WO2015043057A1 - 一种非调质钢及其生产工艺 - Google Patents

一种非调质钢及其生产工艺 Download PDF

Info

Publication number
WO2015043057A1
WO2015043057A1 PCT/CN2013/088377 CN2013088377W WO2015043057A1 WO 2015043057 A1 WO2015043057 A1 WO 2015043057A1 CN 2013088377 W CN2013088377 W CN 2013088377W WO 2015043057 A1 WO2015043057 A1 WO 2015043057A1
Authority
WO
WIPO (PCT)
Prior art keywords
cooling
quenched
temperature
tempered steel
steel
Prior art date
Application number
PCT/CN2013/088377
Other languages
English (en)
French (fr)
Inventor
刘栋林
周旭
徐益峰
周志伟
俞杰
Original Assignee
北大方正集团有限公司
苏州苏信特钢有限公司
江苏苏钢集团有限公司
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 北大方正集团有限公司, 苏州苏信特钢有限公司, 江苏苏钢集团有限公司 filed Critical 北大方正集团有限公司
Priority to EP13894743.7A priority Critical patent/EP3050991A4/en
Priority to US15/023,513 priority patent/US20160208356A1/en
Priority to JP2016516510A priority patent/JP2017502165A/ja
Publication of WO2015043057A1 publication Critical patent/WO2015043057A1/zh

Links

Classifications

    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • 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
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/60—Aqueous agents
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • 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
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • 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
    • 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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • 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

