CN111020383A - Large-thickness high-strength wear-resistant steel plate HYNM650 and production method thereof - Google Patents
Large-thickness high-strength wear-resistant steel plate HYNM650 and production method thereof Download PDFInfo
- Publication number
- CN111020383A CN111020383A CN201911269022.7A CN201911269022A CN111020383A CN 111020383 A CN111020383 A CN 111020383A CN 201911269022 A CN201911269022 A CN 201911269022A CN 111020383 A CN111020383 A CN 111020383A
- Authority
- CN
- China
- Prior art keywords
- temperature
- steel plate
- equal
- steel
- thickness
- Prior art date
- Legal status (The legal status 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 status listed.)
- Pending
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- 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
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- 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
- C21D2211/008—Martensite
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
The invention discloses a large-thickness high-strength wear-resistant steel plate HYNM650, which is 80-90mm thick and comprises the following chemical components: C. si, Mn, P, S, V, Mo, Cr, B, Als, and the others are Fe and residual elements. The production method comprises the following steps: converter smelting, LF refining, VD vacuum degassing, die casting and casting, steel ingot heating, rolling, slow cooling and heat treatment. According to the invention, through reasonable chemical component design and production process control, the high-strength wear-resistant steel plate HYNM650 with large thickness of 80-90mm is developed, V is selected to replace Ni in a conventional scheme in component design, on one hand, the thickness of the produced steel plate is 60mm higher than the maximum grade NM600 steel limit thickness in the wear-resistant steel standard, on the other hand, the surface hardness of the steel plate is far higher than the hardness requirement of NM600 limit thickness, and meanwhile, the cost of steel per ton is obviously reduced, so that the high-strength wear-resistant steel plate has good market prospect and economic benefit.
Description
Technical Field
The invention belongs to the technical field of medium steel plate production, and particularly relates to a large-thickness high-strength wear-resisting plate HYNM650 and a production method thereof.
Background
The abrasion is an important failure mode of mechanical equipment, and according to incomplete statistics, the metal abrasion-resistant material consumed by abrasion in China is about 300 million tons or more every year, so that the economic loss caused by the abrasion is about 400 million yuan every year. The wear not only causes failure of the equipment parts, resulting in frequent replacement and maintenance of the workpieces, reduced equipment operating efficiency, but also consumes a large amount of energy and materials. The wear-resistant steel plate is required to be used in equipment industries such as underground mines, cement industry, road building industry, ore mining, strip mine and metallurgy industry, along with the improvement of industrialization level, the equipment upsizing is increasingly remarkable, the quality grade of the traditional wear-resistant steel cannot meet the actual engineering design requirement, and under the background, a large-thickness high-strength wear-resistant steel plate HYNM650 material is specially researched and developed according to the requirements of a certain equipment company.
Disclosure of Invention
In view of the above problems, the present invention aims to provide a high-strength and high-wear-resistance steel plate HYNM650 with large thickness.
The invention also aims to provide a production method of the large-thickness high-strength wear-resistant steel plate HYNM 650.
In order to achieve the purpose, the technical scheme adopted by the invention is that the large-thickness high-strength wear-resistant steel plate HYNM650 is 80-90mm thick and comprises the following chemical components in percentage by mass (unit, wt%): c: 0.36-0.38, Si: 0.20 to 0.40, Mn: 1.25-1.35, P: less than or equal to 0.010 percent and S: less than or equal to 0.005 and V: 0.055 to 0.075, Mo 0.55 to 0.65, Cr 1.3 to 1.5, B0.02 to 0.04, Als: 0.045-0.065, and the balance Fe and residual elements.
In order to obtain the product, the production method adopted by the invention comprises the following steps: converter smelting, LF refining, VD vacuum degassing, die casting and casting, steel ingot heating, rolling, slow cooling and heat treatment.
