grow, the diameter is not more than 20nm, the ReSnC is still fine and dispersed, the surface hardness is improved, and the oxidation and decarburization are inhibited. The cooling speed is lower than 25 ℃/s, the carburized body piece is not easy to break after growing up, the hardening effect of the ReSnC particles under the surface of the steel plate is not good, and the toughness and the plasticity are poor. The rolling temperature is higher than 680 ℃, the reduction rate is lower than 10%, and the energy for crushing the carbon carbide pieces is insufficient. The rolling temperature is lower than 500 ℃, the reduction rate is too high, the rolling force is large, the load of a rolling mill is too large, the storage energy in steel is large, and the ReSnC particles also grow up rapidly to influence the toughness and plasticity.
After the third rolling, the steel plate is not coiled and is directly put into an induction annealing device for on-line continuous annealing at the annealing speed of 20-50 ℃/h, heating is not needed before annealing, the cost is low, the production efficiency is high, the room-temperature tissue of the steel plate can be a tempered sorbite with the spheroidization rate of 100 percent only by one-time annealing, the tensile strength of the final steel plate is 700-800 MPa, the yield ratio is below 50 percent, the steel plate does not crack after being bent at 180 degrees, and three times of oxidation decarburization can not occur on the surface. The annealing speed is more than 50 ℃/h, the spheroidization effect is poor, and the spheroidization rate is low; the annealing speed is less than 20 ℃/h, three times of oxidation and decarburization can occur on the surface of the steel plate, and the ReSnC particles grow up to influence the surface hardness.
The production process of the cutting tool steel and the processing accessories thereof comprises the following steps: smelting, electromagnetically stirring and pressing a casting blank, hot rolling, annealing, obtaining high-surface hardness steel (replacing offline finished product heat treatment), performing punch forming, performing barreling, electroplating and assembling; the production process of the existing other tool steel and processing accessories comprises the following steps: smelting, hot rolling, cold rolling, annealing, punch forming, heat treatment, sand throwing, roller burnishing, electroplating and assembling. Therefore, when the steel plate is used for processing mechanical parts needing electroplating, three processes of cold rolling, heat treatment and sand blasting are omitted, the production cost is greatly reduced, energy conservation and consumption reduction are realized, the electroplated surface has no corrosion defects such as mildew and the like, and the electroplating qualified rate of products is 100%.
The following examples are carried out on the premise of the technical scheme of the invention, and detailed embodiments and specific operation processes are given, but the scope of the invention is not limited to the following examples.
[ examples ] A method for producing a compound
In this example, the chemical composition of the blade steel is shown in table 1.
TABLE 1 chemical composition and smelting Process%
| Examples | C | Si | Mn | P | S | Als | Sn | Mg | Ca | Re | Ca/Mg | Ca/Re | Ca/S |
| 1 | 0.65 | 0.02 | 0.90 | 0.015 | 0.015 | 0.02 | 0.3 | 0.004 | 0.005 | 0.25 | 1.25 | 0.02 | 0.33 |
| 2 | 0.69 | 0.1 | 1.42 | 0.004 | 0.009 | 0.035 | 0.9 | 0.02 | 0.022 | 0.12 | 1.10 | 0.18 | 2.44 |
| 3 | 0.78 | 0.07 | 0.91 | 0.008 | 0.011 | 0.012 | 0.1 | 0.005 | 0.01 | 0.09 | 2.00 | 0.11 | 0.91 |
| 4 | 0.60 | 0.05 | 0.65 | 0.010 | 0.008 | 0.032 | 0.5 | 0.005 | 0.005 | 0.22 | 1.00 | 0.02 | 0.63 |
| 5 | 0.75 | 0.04 | 0.80 | 0.012 | 0.001 | 0.025 | 0.8 | 0.0005 | 0.0008 | 0.02 | 1.60 | 0.04 | 0.80 |
| 6 | 0.88 | 0.05 | 0.75 | 0.014 | 0.003 | 0.056 | 0.21 | 0.001 | 0.002 | 0.03 | 2.00 | 0.07 | 0.67 |
| 7 | 0.82 | 0.06 | 0.88 | 0.013 | 0.013 | 0.06 | 0.16 | 0.02 | 0.027 | 0.17 | 1.35 | 0.16 | 2.08 |
| 8 | 0.77 | 0.07 | 1.32 | 0.014 | 0.004 | 0.028 | 0.28 | 0.006 | 0.009 | 0.069 | 1.50 | 0.13 | 2.25 |
| 9 | 0.72 | 0.05 | 0.99 | 0.012 | 0.007 | 0.035 | 0.17 | 0.03 | 0.035 | 0.042 | 1.17 | 0.83 | 5.00 |