Definitions

  • the invention relates to a non-quenched and tempered steel and a production process thereof, and belongs to the field of steel metallurgy technology.
  • Non-quenched and tempered steel refers to mechanical structural steel that can meet the performance requirements without quenching and tempering.
  • the use of such steel to manufacture parts can eliminate the quenching and tempering heat treatment process, which has the advantages of energy saving, materials and simple process, and can reduce the environment. Pollution, avoid oxidation, decarburization, deformation, cracking.
  • Shougang Corporation has proposed a new non-quenched and tempered steel production process, which mainly includes: converter smelting, slag tapping, ladle deoxidation alloying, LF ladle refining, feeding S line, ladle bottom blowing argon to achieve The steps of full protection casting, temperature control of the casting blank, controlled cooling, and rolling, wherein, in the rolling step, the heating temperature is 1100 ⁇ 1180.
  • the rolling temperature is 1020 ⁇ 1100.
  • C finishing temperature 850 ⁇ 920.
  • C the relative deformation is 15 ⁇ 35%, and is cooled to 600 after rolling. After C, slowly cool to room temperature.
  • the non-quenched and tempered steel produced by the above process is difficult to ensure the core and surface of the steel in a short time by slow cooling.
  • the temperature tends to be uniform, which tends to cause great fluctuations in the strength and toughness of the steel surface and the core, and the mechanical properties are severely uneven.
  • the large-scale non-tempered steel is produced by the above process (for example, ⁇ 70 ⁇ ⁇ 145 ⁇ bar)
  • the bar The phenomenon of uneven mechanical properties of the surface and the core of the bar is more pronounced.
  • the technical problem to be solved by the present invention is to overcome the defects of surface mechanical properties and uneven core force performance of the steel produced by the existing non-quenched and tempered steel production process, thereby providing a non-quenched and tempered steel and a production process thereof. Ensure the surface mechanical properties of the finished product and the uniformity of the core mechanical properties.
  • the present invention provides a non-quenched and tempered steel which is composed of the following chemical components: carbon 0.42 ⁇ 0.50, silicon 0.20 ⁇ 0.40, manganese 0.50 ⁇ 1.0, chromium 0.00 ⁇ 0.30, stroke 0.010 ⁇ 0.030, nickel 0.00 ⁇ 0.10, copper 0.00 ⁇ 0.20, brick 0.000 ⁇ 0.025, sulfur 0.00 ⁇ 0.025, and the balance is iron.
  • the non-modulated steel of the present invention consists of the following chemical composition: carbon 0.42 ⁇ 0.45, silicon 0.20 ⁇ 0.30, sample 0.50 ⁇ 0.7, chromium 0.00 ⁇ 0.30 0.010 ⁇ 0.030, nickel 0.00 ⁇ 0.10, copper 0.00 ⁇ 0.20, brick 0.000 ⁇ 0.025, sulfur 0.00 ⁇ 0.025, and the balance is iron.
  • the non-modulated steel of the present invention consists of the following chemical composition: carbon 0.42 ⁇ 0.47, silicon 0.25 ⁇ 0.35, manganese 0.60 ⁇ 1.0, chromium 0.00 ⁇ 0.30, aluminum 0.010 ⁇ 0.030, nickel 0.00 ⁇ 0.10, copper 0.00 ⁇ 0.20, brick 0.000 ⁇ 0.025, sulfur 0.00 ⁇ 0.025, and the balance is iron.
  • the non-modulated steel of the present invention consists of the following chemical composition: carbon 0.45 ⁇ 0.50, silicon 0.25 ⁇ 0.35, manganese 0.60 - 0.9, chromium 0.00 - 0.30 0.010 ⁇ 0.030, nickel 0.00 ⁇ 0.10 , copper 0.00 ⁇ 0.20, brick 0.000 - 0.015, sulfur 0.00 - 0.015, and the balance is iron.
  • the invention provides a production process of non-quenched and tempered steel, comprising a cooling step performed at least after the finishing rolling step, in which the alternating weak and weak cooling is used
  • the steel is cooled by at least two stages of water penetration so that the core temperature of the steel tends to coincide with the surface temperature for a certain period of time.
  • the steel material is subjected to three-stage water-passing cooling, wherein the first stage water-cooling is cooled by strong cooling, and the second stage is cooled by water. Weak cooling is used, and the third section is cooled by water.
  • the strength of the cooling is controlled by controlling the degree of opening of the valve of the water-passing cooling device.
  • the steel material is lowered by 100 in 4 to 7 seconds after being cooled by water.
  • C ⁇ 400. C wait for the steel to return to temperature and then cool down again 50.
  • the opening degree of the first stage valve is controlled to be 30% to 40%, and the opening degree of the second stage valve is 20%, and the third stage valve is opened.
  • the degree is 30% ⁇ 40% to ensure that the steel surface temperature is lowered by 100 ° C - 400 in 4 ⁇ 7 seconds. C.
  • the steel material is cooled and cooled by spray cooling after the steel material is warmed up.
  • the steel material is dispersed and placed on a cold bed for air cooling for 10 to 12 minutes.
  • the steel materials are stacked and then subjected to leather cooling.
  • a finishing rolling step before the cooling step is also included, in which the temperature at which the steel material enters the finishing rolling step is controlled to be ⁇ 950. C, at a steel temperature of 850. C ⁇ 900. Low temperature rolling was carried out under C conditions.
  • the smelting step before the finishing rolling step is further included, and the smelting step includes an electric furnace smelting step, a ladle furnace smelting step, and a refining step which are sequentially performed.
  • the whole molten iron smelting is adopted in the electric furnace smelting, the end phosphorus content is ⁇ 0.015%, the end carbon content is 0.03% ⁇ 0.10%, and the end point temperature is 1620. C ⁇ 1700. C.
  • silicon carbide and ferrosilicon powder are used for deoxidation in the ladle furnace smelting step and/or the refining step.
  • the refining time is ensured to be not less than 45 minutes, and the hydrogen content is controlled to be less than 1.5 ppm.
  • the production process of the non-quenched and tempered steel provided by the present invention further includes a continuous casting step after the refining step, in which the superheat degree is controlled at 20 to 35 ° C and the pulling speed is controlled at 0.5 m/ Min - 0.6m/ mm.
  • the production process of the non-quenched and tempered steel provided by the present invention further includes a heating step after the continuous casting step, in which the slab is placed in a heating furnace for heating, wherein the temperature of the preheating section is controlled at 850 ⁇ 30 .
  • the heating section temperature is controlled at 1100 ⁇ 30.
  • the temperature of the soaking section is controlled at 1130 ⁇ 30°C, and the total time of the soaking section is not less than 2 hours.
  • the present invention provides a process for the production of non-quenched and tempered steel, the process comprising the steps of:
  • Electric furnace smelting step providing iron raw material with desired steel composition, using full iron smelting in the electric furnace smelting, the end phosphorus content is ⁇ 0.015%, the end carbon content is 0.03% ⁇ 0.10%, and the end temperature is 1620°C ⁇ 1700 ° C ;
  • continuous casting step continuous casting of the steel melt obtained by the refining step, the superheat of the steel melt is controlled at 20 ⁇ 35 ° C, and the pulling speed is controlled at 0.5 m / min ⁇ 0.6 m / min;
  • Heating step the slab produced by the continuous casting step is placed in a heating furnace for heating, wherein the temperature of the preheating section is controlled at 850 ⁇ 30. C, the heating section temperature is controlled at 1100 ⁇ 30°C, the soaking section temperature is controlled at 1130 ⁇ 30°C, and the soaking section total time is not less than 2 hours;
  • Cooling step wherein the steel material is cooled by at least two stages of water passage in a manner of alternating strong and weak cooling so that the core temperature and the surface temperature tend to coincide during cooling.
  • the production process of the non-quenched and tempered steel changes the manner of cooling before the finish rolling in the production of the non-tempered steel in the past, at least after the finishing rolling step, and the cooling method changes the prior art
  • the use of a single water-cooled or air-cooled and consistent cooling method alternates between strong cooling and weak cooling. Strong cooling ensures that the surface temperature of the steel is rapidly reduced.
  • the weak cooling allows the temperature of the core of the steel to gradually spread to the surface, followed by Strong cold, so that the heat is quickly dissipated, according to actual needs, strong cold and weak cold can be alternated several times, the combination of strong and weak cold water cooling method makes the temperature of the steel core and the temperature of the surface in a short time That is, it tends to be consistent, thereby ensuring the uniformity of the mechanical properties of the steel and improving the production efficiency.
  • the steel material is subjected to three stages of water-passing cooling, wherein the first stage water-cooling is cooled by strong cooling, and the second section is cooled by water. Weak cooling is used, and the third section is cooled by water. After the finish rolling, the temperature of the steel is higher.
  • the first stage is cooled by water
  • the surface temperature of the steel is rapidly lowered. Due to the heat transfer, the heat of the core is gradually transferred to the surface after the surface temperature is lowered.
  • a weak cooling method is adopted.
  • the heat transfer causes the surface temperature to rise, and the surface is cooled again by the strong cooling method. Thereby, the surface heat is quickly taken away, and at this time, the heat transfer causes the surface temperature and the core temperature to converge, thereby ensuring uniformity of mechanical properties.
  • the production process of the non-quenched and tempered steel provided by the present invention, in the cooling step, controlling the strength of the cooling by controlling the degree of opening of the valve of the water-passing cooling device, specifically, controlling the opening degree of the first stage valve to be 30% ⁇ 40%, the second valve opening is 20%, the third valve opening is 30% ⁇ 40%, to ensure that the steel surface temperature is reduced by 100 ° C ⁇ 400 ° C in 4 ⁇ 7 seconds, through Controlling the opening degree of the valve can control the water flow rate, and then control the strength of the water-through cooling.
  • the control method is very simple. After the valve is opened for a certain length, the steel is penetrated into the water for water treatment, and the steel is in the process of water penetration. The surface is cooled in all directions to ensure uniformity of surface cooling.
  • the production process of the non-quenched and tempered steel provided by the present invention, in the cooling step, after the steel material is returned to the temperature, the steel material is cooled and cooled by means of spray cooling.
  • the way of spray cooling is a favorable supplement to water-cooling.
  • spray cooling the heat of the core can be further diffused to the surface, which further ensures the consistency of the core and the surface temperature.
  • the production process of the non-quenched and tempered steel provided by the present invention, after the cooling and cooling, the steel material is dispersed and placed on a cold bed for air cooling for 10 to 12 minutes. After the spray is cooled, the steel is dispersed and placed on a cold bed for air cooling, which can further supplement the spray cooling, so that the surface heat is further lost.
  • the production process of the non-quenched and tempered steel provided by the present invention after the air cooling, the steel materials are stacked and then subjected to leather cooling.
  • Leather cooling is a way of slow cooling.
  • the steel is stacked and then subjected to leather cooling, after cooling by water cooling, spray cooling and air cooling.
  • the surface temperature of the steel is basically consistent with the core temperature. At this time, the cooling rate is lowered by the method of leather cooling, which is beneficial to improve the microstructure of the steel.
  • the production process of the non-quenched and tempered steel ensures that the refining time is not less than 45 minutes in the refining step, and the hydrogen content is controlled to be less than 1.5 ppm, and the refining process effectively controls the hydrogen content, which may be more Good to solve the risk of hydrogen cracking in the subsequent steel; more time to make the composition more uniform; give the inclusions more full floating time, effectively solve the problem of inclusion control, making the finished product more pure.
  • the superheat degree is strictly controlled at 20 to 35 in the continuous casting step.
  • the pulling speed is controlled from 0.5m/min to 0.6m/min.
  • the low superheat and continuous drawing speed of continuous casting ensure the quality of the slab.
  • the non-quenched and tempered steel provided by the invention has a metallographic structure of 500 times magnification as ferrite and pearlite, and the actual grain size (100 times) is rated as 10 to 11 according to GB/T6394, and the grain size is small.
  • Uniform the difference from the core to the edge is not more than 1.5, the mechanical properties of the steel surface and the core are uniform, and the strength and toughness fluctuation from the core to the edge are small, which can effectively avoid the general processing of the surface after the surface processing amount is large.
  • the mechanical properties do not meet the shortcomings of the use requirements.
  • the difference in hardness from core to edge is less than 30HB, which can effectively avoid the adverse effects on the tool and processing when the hardness changes greatly, and the inclusion content is low and the purity is high.
  • the core of the present invention is to improve the quality of the steel by substantially controlling the properties of the steel surface and the core by controlling the rolling and controlling the cooling step after rolling.
  • Specific cooling controls include:
  • the steel material is cooled by at least two stages of water passage in a manner of alternating strong and weak cooling, so that the core temperature of the steel material tends to coincide with the surface temperature in a specific time, specifically, after the finish rolling
  • the steel material is cooled by three stages of water passage, wherein the first section of the water is cooled by strong cooling, the second section is cooled by water, and the third section is cooled by water, and the concrete is cooled by water.
  • the degree of valve opening of the device controls the strength of the cooling.
  • the strong cooling generally refers to cooling with a cooling rate of ⁇ 7 e C/S
  • the weak cooling refers to cooling with a cooling rate of 2-4 ° C/s.
  • the cooling control is performed by the above method (especially, water-cooling) to change the manner of cooling before the finish rolling in the production of the conventional non-quenched and tempered steel, at least after the finishing rolling step, and the cooling method is changed.
  • a single water-cooling or air-cooling method with uniform strength is used to alternate between strong cooling and weak cooling, and strong cooling can ensure that the surface temperature of the steel is rapidly reduced, and the weak cooling can gradually spread the temperature of the steel core to the surface. Then, the strong cooling is carried out, so that the heat is quickly dissipated. According to the actual needs, the strong cooling and the weak cooling can be alternated several times.