The tapping temperature of the converter is 1600-1650 ℃, the tapping P is less than or equal to 0.007%, argon is not blown in the tapping process, and any deoxidizer and alloy are not added into molten steel; in the LF refining process, after the refining process is finished, furnace slag turns white or yellowish white after the refining process is finished, the white slag is kept for 33-38 min, the final slag after the refining process is foamed white slag with good fluidity and proper viscosity, and the fine adjustment frequency of Als components in the LF refining process is controlled within 2 times; in the vacuum refining process, the pressure maintaining time is controlled according to 23-25 min under the pressure less than or equal to 67Pa, and rice hulls are added in time to perform soft blowing for 5-8 min after vacuum breaking; in the die casting pouring process, selecting an ingot type to ensure that the compression ratio of a finished steel plate is more than or equal to 6.0, controlling the casting pouring temperature according to 1560-1565 ℃, executing a soft argon blowing process after molten steel arrives at a station, controlling the argon blowing time to be 5-10 min, and starting pouring after 5min of sedation is required after the argon blowing is finished;
in the heating procedure, the temperature of a steel ingot is 300-400 ℃ when the steel ingot is charged, the furnace temperature is 400-500 ℃, and the steel is braised for 4 hours; after annealing, raising the temperature to 650 ℃ at a speed of less than or equal to 60 ℃/h, slowly cooling the steel along with the furnace for 12 h, raising the temperature to 600-650 ℃ at a speed of less than or equal to 60 ℃/h, preserving the heat for 2 h in the temperature interval, raising the temperature to 800 ℃ at a speed of less than or equal to 100 ℃/h, preserving the heat for 6 h, raising the temperature to 1000 ℃ at a speed of less than or equal to 100 ℃/h, rapidly raising the temperature to 1270-1280 ℃ in the process of raising the temperature to 1280 ℃ at 1000 ℃, and preserving the heat for 16-18 h.
In the rolling procedure, two-stage rolling is adopted, wherein the rolling temperature of one stage is 1050-1150 ℃, the pass reduction is 50-60 mm, and the steel airing thickness is 300-350 mm; the initial rolling temperature of the second stage is 840-880 ℃, the final rolling temperature is 800-840 ℃, and the steel plate is air-cooled after rolling is finished; in the slow cooling process, the temperature of the steel plate entering the slow cooling pit is more than or equal to 450 ℃, and the slow cooling time is 48-72 hours.
In the heat treatment process, a quenching and tempering process is adopted, the quenching heat preservation temperature is 940 ℃, the heat preservation time is 2.0-2.2 mm/mm, the tempering heat preservation temperature is 200-.
According to the invention, through reasonable chemical component design and production process control, the high-strength wear-resistant steel plate HYNM650 with large thickness of 80-90mm is developed, V is selected to replace Ni in a conventional scheme in component design, on one hand, the thickness of the produced steel plate is 60mm higher than the maximum grade NM600 steel limit thickness in the wear-resistant steel standard, on the other hand, the surface hardness of the steel plate is far higher than the hardness requirement of NM600 limit thickness, and meanwhile, the cost of steel per ton is obviously reduced, so that the high-strength wear-resistant steel plate has good market prospect and economic benefit.
Drawings
FIG. 1 is a 90mm thick surface metallographic 100X tempered martensite according to the present invention.
FIG. 2 is a 90mm thick 1/4 thick gold phase diagram 100X tempered martensite of the present invention.
FIG. 3 is a 90mm thick 1/2 thick gold phase diagram 100X tempered martensite of the present invention.