| 10 | 0.65 | 0.06 | 1.18 | 0.010 | 0.01 | 0.045 | 0.5 | 0.004 | 0.004 | 0.07 | 1.00 | 0.06 | 0.40 |
| 11 | 0.90 | 0.09 | 0.50 | 0.008 | 0.012 | 0.035 | 0.22 | 0.03 | 0.045 | 0.5 | 1.50 | 0.09 | 3.75 |
| 12 | 0.78 | 0.06 | 1.32 | 0.013 | 0.006 | 0.036 | 0.48 | 0.002 | 0.008 | 0.016 | 4.00 | 0.50 | 1.33 |
| 13 | 0.63 | 0.08 | 1.38 | 0.013 | 0.008 | 0.046 | 0.16 | 0.009 | 0.01 | 0.097 | 1.11 | 0.10 | 1.25 |
| 14 | 0.70 | 0.07 | 0.92 | 0.014 | 0.014 | 0.079 | 0.79 | 0.008 | 0.009 | 0.18 | 1.13 | 0.05 | 0.64 |
| 15 | 0.82 | 0.03 | 0.59 | 0.012 | 0.007 | 0.036 | 0.12 | 0.006 | 0.0086 | 0.15 | 1.43 | 0.06 | 1.23 |
| 16 | 0.69 | 0.08 | 0.68 | 0.010 | 0.01 | 0.027 | 0.55 | 0.0034 | 0.005 | 0.24 | 1.47 | 0.02 | 0.50 |
| 17 | 0.76 | 0.05 | 0.80 | 0.015 | 0.005 | 0.042 | 0.35 | 0.01 | 0.01 | 0.02 | 1.00 | 0.50 | 2.00 |
| 18 | 0.75 | 0.07 | 1.32 | 0.004 | 0.009 | 0.036 | 0.62 | 0.01 | 0.03 | 0.092 | 3.00 | 0.33 | 3.33 |
| Comparative example 1 | 0.63 | 0.25 | 0.6 | 0.012 | 0.008 | - | - | - | - | - | - | - | - |
| Comparative example 2 | 0.73 | 0.20 | 0.62 | 0.010 | 0.005 | - | - | - | - | - | - | - | - |
In the present example, the production process parameters of the cutting tool steel are shown in tables 2 and 3.
Table 2: smelting production process of hot-rolled strip steel
Table 3: rolling and cooling production process
In this example, the properties of the produced cutting tool steel are shown in table 4.
TABLE 4 Steel sheet Properties
The structural morphology of spheroidized sorbite of the steel plate of example 3 (1000 times) is shown in FIG. 1, the structural morphology of the lower hardened particle layer of the steel plate of example 3 (1000 times) is shown in FIG. 2, and FIG. 3 is the structural morphology of the steel plate of comparative example 1 (500 times).
The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art should be considered to be within the technical scope of the present invention, and the technical solutions and the inventive concepts thereof according to the present invention should be equivalent or changed within the scope of the present invention.
Claims (5)
1. The production method of the high-carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending performance is characterized in that the steel plate comprises the following chemical components in percentage by weight: 0.60 to 1.0 percent of C, less than or equal to 0.1 percent of Si, 0.4 to 1.5 percent of Mn, 0.0005 to 0.05 percent of Ca, 0.01 to 0.5 percent of Re, less than or equal to 0.06 percent of Al, less than or equal to 0.05 percent of Mg, more than or equal to 0.3 percent of Ca/S, more than or equal to 1 percent of Ca/Mg, more than or equal to 0.02 percent of Ca/Re, 0.1 to 1.0 percent of Sn, less than or equal to 0.020 percent of P, less than or equal to 0.015 percent of S, and the balance of Fe and inevitable impurities;
the production process of the cutting tool steel comprises smelting, continuous casting, casting blank treatment, rolling and cooling processes, wherein the production process comprises the following steps:
1) smelting process;
deoxidizing by using an Al deoxidizer, adding Ca for treatment after the oxygen content in the steel is less than or equal to 0.0020% during refining, adding other alloys along the wall of the tundish after the Ca treatment is carried out for at least 5 minutes, adding Re-Mg alloy firstly, and adding Sn alloy finally;
2) a continuous casting process;
blowing argon for 5-8 minutes in the tundish, and controlling the degree of superheat of pouring to be less than or equal to 25 ℃; the continuous casting adopts a pressing process and crystallizer electromagnetic stirring, a stirring coil is made of pure carbon materials, electromagnetic stirring is carried out for 1-3 minutes, and the current intensity is over 1000A; the rolling reduction is 10 mm-30 mm; the continuous casting speed is 1.0-1.4 m/min;
3) a casting blank treatment process;
the casting blank is subjected to off-line slow cooling for more than 72 hours, the casting blank is sent to a stepping heating furnace for heating before rolling, the inside of the stepping heating furnace adopts reducing atmosphere, the temperature of the casting blank in a preheating section is more than 500 ℃, the heating temperature of a heating section is 1200-1350 ℃, and the total time of the furnace is 2-4 hours;