  • the combination of strong and weak cooling combined with the water cooling method makes the temperature of the steel core in a short time and The temperature of the surface tends to be uniform, thereby ensuring the uniformity of the mechanical properties of the steel and improving the production efficiency.
  • the subsequent joint control of spray cooling, air cooling and leather cooling causes the core temperature to continuously scatter to the surface, and the surface temperature is continuously taken away, and the combination of the above cooling methods makes the cooling rate comparison. It is suitable to use leather cold after air cooling, so that the surface temperature of the steel is consistent with the core temperature, the cooling rate is not too fast, and the comprehensive mechanical properties are improved.
  • FIG. 1 is a non-tempered steel produced by the production method of the present invention.
  • Figure 2 is a photograph reflecting the grain size of a non-quenched and tempered steel produced by the production method of the present invention
  • Fig. 3 is a view showing the condition of inclusions of non-heat treated steel produced by the production method of the present invention.
  • the present embodiment provides a production method of non-quenched and tempered steel, which comprises a finish rolling step and a cooling step after finish rolling, wherein, in the finish rolling step, the temperature at which the rod is controlled to enter the finish rolling step is ⁇ 950. C, at bar temperature is 850. C ⁇ 900.
  • the water flow rate is controlled by controlling the degree of opening of the valve of the water-passing cooling device, thereby controlling the cooling strength.
  • the opening of the first section of the valve is 30% - 40%
  • the opening of the second section is 20%
  • the opening of the third section is 30% ⁇ 40%, which ensures that the surface temperature of the bar is reduced by 100 in 5 seconds.
  • C ⁇ 400 °C after the bar is returned to temperature, the temperature of the bar is lowered by 50 °C ⁇ 100 °C by spray cooling, so that the heat is quickly dissipated, and then the bar is dispersed and placed on a cold bed. Cool in air-cooled mode for 10-12 minutes, and finally the bottom of the cooling bed will cool the bar.
  • the production method of the non-quenched and tempered steel for direct cutting of the ordinary quenched and tempered 45 steel in this embodiment is such that the rod is cooled by three stages of water passage, wherein the first section is cooled by water and the second section is watered. The cooling is weakly cooled, and the third section is cooled by water. After the finish rolling, the bar temperature is higher, and the first section is cooled by water, so that the surface temperature of the bar is rapidly lowered. Due to the heat transfer, the core heat is gradually turned to the surface after the surface temperature is lowered.
  • the present embodiment provides a method for producing non-quenched and tempered steel, which is a further improvement based on the embodiment 1, and further includes, in relation to the embodiment 1, a smelting step before the finishing rolling step, the smelting step
  • the steps include an electric furnace smelting step, a ladle furnace smelting step, and a refining step.
  • the electric furnace smelting step the whole iron smelting is adopted, the phosphorus content before tapping is strictly controlled ⁇ 0.015%, the end carbon content is 0.03% ⁇ 0.10%, and the end temperature is 1620°C - 1700°C.
  • the electric furnace smelting can be more than the traditional converter smelting. Good control of slag operation.
  • the ladle furnace (LF furnace) smelting step silicon carbide and ferrosilicon powder are used for deoxidation, and lime is added to make white slag.
  • the white slag is kept for not less than 20 minutes, so that the white slag can completely remove inclusions.
  • the refining furnace (VD furnace) smelting step degassing is performed to ensure that the hydrogen content is controlled below 1.5 ppm, and the refining time is not less than 45 minutes.
  • the embodiment provides a method for producing non-quenched and tempered steel, which is a further improvement based on the embodiment 2.
  • the continuous casting step and the heating step are improved, and the continuous casting step and the heating step are both located. After the refining step, it is before the rolling step and the water cooling step.
  • the molten iron in the tundish is introduced into the crystallizer through the intrusive nozzle. It avoids the problem of easy introduction of air when introduced through the traditional nozzle.
  • argon gas is blown at the joint of the immersion nozzle and the tundish to prevent air from entering the tundish.
  • the superheat degree is strictly controlled at 20 ⁇ 35 °C, and the speed control is controlled. At 0.5m/min ⁇ 0.6m/min, the low superheat and continuous drawing speed of continuous casting ensure the quality of the slab.
  • the temperature at which the cut is made during continuous casting is controlled to be ⁇ 820. C. After cutting, the surface of the slab should be inspected manually to ensure that there are no obvious defects.
  • the slab is taken at a low magnification to ensure that the slab has no cracks, no shrinkage holes, and the center looseness is no more than 3 grades. This requirement is to ensure subsequent rolling out.
  • the preheating section is 850 ⁇ 30°C and the heating section is 1100 ⁇ 30. C, the soaking section is 1130 ⁇ 30. C, to ensure that the total heating period is not less than 2 hours.
  • This embodiment provides a non-quenched and tempered steel produced by the production method described in the above embodiment, which is composed of the following chemical components: carbon 0.42, silicon 0.20, manganese 0.50, chromium 0.30, aluminum 0.010, nickel 0.10, Copper 0.20, phosphorus 0.010, sulfur 0.015, the balance is iron.
  • This embodiment provides a non-quenched and tempered steel produced by the production method described in the above Embodiment 1, which is composed of the following chemical components: carbon 0.50, silicon 0.35, manganese 1.0, chromium 0.30, aluminum 0.030, nickel 0.10. , copper 0.20, phosphorus 0.015, sulfur 0.020, the balance is iron.
  • Example 6
  • This embodiment provides a non-quenched and tempered steel produced by the production method described in the above Embodiment 1, which is composed of the following chemical components: carbon 0.45, silicon 0.30, manganese 0.70, chromium 0.20, aluminum 0.020, nickel 0.05. , copper 0.10, phosphorus 0.010, sulfur 0.025, and the balance is iron.
  • the present embodiment provides a non-quenched and tempered steel produced by the production method described in the above embodiment 2, which is composed of the following chemical components: carbon 0.47, silicon 0.25, Manganese 0.60, chromium 0.30, aluminum 0.010, nickel 0.10, copper 0.20, phosphorus 0.010, sulfur 0.010, and the balance iron.
  • the present embodiment provides a non-quenched and tempered steel produced by the production method described in the above embodiment 2, which is composed of the following chemical components: carbon 0.48, silicon 0.28, manganese 0.8, chromium 0.30, aluminum 0.025, nickel 0.08 , copper 0.10, phosphorus 0.010, sulfur 0.015, and the balance is iron.
  • the present embodiment provides a non-quenched and tempered steel produced by the production method described in the above Embodiment 2, which is composed of a chemical composition of the following weight percentage: carbon 0.43, silicon 0.30, manganese 0.55, chromium 0.25, aluminum 0.020, Nickel 0.10, copper 0.20, sulfur 0.012, and the balance is iron.
  • Example 10 is composed of a chemical composition of the following weight percentage: carbon 0.43, silicon 0.30, manganese 0.55, chromium 0.25, aluminum 0.020, Nickel 0.10, copper 0.20, sulfur 0.012, and the balance is iron.
  • This embodiment provides a non-quenched and tempered steel produced by the production method described in the above embodiment 3, which is composed of the following chemical components: carbon 0.49, silicon 0.32, manganese 0.92, chromium 0.25, aluminum 0.018, nickel 0.20. , phosphorus 0.025, and the balance is iron.
  • the present embodiment provides a non-quenched and tempered steel produced by the production method described in the above embodiment 3, which is composed of the following chemical components: carbon 0.48, silicon 0.29, manganese 0.70, chromium 0.30, aluminum 0.028, nickel 0.15. , phosphorus 0.010, and the balance is iron.
  • the present embodiment provides a non-quenched and tempered steel produced by the production method described in the above embodiment 3, which is composed of a chemical composition having a weight percentage of carbon 0.50, silicon 0.40, manganese 1.0, chromium 0.30, and aluminum 0.018. Nickel 0.20, phosphorus 0.010, and the balance is iron.
  • the present embodiment provides a non-quenched and tempered steel produced by the production method described in the above embodiment 3, which is composed of the following chemical components: carbon 0.48, silicon 0.30, manganese 0.60, chromium 0.30, aluminum 0.015, phosphorus 0.010 , sulfur 0.010, and the balance is iron.
  • Example 14 is composed of the following chemical components: carbon 0.48, silicon 0.30, manganese 0.60, chromium 0.30, aluminum 0.015, phosphorus 0.010 , sulfur 0.010, and the balance is iron.
  • This embodiment provides a non-quenched and tempered steel produced by the production method described in the above embodiment 3, which is composed of the following chemical components: carbon 0.49, silicon 0.28, manganese 0.75, aluminum 0.018, nickel 0.10, phosphorus 0.010. And the balance is iron.
  • the present embodiment provides a non-quenched and tempered steel produced by the production method described in the above embodiment 3, which is composed of the following chemical components: carbon 0.47, silicon 0.28, manganese 0.75, aluminum 0.018, nickel 0.10, sulfur 0.010 , phosphorus 0.010, and the balance is iron.
  • the metallographic structure of the non-quenched and tempered steel core of the above embodiments 4-15 is magnified and pearlite at 500 times (as shown in Fig. 1), and the actual grain size (100 times), according to GB/
  • the T6394 has a rating of 10 to 11 (as shown in Figure 2).
  • the grain is fine and uniform.
  • the difference from the core to the edge is not more than 1.5.
  • the mechanical properties of the steel surface and the core are uniform.
  • the toughness fluctuation is very small, which can effectively avoid the shortcomings of the general material after the surface processing amount is large, the mechanical properties can not meet the requirements of use, and the hardness difference from the core to the edge is less than 30HB, which can effectively avoid the tool when the hardness changes greatly.
  • the adverse effects of processing, and the inclusion content is low, the purity is high (as shown in Figure 3).
  • the mechanical property data of the above Examples 4-15 are shown in Table 1 below.
  • Table 1 the yield strength, tensile strength, elongation, and shrinkage ratio of the non-quenched and tempered steel produced by the production method provided by the present invention are shown.
  • the comprehensive mechanical properties such as impact absorption work are excellent, and, as can be seen from the performance data in Table 1, the production method provided by the embodiment 3 of the present invention, and the chemical composition of the steel is carbon 0.50, silicon 0.35, manganese 1.0, Chromium 0.30, aluminum 0.018, nickel 0.20, phosphorus 0.010, balance iron, this example has the best overall mechanical properties, ie, the overall mechanical properties of Example 12 are the best.
  • This embodiment provides a versatile non-quenched and tempered steel production method, which begins with a smelting step including an electric furnace smelting step, a ladle furnace smelting step, and a refining step.
  • a smelting step including an electric furnace smelting step, a ladle furnace smelting step, and a refining step.
  • the electric furnace smelting step the whole iron smelting is adopted, the phosphorus content before tapping is strictly controlled ⁇ 0.015%, the end carbon content is 0.03% ⁇ 0.10%, and the end temperature is 1620°C ⁇ 1700°C.
  • the electric furnace smelting can be more than the traditional converter smelting. Good control of slag operation.
  • the ladle furnace (LF furnace) smelting step silicon carbide and ferrosilicon powder are used for deoxidation, and lime is added to make white slag.
  • the white slag is kept for not less than 20 minutes, so that the white slag can completely remove the inclusions.
  • Smelting step in refining furnace VD furnace
  • degassing is performed to ensure that the hydrogen content is controlled below 1.5 ppm, and the refining time is not less than 45 minutes.
  • the continuous casting step is carried out after the refining step.
  • the molten iron in the tundish is introduced into the crystallizer through the intrusive nozzle, which avoids the problem of easy introduction of air when introduced through the conventional nozzle, and argon gas is blown at the joint portion of the immersion nozzle and the tundish.
  • the superheat is strictly controlled at 20 ⁇ 35 °C, and the pulling speed is controlled at 0.5m/min ⁇ 0.6m/min.
  • the low superheat and continuous drawing speed of continuous casting ensure the quality of the casting blank.
  • the temperature at which the cut is made during continuous casting is controlled to be ⁇ 820.
  • the preheating section is 850 ⁇ 30.
  • the soaking section is 1130 ⁇ 30 °C, and the total time of the soaking section is not less than 2 hours.
  • a finishing rolling step and a cooling step are performed after the heating step; in the finishing rolling step, the temperature at which the rod is controlled to enter the finishing rolling step is ⁇ 950.
  • C, at bar temperature is 850.
  • the water flow rate is controlled by controlling the degree of opening of the valve of the water-passing cooling device, thereby controlling the cooling strength.
  • the opening degree of the first-stage valve is 30% to 40%
  • the second stage The valve opening is 20%
  • the third valve opening is 30% ⁇ 40%, which can reduce the surface temperature of the bar by 100% within 5s.
  • C ⁇ 400 °C after the bar is returned to temperature, the temperature of the bar is lowered by 50 °C ⁇ 100 °C by spray cooling. The heat is quickly dissipated, and then the bar is dispersed and placed on a cold bed to be cooled by air cooling for 10-12 minutes, and finally the lower bed is cooled by stacking the bar.
  • the rod is subjected to three-stage water-cooling, wherein the first stage of water-cooling adopts strong cooling, the second stage of water-cooling adopts weak cooling, and the third section adopts water-cooling. Strong cold.
  • the bar temperature is higher, and the first section is cooled by water, so that the surface temperature of the bar is rapidly lowered. Due to the heat transfer, the core heat is gradually turned to the surface after the surface temperature is lowered.
  • the weak cooling method in order to transfer the heat of the core to the surface as much as possible, the weak cooling method is adopted in the second stage of water-cooling, so that more time is reserved for heat transfer to the core during the cooling process, after weak cooling, The heat transfer causes the surface temperature to rise, and the surface is quickly cooled by the strong cooling method, so that the surface heat is quickly taken away. At this time, the heat transfer causes the surface temperature and the core temperature to converge, thereby ensuring the mechanical properties. Uniformity.