Detailed Description
In the invention, the steel plate is designed by the following components:
c: with the increase of the C concentration in austenite, the critical cooling speed is obviously reduced, the C curve is shifted to the right, and the hardenability of the steel is increased. When the steel with different carbon contents is heat treated to the same hardness, the steel with high carbon content has better wear resistance, and the wear resistance of the wear-resistant material is improved along with the increase of the carbon content. But the increase of the C content has obvious influence on the improvement of the ductile-brittle transition temperature, and the C content is controlled to be 0.36-0.38;
si: the strength of the steel plate is mainly improved by solid solution strengthening in the steel plate, but the toughness of the steel plate is affected when the content of the steel plate is too high, so the content is not suitable to be too high and is controlled to be 0.20-0.40%;
mn: the method mainly plays a role in reducing the phase transition temperature and improving the hardenability of the steel plate, but the excessive Mn content can aggravate the center segregation of the steel plate and influence the comprehensive performance of the steel plate, and the Mn content is controlled to be 1.25-1.35%;
p and S: in the steel, P, S is an impurity element, is easy to deviate to grain boundaries, reduces the surface energy of the grain boundaries, reduces the brittle fracture stress, and influences the ductile-brittle transition temperature, so the lower the content is, the better the content is;
al: the method has the advantages that the grains can be refined, the toughness of the steel can be improved, and the content of ALs is controlled to be 0.045-0.065;
v: the tempering stability of the quenched steel is improved, a secondary hardening effect is generated, the carbonization dispersion degree is high, the tempering stability and the wear resistance are improved, and the V content is controlled to be 0.055-0.075;
cr is a carbide which is the finest and can be uniformly distributed in the steel, so that the wear resistance, the strength and the hardness are higher and are controlled to be 1.30-1.50%;
refining the crystal grains of the steel, keeping enough strength and creep resistance at high temperature, improving hardenability and heat strength, and controlling the content of Mo to be 0.55-0.65;
b: the hardenability is obviously improved, and the strength of the steel plate is obviously improved after the steel plate is quenched and tempered.
The large-thickness high-strength wear-resistant steel plate HYNM650 is 80-90mm thick and comprises the following chemical components in percentage by mass (unit, wt%): c: 0.36-0.38, Si: 0.20 to 0.40, Mn: 1.25-1.35, P: less than or equal to 0.010 percent and S: less than or equal to 0.005 and V: 0.055 to 0.075, Mo 0.55 to 0.65, Cr 1.3 to 1.5, B0.02 to 0.04, Als: 0.045-0.065, and the balance Fe and residual elements.
The beneficial effect of the above component design is that by adopting the component design, the Ni with the weight percent of more than 1 percent contained in the chemical components of the conventional wear-resistant steel is cancelled, and the Ni is replaced by the V with the weight percent of 0.055-0.075 percent, so that the cost of per ton of steel can be reduced by about 400 yuan on the premise of ensuring the performance of the steel plate.
The process control in the steel plate production method is mainly as follows:
1) the requirements of converter smelting process points
The tapping temperature of the converter is 1600-1650 ℃, the tapping P is less than or equal to 0.007%, argon is not blown in the tapping process, and any deoxidizer and alloy are not added into molten steel.
2) Point requirement of LF refining process
And after the first refining and heating, turning white or yellowish white slag, keeping the white slag for 33-38 min, wherein the final slag after the refining is foamed white slag with good fluidity and proper viscosity, and the fine adjustment times of the Als component in the LF refining process are controlled within 2 times. Al wire is mainly added for deoxidation in the refining process, in addition, the component of Als also meets the material requirement, but if the adding amount of the aluminum wire is large, Al formed inside is large2O3The number of inclusions is also large, and in order to ensure that the internal inclusions are within a controllable level, the number of times of adding Al wires, namely the number of times of Als fine adjustment, needs to be limited.
3) Vacuum refining process point requirement
In the vacuum refining process, the pressure maintaining time is controlled according to 23-25 min under the pressure less than or equal to 67Pa, and rice hulls are added in time to perform soft blowing for 5-8 min after vacuum breaking.
4) Die casting
The ingot type is selected to ensure that the compression ratio of a finished steel plate is more than or equal to 6.0, the casting and pouring temperature is controlled according to 1560-1565 ℃, a soft argon blowing process is performed after molten steel arrives at a station, the argon blowing time is controlled within 5-10 min, and casting is performed after 5min of sedation is required after argon blowing is finished.