4) a rolling process;
the rolling process comprises three procedures of rough rolling, finish rolling and third rolling:
a) the first pass reduction rate of rough rolling is more than or equal to 50 percent;
b) the finish rolling adopts a continuous rolling mode of not less than 6 passes, the total rolling reduction rate is not less than 80 percent, the first pass rolling reduction rate is not less than 30 percent, the rolling speed is not less than 25m/s, the initial rolling temperature is 1100-1150 ℃, and the finishing temperature is 900-950 ℃;
c) after finish rolling, the steel plate enters laminar cooling and is quenched at the cooling speed of more than or equal to 25 ℃/s, and is cooled to 500-680 ℃ and then enters a double-vertical-roller four-horizontal-roller mill for continuous two-pass rolling, wherein the upper and lower reduction rate is 10-20%, and the side pressure reduction rate is 5-20%;
5) a cooling process;
after the third rolling, the steel plate directly enters an induction annealing unit for annealing, the cooling speed is 20-50 ℃/h, and the steel plate is cooled to below 200 ℃ for air cooling.
2. The method for producing a high-carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending property according to claim 1, wherein the structure of the steel plate is a sorbite structure with 100% spheroidization rate, the tensile strength is 700MPa to 800MPa, the yield ratio is less than or equal to 50%, and the steel plate does not crack when bent at 180 degrees.
3. The method for producing high carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending property according to claim 1, wherein a ReSnC hardening particle layer with the diameter not more than 20nm is dispersedly distributed under the surface of the steel plate, the depth of the hardening particle layer is not less than 10% of the thickness of the steel plate, the depths of a grain boundary oxidation layer and a decarburized layer are both 0mm, the surface hardness after annealing is more than 48HRC, and the wear rate is not more than 30 mg/km.
4. The production method of the high-carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending property according to claim 1, characterized in that the smelting process comprises converter smelting and electric furnace refining, and the thickness of a continuous casting billet is 170-250 mm.
5. The method for producing a high carbon spheroidized sorbite cutting tool steel with high surface hardness and excellent bending property according to claim 1, wherein high-pressure water is used for descaling before rough rolling, finish rolling and third rolling, and the high-pressure water pressure is not less than 30 MPa.
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102851622A (en) * | 2012-09-19 | 2013-01-02 | 南京钢铁股份有限公司 | Superhigh-strength high-toughness steel plate for ocean engineering and production method thereof |
| CN109280847A (en) * | 2018-10-08 | 2019-01-29 | 鞍钢股份有限公司 | High-carbon alloy chain tool steel and manufacturing method thereof |
| CN110318008A (en) * | 2019-06-20 | 2019-10-11 | 江阴兴澄特种钢铁有限公司 | A kind of anti-960MPa grades of high strength steel plates of lamellar tearing yield strength of big thickness and its production method |
| CN111411311A (en) * | 2020-04-30 | 2020-07-14 | 鞍钢股份有限公司 | Steel for die casting corrosion-resistant chain plate and manufacturing method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102851622A (en) * | 2012-09-19 | 2013-01-02 | 南京钢铁股份有限公司 | Superhigh-strength high-toughness steel plate for ocean engineering and production method thereof |
| CN109280847A (en) * | 2018-10-08 | 2019-01-29 | 鞍钢股份有限公司 | High-carbon alloy chain tool steel and manufacturing method thereof |
| CN110318008A (en) * | 2019-06-20 | 2019-10-11 | 江阴兴澄特种钢铁有限公司 | A kind of anti-960MPa grades of high strength steel plates of lamellar tearing yield strength of big thickness and its production method |
| CN111411311A (en) * | 2020-04-30 | 2020-07-14 | 鞍钢股份有限公司 | Steel for die casting corrosion-resistant chain plate and manufacturing method thereof |
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