Abstract

一种非调质钢及其生产工艺。该工艺改变以往非调质钢生产中在精轧之前进行冷却的方式，至少在精轧步骤后设置冷却步骤，并且冷却方式一改现有技术中采用单一水冷或者空冷且强弱一致的冷却方式，将强冷和弱冷交替进行，强冷可以保证钢材表面温度迅速减低，弱冷可以使得钢材芯部的温度逐渐扩散到表面，随后再进行强冷，使得热量快速散出，根据实际需要，强冷和弱冷可以交替进行多次，强弱冷相结合的穿水冷却方式使得在较短的时间内钢材芯部的温度和表面的温度即趋于一致，从而确保了钢材力学性能的均匀性。

Description

一种非调质钢及其生产工艺 技术领域
本发明涉及一种非调质钢及其生产工艺， 属于钢铁冶金技术 领域。
背景技术
目前， 国内机械加工行业切削用棒材多数使用 45、 40Cr及 42CrMo 等普通钢， 这些棒材在作为机加工切削用原料时需进行 调质热处理， 调质成本高， 而且由于调质过程会增加能耗并污染 环境， 同时还有一些废品损耗， 不符合现今的节能环保要求。 因 此， 不需要调质处理的可直接切削用非调质钢必将逐步替代普通 钢， 成为未来发展趋势。 非调质钢是指不经过调质处理就可以达 到性能要求的机械结构钢， 采用此类钢制造零件， 可省去调质热 处理工序， 具有节省能源、 材料、 工艺简单等优点， 可以减少环 境污染、 避免氧化、 脱碳、 变形、 开裂。
国内生产易切削非调质钢传统工艺为：电炉冶炼~精炼 ~模 铸~控轧控冷。 该种工艺在生产中的难点为： 钢材性能的控制。 现有国内外生产厂家大多通过改善非调质钢的化学成分来达到对 钢材性能的控制， 然而， 研究证明， 单纯通过成分设计很难使得 非调质钢达到性能上的要求。
为此， 首钢总公司提出了一种新的非调质钢的生产工艺， 主 要包括： 转炉冶炼、 挡渣出钢、 钢包脱氧合金化、 LF钢包精炼、 喂 S线、 钢包底吹氩以实现全保护浇铸、 铸坯控温、 控冷以及轧 制等步骤， 其中， 在轧制步骤中， 加热温度 1100 ~ 1180。C， 开轧 温度 1020 ~ 1100。C， 终轧温度 850 ~ 920。C， 相对变形量为 15 ~ 35%, 轧后冷却到 600。C后緩慢冷却到室温。 上述工艺生产的非 调质钢， 通过緩慢冷却方式在短时间内很难保证钢材芯部和表面 的温度趋于一致， 很容易导致钢材表面和芯部的强度、 韧性波动 很大， 力学性能严重不均匀， 采用上述工艺生产大尺寸非调质钢 时 （例如 φ70 ~ φ145ππη棒材） ， 棒材表面和棒材芯部力学性能 不均匀的现象更加明显。
发明内容
因此， 本发明要解决的技术问题在于克服现有非调质钢生产 工艺生产出的钢材的表面力学性能和芯部力性能不均匀的缺陷， 从而提供一种非调质钢以及其生产工艺， 确保成品的表面力学性 能和芯部力学性能的均匀性。
为此， 本发明提供一种非调质钢， 其由重量百分比如下的化 学成分组成： 碳 0.42 ~ 0.50，硅 0.20 ~ 0.40，锰 0.50 ~ 1.0，铬 0.00 ~ 0.30，招 0.010 ~ 0.030,镍 0.00 ~ 0.10,铜 0.00 ~ 0.20,磚 0.000 ~ 0.025, 硫 0.00 ~ 0.025，以及余量为铁。
在优选实施方案中， 本发明的非调制钢由重量百分比如下的 化学成分组成：碳 0.42 ~ 0.45，娃 0.20 ~ 0.30，樣 0.50 ~ 0.7，铬 0.00 ~ 0.30 0.010 ~ 0.030,镍 0.00 ~ 0.10,铜 0.00 ~ 0.20,磚 0.000 ~ 0.025, 硫 0.00 ~ 0.025，以及余量为铁。
在更优选的实施方案中， 本发明的非调制钢由重量百分比如 下的化学成分组成： 碳 0.42 ~ 0.47，硅 0.25 ~ 0.35，锰 0.60 ~ 1.0，铬 0.00 ~ 0.30，铝 0.010 ~ 0.030,镍 0.00 ~ 0.10,铜 0.00 ~ 0.20,磚 0.000 ~ 0.025，硫 0.00 ~ 0.025，以及余量为铁。
在更加优选的实施方案中， 本发明的非调制钢由重量百分比 如下的化学成分组成： 碳 0.45 ~ 0.50，硅 0.25 ~ 0.35，锰 0.60 - 0.9, 铬 0.00 - 0.30 0.010 ~ 0.030,镍 0.00 ~ 0.10,铜 0.00 ~ 0.20,磚 0.000 - 0.015，硫 0.00 - 0.015，以及余量为铁。
本发明提供一种非调质钢的生产工艺， 包括至少在精轧步骤 后进行的冷却步骤， 在所述冷却步骤中， 采用强弱冷却交替的方 式使所述钢材至少经过两段穿水冷却， 以使得在特定时间内钢材 的芯部温度与表面温度趋于一致。
在本发明提供的非调质钢的生产工艺中，在所述冷却步骤中， 使所述钢材经过三段穿水冷却，其中，第一段穿水冷却采用强冷， 第二段穿水冷却采用弱冷， 第三段穿水冷却采用强冷。
在本发明提供的非调质钢的生产工艺中，在所述冷却步骤中， 通过控制穿水冷却装置的阀门开启程度控制冷却的强弱。
在本发明提供的非调质钢的生产工艺中，在所述冷却步骤中， 所述钢材经过穿水冷却后， 在 4 ~ 7秒内降低 100。C ~ 400。C， 待 钢材回温后再次降温 50。C ~ 100。C。
在本发明提供的非调质钢的生产工艺中，在所述冷却步骤中， 控制第一段阀门开度为 30% ~ 40%， 第二段阀门开度为 20%， 第 三段阀门开度为 30% ~ 40%， 以确保在 4 ~ 7秒使所述钢材表面 温度降低 100°C - 400。C。
在本发明提供的非调质钢的生产工艺中，在所述冷却步骤中， 待钢材回温后采用喷雾冷却的方式对所述钢材进行降温冷却。
在本发明提供的非调质钢的生产工艺中，在所述降温冷却后， 将所述钢材分散放置到冷床上进行 10 ~ 12分钟的空冷。
在本发明提供的非调质钢的生产工艺中， 在所述空冷后， 将 所述钢材叠放后进行革冷。
在本发明提供的非调质钢的生产工艺中， 还包括位于冷却步 骤前的精轧步骤， 在所述精轧步骤中， 控制所述钢材进入精轧步 骤时的温度≤950。C， 在钢材温度处于 850。C ~ 900。C条件下进行低 温轧制。
在本发明提供的非调质钢的生产工艺中， 还包括位于精轧步 骤之前的冶炼步骤，所述冶炼步骤包括依次进行的电炉冶炼步骤、 钢包炉冶炼步骤以及精炼步骤。 在本发明提供的非调质钢的生产工艺中， 在所述电炉冶炼中 采用全铁水冶炼， 终点磷含量≤0.015%， 终点碳含量 0.03% ~ 0.10% , 终点温度 1620。C ~ 1700。C。
在本发明提供的非调质钢的生产工艺中， 在所述钢包炉冶炼 步骤和 /或所述精炼步骤中采用碳化硅、 硅铁粉脱氧。
在本发明提供的非调质钢的生产工艺中， 在所述钢包炉冶炼 步骤中， 造白渣， 并使得白渣保持时间不少于 20分钟。
在本发明提供的非调质钢的生产工艺中， 在精炼步骤中， 确 保精炼时间不少于 45分钟， 将含氢量控制在 1.5ppm以下。
本发明提供的非调质钢的生产工艺， 还包括位于所述精炼步 骤之后的连铸步骤，在所述连铸步骤中，过热度控制在 20 ~ 35°C , 拉速控制在 0.5m/min - 0.6m/ mm。
本发明提供的非调质钢的生产工艺， 还包括连铸步骤之后的 加热步骤， 在所述加热步骤中， 将钢坯放入加热炉中进行加热， 其中，预热段温度控制在 850±30。C，加热段温度控制在 1100±30。C， 均热段温度控制在 1130±30°C， 均热段总时间不少于 2小时。
在一种优选实施方案中， 本发明提供一种非调质钢的生产工 艺， 该工艺依次包括如下步骤：
( 1 ) 电炉冶炼步骤： 提供具有期望的钢组成的铁原料，在所 述电炉冶炼中采用全铁水冶炼， 终点磷含量≤0.015%， 终点碳含 量 0.03% ~ 0.10% , 终点温度 1620°C ~ 1700 °C ;
( 2 )钢包炉冶炼步骤： 其中采用碳化硅和 /或硅铁粉脱氧， 并加入石灰造白渣， 并使得白渣保持时间不少于 20分钟；
( 3 )精炼步骤， 其中进行脱气处理， 确保精炼时间不少于 45分钟， 从而将含氢量控制在 1.5ppm以下；
( 4 )连铸步骤： 对精炼步骤得到的钢熔体进行连铸， 钢熔体 的过热度控制在 20 ~ 35 °C， 拉速控制在 0.5m/min ~ 0.6m/ min; ( 5 )加热步骤：将连铸步骤产生的钢坯放入加热炉中进行加 热， 其中， 预热段温度控制在 850±30。C， 加热段温度控制在 1100±30°C , 均热段温度控制在 1130±30°C， 均热段总时间不少于 2小时；
( 6 )精轧步骤： 其中控制所述钢材进入精轧步骤时的温度 <950°C , 在钢材温度处于 850。C ~ 900。C条件下进行低温轧制； 和
( 7 )冷却步骤：其中采用强弱冷却交替的方式使所述钢材至 少经过两段穿水冷却， 以使得在冷却过程中芯部温度与表面温度 趋于一致。
本发明提供的非调质钢具有以下优点：
1.本发明提供的非调质钢的生产工艺， 改变以往非调质钢生 产中在精轧之前进行冷却的方式， 至少在精轧步碌后设置冷却步 骤， 并且冷却方式一改现有技术中采用单一水冷或者空冷且强弱 一致的冷却方式， 将强冷和弱冷交替进行， 强冷可以保证钢材表 面温度迅速减低，弱冷可以使得钢材芯部的温度逐渐扩散到表面， 随后再进行强冷， 使得热量快速散出， 根据实际需要， 强冷和弱 冷可以交替进行多次， 强弱冷相结合的穿水冷却方式使得在较短 的时间内钢材芯部的温度和表面的温度即趋于一致， 从而确保了 钢材力学性能的均匀性， 且提高了生产效率。