5) Requirement of heating Process
And when charging, the steel ingot temperature is 300-400 ℃, the furnace temperature is 400-500 ℃, and the steel is braised for 4 hours. After annealing, heating to 650 ℃ at a speed of less than or equal to 60 ℃/h, then slowly cooling for 12 h along with the furnace, heating to 600-650 ℃ at a speed of less than or equal to 60 ℃/h, preserving heat for 2 h in the temperature interval, heating to 800 ℃ at a speed of less than or equal to 100 ℃/h, preserving heat for 6 h, heating to 1000 ℃ at a speed of less than or equal to 100 ℃/h, then rapidly heating to 1270-1280 ℃ in the process of heating to 1280 ℃ at 1000 ℃, and preserving heat for 16-18 h.
The steel is braised mainly in a low-temperature stage, so that the temperature of the steel ingot is slowly transited to be consistent with the temperature of the furnace, on one hand, stress cracking of the steel ingot caused by overlarge temperature difference between the steel ingot and the furnace temperature is avoided, and on the other hand, temperature conditions are provided for heating the subsequent steel ingot. The temperature is raised and preserved in stages in the subsequent heating process, when the temperature is low, the temperature is not excessively raised, the steel ingot reaches a certain temperature platform, the heat preservation is carried out, the uniform temperature of the surface and the inner part of the steel ingot is mainly ensured, and the stress cracking caused by the excessively large temperature difference of the surface and the core part of the steel ingot is avoided.
6) Requirements of rolling process
Two-stage rolling is adopted, and a high-temperature low-speed high-pressure rolling process is adopted in one stage, so that the rolling force is fully permeated. The initial rolling temperature is 1050-1150 ℃, the pass reduction is 50-60 mm, and the steel airing thickness is 300-350 mm; the initial rolling temperature of the second stage is 840-880 ℃, the final rolling temperature is 800-840 ℃, the cumulative reduction rate of four passes after the second stage is more than or equal to 50%, and the steel plate is air-cooled after rolling.
In the process of pass rolling, water can be added or not. If the surface scale is less, water can not be pumped, and if the surface scale is more, a proper amount of water can be pumped. Proper amount of water is pumped to accelerate the surface cooling speed, so that a layer of hard shell relative to the inside is formed on the surface of the steel ingot, and large rolling force permeates into the steel ingot, so that core crystal grains of the steel ingot are fully crushed, internal defects are closed, and the crystal grains are refined. The flow of the high-pressure water of the rolling mill is smaller than that of ACC, the cooling speed is also smaller than that of ACC, and stress cracking of the steel plate due to rapid cooling of water pumping is avoided.
7) Requirement of slow cooling process
In the slow cooling process, the temperature of a steel plate entering a slow cooling pit is more than or equal to 450 ℃, the height of a slow cooling stack is controlled to be 1.5-2m, the upper surface and the lower surface of the steel plate are strictly prevented from being exposed in the air, and the slow cooling time is 48-72 hours.
8) Requirement of Heat treatment Process
And (3) researching various heat treatment parameters by adopting an orthogonal test, when the quenching heat preservation temperature is 940 ℃, the heat preservation time is 2.0-2.2 mm/mm, the steel plate is taken out of the furnace and cooled to the normal temperature, the cooling speed is more than or equal to 15 ℃/s, the tempering heat preservation temperature is 200-. The quality of the steel plate meets the use requirement.
The influence of the chemical composition of the steel and the heat treatment process on the wear resistance is finally reflected in the structural state. Generally, the ferritic structure steel has the worst wear resistance, while the martensitic structure steel has the better wear resistance. The steel with the tempered martensite structure obtained after quenching and tempering has obviously improved wear resistance compared with the steel with the pearlite and ferrite structure obtained after normalizing.
Examples
The high-strength wear-resistant steel plate with the chemical components of 80-90mm thickness is obtained by the processes of converter smelting, LF refining, VD vacuum degassing, die casting and casting, steel ingot heating, rolling, slow cooling, heat treatment and the like, wherein the process parameters and the mechanical properties are shown in the following tables 1 and 2.