2.本发明提供的非调质钢的生产工艺， 在所述冷却步骤中， 使所述钢材经过三段穿水冷却，其中，第一段穿水冷却采用强冷， 第二段穿水冷却采用弱冷， 第三段穿水冷却采用强冷。 精轧之后 的钢材温度较高， 在第一段穿水冷却时采用强冷的方式， 使得钢 材的表面温度迅速降低， 由于热量的传递作用， 表面温度降低之 后， 芯部热量逐渐向表面传递， 为了使得芯部热量尽可能多的传 递到表面， 在第二段穿水冷却中采用弱冷的方式， 弱冷之后， 热 传递使得表面温度有所升高， 再次通过强冷方式快速冷却表面， 从而使得表面热量被迅速带走， 此时， 热传递使得表面温度和芯 部温度趋于一致， 从而确保了力学性能的均匀性。
3.本发明提供的非调质钢的生产工艺， 在所述冷却步骤中， 通过控制穿水冷却装置的阀门开启程度控制冷却的强弱，具体地， 控制第一段阀门开度为 30% ~ 40%， 第二段阀门开度为 20%， 第 三段阀门开度为 30% ~ 40%， 以确保在 4 ~ 7秒使所述钢材表面 温度降低 100°C ~ 400°C , 通过控制阀门开启程度可以控制水流量， 进而控制穿水冷却的强弱程度， 该种控制方式非常简便， 在阀门 开启一定长度后， 将钢材穿入水中进行穿水处理， 钢材在穿水过 程中， 其表面被全方位冷却， 确保了表面冷却的均匀性。
4.本发明提供的非调质钢的生产工艺， 在所述冷却步骤中， 待钢材回温后采用喷雾冷却的方式对所述钢材进行降温冷却。 喷 雾冷却的方式是对穿水冷却的有利补充， 通过喷雾冷却可以使得 芯部的热量进一步扩散到表面， 更加确保了芯部与表面温度的一 致性。
5.本发明提供的非调质钢的生产工艺， 在所述降温冷却后， 将所述钢材分散放置到冷床上进行 10 ~ 12分钟的空冷。在喷雾冷 却后， 将钢材分散放置到冷床上进行空冷， 可以进一步补充喷雾 冷却， 使得表面热量进一步散失。
6.本发明提供的非调质钢的生产工艺， 在所述空冷后， 将所 述钢材叠放后进行革冷。 革冷是緩慢冷却的一种方式， 为了避免 上述冷却过程过快而对钢材组织性能造成的不利影响， 将所述钢 材叠放后进行革冷， 在经过穿水冷却、 喷雾冷却以及空冷等冷却 方式后， 钢材表面温度与芯部温度已经基本上达到一致， 此时， 采用革冷的方式， 将冷却速度降下来， 有利于改善钢材的组织性 能。
7.本发明提供的非调质钢的生产工艺， 在所述钢包炉冶炼步 骤中， 造白渣， 并使得白渣保持时间不少于 20分钟，严格控制白 渣保持时间， 使得白渣的脱氧、 脱硫以及去除夹杂物的作用更加 明显， 有利于提高钢的纯净度。
8.本发明提供的非调质钢的生产工艺， 在精炼步骤中， 确保 精炼时间不少于 45分钟， 将含氢量控制在 1.5ppm以下， 该精炼 工艺有效的控制了氢含量， 可以更好的解决后续钢材氢致裂纹的 风险； 有更充分的时间使得成分更均 ； 给予夹杂物更充分的上 浮时间， 有效的解决夹杂物控制的问题， 使得成品更加纯净。
9.本发明提供的非调质钢的生产工艺， 连铸步骤中， 过热度 严格控制在 20 ~ 35。C， 拉速控制在 0.5m/min ~ 0.6m/ min, 连铸 的低过热度、 低拉速保证了铸坯的质量。
10.本发明提供的非调质钢，放大 500倍下的金相组织为铁素 体和珠光体， 实际晶粒度（100倍） ， 按 GB/T6394评级为 10 ~ 11级， 晶粒细小， 均匀， 从芯部到边缘级差不大于 1.5级， 钢材 表面和芯部的力学性能均匀， 由芯部到边缘的强度、 韧性波动很 小， 可以有效避免一般材料在表面加工量较大后， 力学性能达不 到使用要求的缺点， 由芯部到边缘硬度差小于 30HB, 可以有效 的避免硬度变化大时对刀具、 加工产生的不利影响， 并且夹杂物 含量低， 纯净度较高。
本发明的核心在于通过控制轧制和控制轧制后的冷却步碌使 得钢材表面和芯部的性能大体一致， 从而提高了钢材的品质。 具 体的冷却控制包括：
1 )在精轧之后采用强弱冷却交替的方式使所述钢材至少经过 两段穿水冷却， 以使得在特定时间内钢材的芯部温度与表面温度 趋于一致， 具体地， 在精轧之后使所述钢材经过三段穿水冷却， 其中， 第一段穿水冷却采用强冷， 第二段穿水冷却采用弱冷， 第 三段穿水冷却采用强冷， 在具体的穿水冷却中， 通过控制穿水冷 却装置的阀门开启程度控制冷却的强弱。 在本发明中， 所述强冷 通常指冷却速度≥7eC/S 的冷却； 而所述弱冷是指冷却速度为 2-4°C/S的冷却。
2 )穿水冷却后， 待钢材回温后采用喷雾冷却的方式对所述钢 材进行降温冷却；
3 )在所述降温冷却后， 将所述钢材分散放置到冷床上进行 10 ~ 12分钟的空冷；
4 )在所述空冷后， 将所述钢材叠放后进行革冷。
在精轧之后通过上述方式（尤其是穿水冷却）进行冷却控制， 改变以往非调质钢生产中在精轧之前进行冷却的方式， 至少在精 轧步骤后设置冷却步骤， 并且冷却方式一改现有技术中采用单一 水冷或者空冷且强弱一致的冷却方式， 将强冷和弱冷交替进行， 强冷可以保证钢材表面温度迅速减低， 弱冷可以使得钢材芯部的 温度逐渐扩散到表面， 随后再进行强冷， 使得热量快速散出， 根 据实际需要， 强冷和弱冷可以交替进行多次， 强弱冷相结合的穿 水冷却方式使得在较短的时间内钢材芯部的温度和表面的温度即 趋于一致， 从而确保了钢材力学性能的均匀性， 且提高了生产效 率。 在此基础之上， 后续的喷雾冷却、 空冷以及革冷方式的联合 控制，使得芯部温度不断的散向表面，而表面温度不断的被带走， 并且， 上述冷却方式的结合使得冷却速度比较适宜， 在空冷之后 采用革冷， 使得钢材表面温度与芯部温度一致的情况下， 冷却速 度不至于过快， 提高了综合力学性能。
附图说明
为了使本发明的内容更容易被清楚的理解， 下面根据本发明 的具体实施例并结合附图， 对本发明作进一步详细的说明， 其中 图 1是采用本发明的生产方法生产的非调质钢在放大 500倍 下的金相图片； 图 2是反映采用本发明的生产方法生产的非调质钢的晶粒度 的图片；
图 3是反映采用本发明的生产方法生产的非调质钢的夹杂物 情况的图片。
具体实施方式
实施例 1
本实施例提供一种非调质钢的生产方法， 包括精轧步骤以及 在精轧之后的冷却步骤， 其中， 在所述精轧步骤中， 控制棒材进 入精轧步骤时的温度≤950。C， 在棒材温度处于 850。C ~ 900。C条件 下进行低温轧制； 轧制后通过专业可控的穿水冷却设备对钢材进 行三段穿水冷却， 第一段穿水冷却采用强冷， 第二段穿水冷却采 用弱冷， 第三段穿水冷却采用强冷。
在此， 需要说明的是， 控制穿水冷却强弱的方式有很多， 在 本实施例中， 通过控制穿水冷却装置的阀门开启程度来控制水流 量， 以此来控制冷却强弱的目的， 具体地， 第一段阀门开度为 30% - 40% , 第二段阀门开度为 20%， 第三段阀门开度为 30% ~ 40% ,可确保 5s内降低棒材表面温度 100。C ~ 400 °C，之后待棒材 回温后采用喷雾冷却的方式将棒材温度降低 50°C ~ 100°C， 使其 热量快速散出， 然后将棒材分散开来放置到冷床上采用空冷方式 冷却 10-12分钟， 最后下冷床将棒材叠加革冷。
本实施例的代替普通调质 45 钢直接切削用非调质钢的生产 方法， 使所述棒材经过三段穿水冷却， 其中， 第一段穿水冷却采 用强冷， 第二段穿水冷却采用弱冷， 第三段穿水冷却采用强冷。 精轧之后的棒材温度较高，在第一段穿水冷却时采用强冷的方式， 使得棒材的表面温度迅速降低， 由于热量的传递作用， 表面温度 降低之后， 芯部热量逐渐向表面传递， 为了使得芯部热量尽可能 多的传递到表面， 在第二段穿水冷却中采用弱冷方式， 以使得冷 却过程中预留较多的时间给芯部进行热传递， 弱冷之后， 热传递 使得表面温度有所升高， 再次通过强冷方式快速冷却表面， 从而 使得表面热量被迅速带走， 此时， 热传递使得表面温度和芯部温 度趋于一致， 从而确保了力学性能的均匀性。
实施例 2
本实施例提供一种非调质钢的生产方法， 其是在实施例 1基 础之上的进一步改进， 相对于实施例 1来说， 还包括位于精轧步 骤之前的冶炼步骤，所述冶炼步骤包括依次进行的电炉冶炼步骤、 钢包炉冶炼步骤以及精炼步骤。
在电炉冶炼步骤中， 采用全铁水冶炼， 严格控制出钢前磷含 量≤0.015%， 终点碳含量 0.03% ~ 0.10%， 终点温度 1620°C - 1700°C , 电炉冶炼较传统的转炉冶炼可以更好的控制下渣操作。
在钢包炉 （LF炉） 冶炼步骤中， 使用碳化硅、 硅铁粉脱氧， 加入石灰造白渣， 白渣保持时间不少于 20分钟， 以使得白渣能够 较为彻底的清除夹杂物。
在精炼炉 （VD 炉） 冶炼步骤中， 进行脱气处理， 确保含氢 量控制在 1.5ppm以下， 确保精炼时间不少于 45分钟。
用 LF炉 +VD炉精炼的优点： 相对于传统的仅用 LF炉精炼 来说， 该精炼工艺有效的控制了氢含量， 可以更好的解决后续棒 材氢至裂纹的风险； 有更充分的时间使得成分更均 ； 给予夹杂 物有更充分的上浮时间， 有效的解决夹杂物控制的问题。
实施例 3
本实施例提供一种非调质钢的生产方法， 其是在实施例 2基 础上的进一步改进， 在本实施例中， 对连铸步骤以及加热步骤进 行改进， 连铸步骤和加热步骤均位于精炼步骤之后， 而又位于轧 制步骤和穿水冷却步碌之前。
连铸步骤中，通过侵入式水口将中间包中的铁水引入结晶器， 避免了通过传统水口引入时易于引入空气的问题， 另外， 在浸入 式水口与中间包的结合部位吹氩气， 以避免空气进入中间包， 过 热度严格控制在 20 ~ 35 °C，拉速控制在 0.5m/min ~ 0.6m/min,连 铸的低过热度、 低拉速保证了铸坯的质量。 连铸后切割时据切处 的温度控制在≤820。C， 切割后， 需人工检查铸坯表面， 确保无明 显缺陷， 取铸坯低倍样， 确保铸坯无裂纹， 无缩孔， 中心疏松不 大于 3级， 该要求是为了保证后续轧制出的棒材表面与低倍的质 量， 铸坯检查合格后， 送往加热炉进行加热， 预热段 850±30°C , 加热段 1100±30。C，均热段 1130±30。C，确保均热段总时间不少于 2小时。
实施例 4
本实施例提供一种采用上述实施例所述的生产方法生产的非 调质钢， 其由重量百分比如下的化学成分组成： 碳 0.42，硅 0.20， 锰 0.50，铬 0.30 ，铝 0.010，镍 0.10，铜 0.20，磷 0.010，硫 0.015，余量为 铁。
实施例 5
本实施例提供一种采用上述实施例 1所述的生产方法生产的 非调质钢，其由重量百分比如下的化学成分组成：碳 0.50，硅 0.35， 锰 1.0，铬 0.30，铝 0.030，镍 0.10，铜 0.20，磷 0.015，硫 0.020，余量为铁。 实施例 6
本实施例提供一种采用上述实施例 1所述的生产方法生产的 非调质钢，其由重量百分比如下的化学成分组成：碳 0.45，硅 0.30， 锰 0.70，铬 0.20 ，铝 0.020，镍 0.05，铜 0.10，磷 0.010，硫 0.025，以及余 量为铁。
实施例 7
本实施例提供一种采用上述实施例 2所述的生产方法生产的 非调质钢，其由重量百分比如下的化学成分组成：碳 0.47，硅 0.25， 锰 0.60，铬 0.30 ，铝 0.010，镍 0.10，铜 0.20，磷 0.010，硫 0.010，以及余 量为铁。
实施例 8
本实施例提供一种采用上述实施例 2所述的生产方法生产的 非调质钢，其由重量百分比如下的化学成分组成：碳 0.48，硅 0.28， 锰 0.8，铬 0.30，铝 0.025，镍 0.08，铜 0.10，磷 0.010，硫 0.015，以及余量 为铁。
实施例 9
本实施例提供一种采用上述实施例 2所述的生产方法生产的 非调质钢，其由重量百分比如下的化学成分组成：碳 0.43，硅 0.30， 锰 0. 55，铬 0.25，铝 0.020，镍 0.10，铜 0.20，硫 0.012，以及余量为铁。 实施例 10
本实施例提供一种采用上述实施例 3所述的生产方法生产的 非调质钢，其由重量百分比如下的化学成分组成：碳 0.49，硅 0.32， 锰 0.92，铬 0.25，铝 0.018， 镍 0.20，磷 0.025，以及余量为铁。
实施例 11
本实施例提供一种采用上述实施例 3所述的生产方法生产的 非调质钢，其由重量百分比如下的化学成分组成：碳 0.48，硅 0.29， 锰 0.70，铬 0.30，铝 0.028，镍 0.15，磷 0.010，以及余量为铁。
实施例 12
本实施例提供一种采用上述实施例 3所述的生产方法生产的 非调质钢，其由重量百分比如下的化学成分组成：碳 0.50，硅 0.40， 锰 1. 0，铬 0.30，铝 0.018， 镍 0.20，磷 0.010，以及余量为铁。
实施例 13
本实施例提供一种采用上述实施例 3所述的生产方法生产的 非调质钢，其由重量百分比如下的化学成分组成：碳 0.48，硅 0.30， 锰 0.60， 铬 0.30， 铝 0.015，磷 0.010，硫 0.010， 以及余量为铁。 实施例 14
本实施例提供一种采用上述实施例 3所述的生产方法生产的 非调质钢，其由重量百分比如下的化学成分组成：碳 0.49，硅 0.28， 锰 0.75， 铝 0.018， 镍 0.10， 磷 0.010，以及余量为铁。
实施例 15
本实施例提供一种采用上述实施例 3所述的生产方法生产的 非调质钢，其由重量百分比如下的化学成分组成：碳 0.47，硅 0.28， 锰 0.75， 铝 0.018， 镍 0.10， 硫 0.010， 磷 0.010，以及余量为铁。
上述实施例 4-15的非调质钢芯部放大 500倍下的金相组织为 都为铁素体和珠光体（如图 1所示） ， 实际晶粒度（100倍） ， 按 GB/T6394评级为 10 ~ 11级（如图 2所示），晶粒细小，均匀， 从芯部到边缘级差都不大于 1.5级， 钢材表面和芯部的力学性能 均匀， 由芯部到边缘的强度、 韧性波动很小， 可以有效避免一般 材料在表面加工量较大后， 力学性能达不到使用要求的缺点， 由 芯部到边缘硬度差小于 30HB, 可以有效的避免硬度变化大时对 刀具、加工产生的不利影响，并且夹杂物含量低， 纯净度较高（如 图 3所示） 。
上述实施例 4-15的力学性能数据见下表 1， 从表 1中可以看 出， 采用本发明提供的生产方法生产的非调质钢在屈服强度、 抗 拉强度、 延伸率、 面缩率、 冲击吸收功等综合力学性能优良， 并 且， 从表 1中的性能数据可以看出， 采用本发明的实施例 3提供 的生产方法， 且钢的化学组成为碳 0.50，硅 0.35，锰 1.0，铬 0.30，铝 0.018， 镍 0.20，磷 0.010，余量为铁，这一实施例的综合力学性能最 好， 即实施例 12的综合力学性能最好。
从下表性能数据可以看出， 本发明提供的采用上述方法生产 的非调质钢，完全可以替代普通调质 45钢进行直接切削加工，并 且， 在综合力学性能上更加优良。 表 1 实施例 4-15的力学性能数据
Figure imgf000016_0001
实施例 16
本实施例提供一种通用性的非调质钢生产方法， 该方法以冶 炼步骤开始， 所述冶炼步骤包括依次进行的电炉冶炼步骤、 钢包 炉冶炼步骤以及精炼步骤。在电炉冶炼步骤中，采用全铁水冶炼， 严格控制出钢前磷含量≤0.015%，终点碳含量 0.03% ~ 0.10%，终 点温度 1620°C ~ 1700°C， 电炉冶炼较传统的转炉冶炼可以更好的 控制下渣操作。 在钢包炉（LF炉）冶炼步骤中， 使用碳化硅、 硅 铁粉脱氧， 加入石灰造白渣， 白渣保持时间不少于 20分钟， 以使 得白渣能够较为彻底的清除夹杂物。 在精炼炉 （VD 炉） 冶炼步 骤中， 进行脱气处理， 确保含氢量控制在 1.5ppm 以下， 确保精 炼时间不少于 45分钟。
用 LF炉 +VD炉精炼的优点： 相对于传统的仅用 LF炉精炼 来说， 该精炼工艺有效的控制了氢含量， 可以更好的解决后续棒 材氢至裂纹的风险； 有更充分的时间使得成分更均 ； 给予夹杂 物有更充分的上浮时间， 有效的解决夹杂物控制的问题。
在精炼步骤之后进行连铸步骤。 在所述连铸步骤中， 通过侵 入式水口将中间包中的铁水引入结晶器， 避免了通过传统水口引 入时易于引入空气的问题， 另外， 在浸入式水口与中间包的结合 部位吹氩气， 以避免空气进入中间包， 过热度严格控制在 20 ~ 35°C , 拉速控制在 0.5m/min ~ 0.6m/min， 连铸的低过热度、 低拉 速保证了铸坯的质量。连铸后切割时据切处的温度控制在≤820。C， 切割后，需人工检查铸坯表面，确保无明显缺陷，取铸坯低倍样， 确保铸坯无裂纹， 无缩孔， 中心疏松不大于 3级， 该要求是为了 保证后续轧制出的棒材表面与低倍的质量， 铸坯检查合格后， 送 往加热炉进行加热步骤，其中预热段 850±30。C，加热段 1100±30。C， 均热段 1130±30 °C， 确保均热段总时间不少于 2小时。
在加热步骤之后进行精轧步骤和冷却步骤； 在所述精轧步骤 中， 控制棒材进入精轧步骤时的温度≤950。C， 在棒材温度处于 850。C ~ 900。C条件下进行低温轧制； 轧制后通过专业可控的穿水 冷却设备对钢材进行三段穿水冷却， 第一段穿水冷却采用强冷， 第二段穿水冷却采用弱冷， 第三段穿水冷却采用强冷。
在本实施例中， 通过控制穿水冷却装置的阀门开启程度来控 制水流量， 以此来控制冷却强弱的目的， 具体地， 第一段阀门开 度为 30% ~ 40%， 第二段阀门开度为 20%， 第三段阀门开度为 30% ~ 40%,可确保 5s内降低棒材表面温度 100。C ~ 400 °C，之后 待棒材回温后采用喷雾冷却的方式将棒材温度降低 50°C ~ 100°C， 使其热量快速散出， 然后将棒材分散开来放置到冷床上采用空冷 方式冷却 10-12分钟， 最后下冷床将棒材叠加革冷。
在本实施例的生产方法中， 使所述棒材经过三段穿水冷却， 其中， 第一段穿水冷却采用强冷， 第二段穿水冷却采用弱冷， 第 三段穿水冷却采用强冷。 精轧之后的棒材温度较高， 在第一段穿 水冷却时采用强冷的方式， 使得棒材的表面温度迅速降低， 由于 热量的传递作用，表面温度降低之后，芯部热量逐渐向表面传递， 为了使得芯部热量尽可能多的传递到表面， 在第二段穿水冷却中 采用弱冷方式， 以使得冷却过程中预留较多的时间给芯部进行热 传递， 弱冷之后， 热传递使得表面温度有所升高， 再次通过强冷 方式快速冷却表面， 从而使得表面热量被迅速带走， 此时， 热传 递使得表面温度和芯部温度趋于一致， 从而确保了力学性能的均 匀性。
显然， 上述实施例仅是为清楚地说明所作的举例， 而并非对 实施方式的限定。 对于所属领域的普通技术人员来说， 在上述说 明的^？上还可以做出其它不同形式的变化或变动。 这里无需也 无法对所有的实施方式予以穷举。 而由此所引伸出的显而易见的 变化或变动仍处于本发明创造的保护范围之中。