TABLE 180-90 mm chemical composition of high-strength abrasion-resistant steel plate (Wt,%)
| Thickness (mm) | C | Si | Mn | P | S | Als | V | Mo | Cr | B |
| 80 | 0.37 | 0.35 | 1.31 | 0.008 | 0.002 | 0.055 | 0.063 | 0.62 | 1.39 | 0.033 |
| 90 | 0.36 | 0.33 | 1.33 | 0.008 | 0.002 | 0.058 | 0.065 | 0.61 | 1.42 | 0.035 |
Mechanical properties of high-strength wear-resistant steel plate with gauge of 280 mm-90 mm
10 batches of weather-resistant steel plates with the thickness of 80mm and 90mm are respectively produced by trial at this time, through reasonable chemical composition design and production process control, the surface HBW hardness 603-654, the HBW hardness 550-598 with the thickness of 1/4, the HBW hardness 500-552 with the thickness of 1/2 and the impact energy 21-49J at the temperature of minus 40 ℃ are obtained, and the structure after hardening and tempering is tempered martensite. The thickness of the steel plate is 60mm higher than the maximum NM600 steel limit thickness in the wear-resistant steel standard, and the surface hardness of the steel plate is far higher than the hardness requirement of the NM600 limit thickness, so that the special use requirement of a cooperative client is met.
Claims (3)
1. The large-thickness high-strength wear-resistant steel plate HYNM650 is characterized by comprising the following chemical components in percentage by mass: c: 0.36-0.38, Si: 0.20 to 0.40, Mn: 1.25-1.35, P: less than or equal to 0.010 percent and S: less than or equal to 0.005 and V: 0.055 to 0.075, Mo 0.55 to 0.65, Cr 1.3 to 1.5, B0.02 to 0.04, Als: 0.045-0.065, and the balance Fe and residual elements.
2. A high-strength and high-wear resistant steel plate HYNM650 as claimed in claim 1, wherein the thickness of the steel plate is 80-90 mm.
3. The production method of the large-thickness high-strength wear-resistant steel plate HYNM650 according to claim 1, which comprises the following steps: converter smelting, LF refining, VD vacuum degassing, die casting and casting, steel ingot heating, rolling, slow cooling and heat treatment, and is characterized in that:
1) a converter smelting process, wherein the tapping temperature of the converter is 1600-1650 ℃, the tapping P is less than or equal to 0.007%, argon is not blown in the tapping process, and any deoxidizer and alloy are not added into molten steel;
2) an LF refining process, namely after refining and heating are finished, changing the slag into white or yellow-white, keeping the white slag for 33-38 min, wherein the final slag after refining is foamed white slag with good fluidity and proper viscosity, and the fine adjustment frequency of Als components in the LF refining process is controlled within 2 times;
3) a VD vacuum degassing process, wherein the pressure maintaining time is controlled according to 23-25 min under the pressure of less than or equal to 67Pa, and rice hulls are added in time to conduct soft blowing for 5-8 min after vacuum breaking;
4) a die casting process, wherein an ingot type is selected to ensure that the compression ratio of a finished steel plate is more than or equal to 6.0, the casting and pouring temperature is controlled according to 1560-1565 ℃, a soft argon blowing process is performed after molten steel arrives at a station, the argon blowing time is controlled within 5-10 min, and casting is performed after 5min of sedation is required after argon blowing is finished;
5) a steel ingot heating step, wherein the temperature of a steel ingot is 300-400 ℃ during charging, the furnace temperature is 400-500 ℃, and the steel is braised for 4 hours; after annealing, raising the temperature to 650 ℃ at a speed of less than or equal to 60 ℃/h, then slowly cooling the steel along with the furnace for 12 h, after the slow cooling time is reached, raising the temperature to 600-650 ℃ at a speed of less than or equal to 60 ℃/h, preserving the heat for 2 h in the temperature interval, raising the temperature to 800 ℃ at a speed of less than or equal to 100 ℃/h, preserving the heat for 6 h, raising the temperature to 1000 ℃ at a speed of less than or equal to 100 ℃/h, rapidly raising the temperature to 1270-1280 ℃ in the process of raising the temperature to 1280 ℃, and preserving the heat for 16-;