Claims

1. 一种非调质钢， 其包括重量百分比如下的化学成分： 碳 0.42 ~ 0.50,娃 0.20 ~ 0.40,樣 0.50 ~ 1.0,铬 0.00 - 0.30 ，铝 0.010 ~ 0.030,镍 0.00 ~ 0.10,铜 0.00 ~ 0.20,磚 0.000 ~ 0.025,疏 0.00 ~ 0.025, 余量为铁。
2. 根据权利要求 1所述的非调质钢， 其包括重量百分比如下 的化学成分： 碳 0.42 ~ 0.45，娃 0.20 ~ 0.30，樣 0.50 ~ 0.7，铬 0.00 ~ 0.30 0.010 ~ 0.030,镍 0.00 ~ 0.10,铜 0.00 ~ 0.20,磚 0.000 ~ 0.025, 硫 0.00 ~ 0.025，余量为铁。
3. 根据权利要求 1所述的非调质钢， 其包括重量百分比如下 的化学成分： 碳 0.42 ~ 0.47，娃 0.25 ~ 0.35，樣 0.60 ~ 1.0，铬 0.00 ~ 0.30 0.010 ~ 0.030,镍 0.00 ~ 0.10,铜 0.00 ~ 0.20,磚 0.000 ~ 0.025, 硫 0.00 ~ 0.025，余量为铁。
4. 根据权利要求 1所述的非调质钢， 其包括重量百分比如下 的化学成分： 碳 0.45 ~ 0.50，娃 0.25 ~ 0.35，樣 0.60 ~ 0.9，铬 0.00 ~ 0.30 0.010 ~ 0.030,镍 0.00 ~ 0.10,铜 0.00 ~ 0.20,磚 0.000 ~ 0.015, 硫 0.00 ~ 0.015，余量为铁。
5. 一种生产权利要求 1-4 中任一项所述的非调质钢的生产工 艺， 包括至少在精轧步碌后进行的冷却步骤， 其特征在于： 在所 述冷却步骤中， 采用强弱冷却交替的方式使所述钢材至少经过两 段穿水冷却， 以使得在特定时间内钢材的芯部温度与表面温度趋 于一致。
6. 根据权利要求 5所述的非调质钢的生产工艺，其特征在于： 在所述冷却步骤中， 使所述钢材经过三段穿水冷却， 其中， 第一 段穿水冷却采用强冷， 第二段穿水冷却采用弱冷， 第三段穿水冷 却采用强冷。
7. 根据权利要求 5或 6所述的非调质钢的生产工艺， 其特征 在于： 在所述冷却步骤中， 通过控制穿水冷却装置的阀门开启程 度控制冷却的强弱。
8. 根据权利要求 5 ~ 7中任一项所述的非调质钢的生产工艺， 其特征在于： 在所述冷却步骤中， 所述钢材经过穿水冷却后， 在 4 - 7 秒内降低 100。C ~ 400。C， 待钢材回温后再次降温 50。C ~
100。c。
9. 根据权利要求 8所述的非调质钢的生产工艺，其特征在于： 在所述冷却步骤中， 控制第一段阀门开度为 30% ~ 40%， 第二段 阀门开度为 20%， 第三段阀门开度为 30% ~ 40%， 以确保在 4 ~ 7秒使所述钢材表面温度降低 100。C ~ 400。C。
10. 根据权利要求 8或 9所述的非调质钢的生产工艺， 其特征 在于： 在所述冷却步骤中， 待钢材回温后采用喷雾冷却的方式对 所述钢材进行降温冷却。
11. 根据权利要求 8 ~ 10中任一项所述的非调质钢的生产工艺， 其特征在于： 在所述降温冷却后， 将所述钢材分散放置到冷床上 进行 10 ~ 12分钟的空冷。
12. 根据权利要求 11所述的非调质钢的生产工艺，其特征在于: 在所述空冷后， 将所述钢材叠放后进行革冷。
13. 根据权利要求 5 ~ 12中任一项所述的非调质钢的生产工艺， 其特征在于： 还包括位于冷却步骤前的精轧步骤， 在所述精轧步 骤中， 控制所述钢材进入精轧步骤时的温度≤950。0：， 在钢材温度 处于 850°C ~ 900°C条件下进行低温轧制。
14. 根据权利要求 5 ~ 13中任一项所述的非调质钢的生产工艺， 其特征在于： 还包括位于精轧步骤之前的冶炼步骤， 所述冶炼步 骤包括依次进行的电炉冶炼步骤、钢包炉冶炼步骤以及精炼步骤。
15. 根据权利要求 14所述的非调质钢的生产工艺，其特征在于: 在所述电炉冶炼中采用全铁水冶炼， 终点磷含量≤0.015%， 终点 碳含量 0.03% ~ 0.10%, 终点温度 1620°C ~ 1700。C。
16. 根据权利要求 14或 15所述的非调质钢的生产工艺， 其特 征在于：在所述钢包炉冶炼步骤和 /或所述精炼步骤中采用碳化硅、 硅铁粉脱氧。
17. 根据权利要求 14 ~ 16中任一项所述的非调质钢的生产工艺， 其特征在于： 在所述钢包炉冶炼步骤中， 造白渣， 并使得白渣保 持时间不少于 20分钟。
18. 根据权利要求 14 ~ 17中任一项所述的非调质钢的生产工艺， 其特征在于： 在精炼步骤中， 确保精炼时间不少于 45分钟， 将含 氢量控制在 1.5ppm以下。
19. 根据权利要求 18所述的非调质钢的生产工艺，其特征在于: 还包括位于所述精炼步骤之后的连铸步骤， 在所述连铸步骤中， 过热度控制在 20 ~ 35 °C， 拉速控制在 0.5m/min ~ 0.6m/ min。
20. 根据权利要求 19所述的非调质钢的生产工艺，其特征在于: 还包括连铸步碌之后的加热步骤， 在所述加热步骤中， 将钢坯放 入加热炉中进行加热， 其中， 预热段温度控制在 850±30。C， 加热 段温度控制在 1100±30。C，均热段温度控制在 1130±30。C，均热段 总时间不少于 2小时。
21. 一种生产非调质钢的工艺， 该工艺依次包括如下步骤：
( 1 ) 电炉冶炼步骤： 提供具有期望的钢组成的铁原料，在所 述电炉冶炼中采用全铁水冶炼， 终点磷含量≤0.015%， 终点碳含 量 0.03% ~ 0.10%, 终点温度 1620°C ~ 1700 °C ;
( 2 )钢包炉冶炼步骤： 其中采用碳化硅和 /或硅铁粉脱氧， 并加入石灰造白渣， 并使得白渣保持时间不少于 20分钟；
( 3 )精炼步骤， 其中进行脱气处理， 确保精炼时间不少于 45分钟， 从而将含氢量控制在 1.5ppm以下； (4)连铸步骤： 对精炼步骤得到的钢熔体进行连铸， 钢熔体 的过热度控制在 20 ~ 35 °C， 拉速控制在 0.5m/min ~ 0.6m/ min;
(5)加热步骤：将连铸步骤产生的钢坯放入加热炉中进行加 热， 其中， 预热段温度控制在 850±30。C， 加热段温度控制在 1100±30°C, 均热段温度控制在 1130±30°C， 均热段总时间不少于 2小时；
(6)精轧步骤： 其中控制所述钢材进入精轧步骤时的温度 <950°C, 在钢材温度处于 850。C~900。C条件下进行低温轧制； 和
(7)冷却步骤：其中采用强弱冷却交替的方式使所述钢材至 少经过两段穿水冷却， 以使得在冷却过程中芯部温度与表面温度 趋于一致。
PCT/CN2013/088377 2013-09-26 2013-12-03 一种非调质钢及其生产工艺 WO2015043057A1 (zh)

Priority Applications (3)

Application Number Priority Date Filing Date Title
EP13894743.7A EP3050991A4 (en) 2013-09-26 2013-12-03 Non-quenched and tempered steel and manufacturing method therefor
US15/023,513 US20160208356A1 (en) 2013-09-26 2013-12-03 Non quenched and tempered steel and manufacturing process thereof
JP2016516510A JP2017502165A (ja) 2013-09-26 2013-12-03 非調質鋼及びその製造方法

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201310443674.4A CN104032224B (zh) 2013-09-26 2013-09-26 一种非调质钢及其生产工艺
CN201310443674.4 2013-09-26

Publications (1)

Publication Number Publication Date
WO2015043057A1 true WO2015043057A1 (zh) 2015-04-02

Family

ID=51463215

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2013/088377 WO2015043057A1 (zh) 2013-09-26 2013-12-03 一种非调质钢及其生产工艺

Country Status (5)

Country Link
US (1) US20160208356A1 (zh)
EP (1) EP3050991A4 (zh)
JP (1) JP2017502165A (zh)
CN (1) CN104032224B (zh)
WO (1) WO2015043057A1 (zh)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113145817A (zh) * 2020-12-24 2021-07-23 山东寿光巨能特钢有限公司 一种控制含锰钢大圆坯表面微裂纹的方法

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105855299B (zh) * 2014-12-22 2019-03-15 苏州苏信特钢有限公司 一种钢的轧制方法及使用该方法获得的钢
CN105568134A (zh) * 2016-01-05 2016-05-11 江阴兴澄特种钢铁有限公司 一种微合金化轿车碳素轮毂轴承用钢及其制造方法
CN110964975B (zh) * 2018-09-28 2021-10-26 苏州苏信特钢有限公司 一种非调质钢及其制备方法和注塑机用拉杆
CN111618264B (zh) * 2020-06-02 2021-08-20 北京科技大学 一种提高铸坯温度均匀性的铸坯冷却方法
CN111549287B (zh) * 2020-06-28 2021-08-03 宝钢特钢韶关有限公司 中碳钢及其生产工艺
CN113634594B (zh) * 2021-07-09 2023-03-21 包头钢铁（集团）有限责任公司 一种汽车车桥管用热轧圆钢的制备方法

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20070098589A1 (en) * 2005-10-26 2007-05-03 Nissan Motor Co., Ltd. Non-heat treated steel for connecting rod and connecting rod formed of same
CN101050504A (zh) * 2007-05-10 2007-10-10 武汉科技大学 一种大线能量焊接非调质高强度钢板及其制造方法
JP4419572B2 (ja) * 2004-01-08 2010-02-24 Ｊｆｅスチール株式会社 疲労特性に優れた複合組織鋼板の製造方法
CN102482753A (zh) * 2009-08-31 2012-05-30 新日本制铁株式会社 高强度热浸镀锌钢板及其制造方法

Family Cites Families (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2287956B (en) * 1994-03-31 1998-02-04 Daewoo Heavy Ind Co Ltd Thermal refiningless hot-rolled steel and method of making same
JP3598868B2 (ja) * 1999-03-09 2004-12-08 住友金属工業株式会社 熱間圧延線材の製造方法
JP3554506B2 (ja) * 1999-05-27 2004-08-18 新日本製鐵株式会社 機械構造用熱間圧延線材・棒鋼の製造方法
EP1905851B1 (en) * 2005-06-29 2015-11-04 JFE Steel Corporation High-carbon hot-rolled steel sheet and process for producing the same
CN100478480C (zh) * 2008-05-27 2009-04-15 机械科学研究总院先进制造技术研究中心 高性能低成本非调质钢
JP5565102B2 (ja) * 2010-05-27 2014-08-06 Ｊｆｅスチール株式会社 機械構造用鋼およびその製造方法
JP5370281B2 (ja) * 2010-06-16 2013-12-18 新日鐵住金株式会社 鍛造クランクシャフト
CN101984091A (zh) * 2010-11-26 2011-03-09 上海交通大学 在线控时控温穿水淬火冷却装置
CN102071368A (zh) * 2011-01-30 2011-05-25 钢铁研究总院 低成本锻造用中碳非调质钢
JP5590246B2 (ja) * 2011-08-26 2014-09-17 新日鐵住金株式会社 非調質機械部品用線材、非調質機械部品用鋼線、及び、非調質機械部品とそれらの製造方法
CN103266287B (zh) * 2013-05-14 2016-03-16 莱芜钢铁集团有限公司 一种中碳铁素体-珠光体型非调质钢及其制造方法

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4419572B2 (ja) * 2004-01-08 2010-02-24 Ｊｆｅスチール株式会社 疲労特性に優れた複合組織鋼板の製造方法
US20070098589A1 (en) * 2005-10-26 2007-05-03 Nissan Motor Co., Ltd. Non-heat treated steel for connecting rod and connecting rod formed of same
CN101050504A (zh) * 2007-05-10 2007-10-10 武汉科技大学 一种大线能量焊接非调质高强度钢板及其制造方法
CN102482753A (zh) * 2009-08-31 2012-05-30 新日本制铁株式会社 高强度热浸镀锌钢板及其制造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP3050991A4 *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113145817A (zh) * 2020-12-24 2021-07-23 山东寿光巨能特钢有限公司 一种控制含锰钢大圆坯表面微裂纹的方法

Also Published As

Publication number Publication date
JP2017502165A (ja) 2017-01-19
EP3050991A4 (en) 2017-04-19
US20160208356A1 (en) 2016-07-21
EP3050991A1 (en) 2016-08-03
CN104032224A (zh) 2014-09-10
CN104032224B (zh) 2015-12-02

Similar Documents

Publication Publication Date Title
WO2015043061A1 (zh) 一种非调质钢及其生产工艺
WO2015043060A1 (zh) 一种非调质钢及其生产工艺
WO2015043059A1 (zh) 一种非调质钢及其生产工艺
WO2015043057A1 (zh) 一种非调质钢及其生产工艺
CN104532126B (zh) 一种低屈强比超高强度热轧q&amp;p钢及其制造方法
CN105525078B (zh) 一种提高4Cr5MoSiV1热作模具钢性能的制备方法
WO2015043058A1 (zh) 一种非调质钢的生产工艺
CN105803299B (zh) 一种特厚高纯净度塑料模具钢板的生产方法
JP7159311B2 (ja) 磁気特性に優れる無方向性電磁鋼板およびその製造方法
CN111349853B (zh) 微合金处理热轧h型钢的轧制方法
CN115055654B (zh) 高碳钢盘条及其生产方法
CN115976415A (zh) 一种特高强度85级帘线钢盘条及其生产方法
JP2022516182A (ja) ６９０ＭＰａグレードの極厚鋼板およびその製造方法
CN104451379A (zh) 一种高强度低合金铌钒结构钢及其制备方法
CN107974615A (zh) 厚度小于12mm的Q460E高强钢板及其生产方法
CN104004957B (zh) 利用氧化物冶金技术生产小压缩比低温用h型钢的方法
CN103614637A (zh) 一种梳理用齿条钢盘条及其生产方法
CN103484764A (zh) Ti析出强化型超高强热轧薄板及其生产方法
CN103602892B (zh) 厚规格钢板的生产方法
CN103160751B (zh) 一种屈服强度为590MPa级球扁钢及其生产方法
CN114908297A (zh) 一种降低疲劳裂纹扩展速率的贝马复相重轨钢及其方法
CN115679222A (zh) 一种制钉用冷镦钢盘条的生产方法
CN115852241A (zh) 一种高均质高淬透性风电螺栓用钢、棒材及其制造方法

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 13894743

Country of ref document: EP

Kind code of ref document: A1

ENP Entry into the national phase

Ref document number: 2016516510

Country of ref document: JP

Kind code of ref document: A

REEP Request for entry into the european phase

Ref document number: 2013894743

Country of ref document: EP

WWE Wipo information: entry into national phase

Ref document number: 15023513

Country of ref document: US

Ref document number: 2013894743

Country of ref document: EP

NENP Non-entry into the national phase

Ref country code: DE