6) the rolling procedure adopts two-stage rolling, wherein the initial rolling temperature of one stage is 1050-1150 ℃, the pass reduction is 50-60 mm, the air-dried steel thickness is 300-350 mm, the initial rolling temperature of the two stages is 840-880 ℃, the final rolling temperature is 800-840 ℃, the four-pass accumulated reduction rate after the two stages is more than or equal to 50%, and the steel plate is air-cooled after the rolling;
7) a slow cooling process, wherein the temperature of the steel plate entering a slow cooling pit is more than or equal to 450 ℃, the slow cooling time is 48-72 hours, the height of the slow cooling stack is controlled to be 1.5-2m, and the upper surface and the lower surface of the steel plate are strictly prevented from being exposed in the air;
8) a heat treatment process, wherein a quenching and tempering process is adopted, the quenching heat preservation temperature is 940 ℃, the heat preservation time is 2.0-2.2 mim/mm, the steel plate is taken out of the furnace and cooled to the normal temperature, and the cooling speed is more than or equal to 15 ℃/s; the tempering heat preservation temperature is 200-.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201911269022.7A CN111020383A (en) | 2019-12-11 | 2019-12-11 | Large-thickness high-strength wear-resistant steel plate HYNM650 and production method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201911269022.7A CN111020383A (en) | 2019-12-11 | 2019-12-11 | Large-thickness high-strength wear-resistant steel plate HYNM650 and production method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN111020383A true CN111020383A (en) | 2020-04-17 |
Family
ID=70206041
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201911269022.7A Pending CN111020383A (en) | 2019-12-11 | 2019-12-11 | Large-thickness high-strength wear-resistant steel plate HYNM650 and production method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111020383A (en) |
Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SU1104185A1 (en) * | 1983-06-07 | 1984-07-23 | Специализированное Конструкторско-Технологическое Бюро "Нормаль" | Die steel |
| CN102409235A (en) * | 2010-09-21 | 2012-04-11 | 鞍钢股份有限公司 | High-strength cold rolling transformation induced plasticity steel plate and preparation method thereof |
| CN102747272A (en) * | 2012-08-01 | 2012-10-24 | 攀枝花贝氏体耐磨管道有限公司 | B-P-T steel tube and preparation method thereof |
| JP2013076137A (en) * | 2011-09-30 | 2013-04-25 | Nippon Steel & Sumitomo Metal Corp | High strength hot-dip galvanized steel sheet excellent in plating adhesion and formability, and manufacturing method therefor |
| CN104561772A (en) * | 2014-12-26 | 2015-04-29 | 南阳汉冶特钢有限公司 | Ultralow-temperature steel plate with thickness of 130-150 mm and production method for ultralow-temperature steel plate |
| CN106498294A (en) * | 2016-11-08 | 2017-03-15 | 东北大学 | A kind of high-level low-alloy wear-resistant steel of NM600 and its application |
| CN108085589A (en) * | 2017-11-22 | 2018-05-29 | 南阳汉冶特钢有限公司 | A kind of 120mm~150mm thickness ultralow-temperature flexibility fire-resistant and weather-resistant steel and its production method |
| CN110055462A (en) * | 2019-04-25 | 2019-07-26 | 东北大学 | A kind of super abrasion-resistant stee of double scale TiC particle complex intensifying low-alloy and its manufacturing method |
| CN110453151A (en) * | 2019-09-18 | 2019-11-15 | 南阳汉冶特钢有限公司 | A kind of wearable steel plate with low cost and high strength NM600 and its production method |
-
2019
- 2019-12-11 CN CN201911269022.7A patent/CN111020383A/en active Pending
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SU1104185A1 (en) * | 1983-06-07 | 1984-07-23 | Специализированное Конструкторско-Технологическое Бюро "Нормаль" | Die steel |
| CN102409235A (en) * | 2010-09-21 | 2012-04-11 | 鞍钢股份有限公司 | High-strength cold rolling transformation induced plasticity steel plate and preparation method thereof |
| JP2013076137A (en) * | 2011-09-30 | 2013-04-25 | Nippon Steel & Sumitomo Metal Corp | High strength hot-dip galvanized steel sheet excellent in plating adhesion and formability, and manufacturing method therefor |
| CN102747272A (en) * | 2012-08-01 | 2012-10-24 | 攀枝花贝氏体耐磨管道有限公司 | B-P-T steel tube and preparation method thereof |
| CN104561772A (en) * | 2014-12-26 | 2015-04-29 | 南阳汉冶特钢有限公司 | Ultralow-temperature steel plate with thickness of 130-150 mm and production method for ultralow-temperature steel plate |
| CN106498294A (en) * | 2016-11-08 | 2017-03-15 | 东北大学 | A kind of high-level low-alloy wear-resistant steel of NM600 and its application |
| CN108085589A (en) * | 2017-11-22 | 2018-05-29 | 南阳汉冶特钢有限公司 | A kind of 120mm~150mm thickness ultralow-temperature flexibility fire-resistant and weather-resistant steel and its production method |
| CN110055462A (en) * | 2019-04-25 | 2019-07-26 | 东北大学 | A kind of super abrasion-resistant stee of double scale TiC particle complex intensifying low-alloy and its manufacturing method |
| CN110453151A (en) * | 2019-09-18 | 2019-11-15 | 南阳汉冶特钢有限公司 | A kind of wearable steel plate with low cost and high strength NM600 and its production method |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109252097B (en) | Non-quenched and tempered steel of high-strength expansion-fracture connecting rod and continuous casting production process thereof | |
| CN109023060B (en) | Steel rail and production method of steel rail | |
| CN109266966B (en) | Non-quenched and tempered round steel for direct cutting and production method thereof | |
| CN111676418B (en) | Rare earth treated HB500 grade high-wear-resistance steel plate and production method thereof | |
| CN114672723B (en) | 46MnVS series steel for expansion connecting rod and manufacturing method thereof | |
| CN114134400B (en) | Steel for large-size high-strength high-toughness oil well drill bit and preparation method thereof | |
| CN109182636B (en) | Preparation method of low-alloy bainite nodular cast iron grinding ball | |
| CN111549274A (en) | Wear-resistant Nb-containing chain plate hot-rolled steel strip and manufacturing method thereof | |
| CN114941101B (en) | Steel for bearing shaft of automobile engine and production method thereof | |
| CN109487155B (en) | Non-quenched and tempered steel for hydraulic rod of high-pressure oil cylinder and production method thereof | |
| CN109518090B (en) | Bainite steel for frog point rail and manufacturing method thereof | |
| CN111118403A (en) | Ti microalloyed high-strength high-toughness bainite non-quenched and tempered steel and forging and cooling control process and production process thereof | |
| CN114150218A (en) | Q355NE hot-rolled round steel for high-speed rail bogie and production process | |
| CN109930063B (en) | Steel for engineering machinery crawler chassis wheel body and production method thereof | |
| CN112143970A (en) | High-strength high-toughness non-quenched and tempered front axle steel and production method thereof | |
| CN111534744A (en) | Steel for die casting wear-resistant chain plate and manufacturing method thereof | |
| CN116179967A (en) | Material for thrust wheel axle and preparation method thereof | |
| CN111074146B (en) | Low-chromium cast iron grinding ball for mine and preparation method thereof | |
| CN115233503A (en) | Medium-strength steel rail with high yield strength and production method thereof | |
| CN115125448A (en) | Non-quenched and tempered steel for cold machining of hydraulic piston rod and preparation method | |
| CN112281058B (en) | Steel for large forklift goods fork and production process thereof | |
| CN111020383A (en) | Large-thickness high-strength wear-resistant steel plate HYNM650 and production method thereof | |
| CN114934239A (en) | Forged non-quenched and tempered steel for hydraulic cylinder rod head and production method thereof | |
| CN111778450A (en) | Medium-manganese medium-thickness steel for 800MPa engineering machinery and manufacturing method thereof | |
| CN111074169A (en) | Bainite ultrahigh-strength wear-resistant steel plate and production method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20200417 |