CN111471931B - Low-alloy wear-resistant steel with good bending and forming performance and production method thereof - Google Patents
Low-alloy wear-resistant steel with good bending and forming performance and production method thereof Download PDFInfo
- Publication number
- CN111471931B CN111471931B CN202010476171.7A CN202010476171A CN111471931B CN 111471931 B CN111471931 B CN 111471931B CN 202010476171 A CN202010476171 A CN 202010476171A CN 111471931 B CN111471931 B CN 111471931B
- Authority
- CN
- China
- Prior art keywords
- stage
- heating
- temperature
- quenching
- equal
- 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.)
- Active
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 115
- 239000010959 steel Substances 0.000 title claims abstract description 115
- 238000005452 bending Methods 0.000 title claims abstract description 43
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 35
- 239000000956 alloy Substances 0.000 title claims abstract description 35
- 238000004519 manufacturing process Methods 0.000 title claims description 21
- 238000010438 heat treatment Methods 0.000 claims abstract description 143
- 238000010791 quenching Methods 0.000 claims abstract description 81
- 230000000171 quenching effect Effects 0.000 claims abstract description 79
- 238000000034 method Methods 0.000 claims abstract description 56
- 230000008569 process Effects 0.000 claims abstract description 48
- 238000004321 preservation Methods 0.000 claims abstract description 40
- 238000003825 pressing Methods 0.000 claims abstract description 21
- 238000005496 tempering Methods 0.000 claims abstract description 16
- 238000002791 soaking Methods 0.000 claims abstract description 12
- 230000000452 restraining effect Effects 0.000 claims abstract description 7
- 239000000126 substance Substances 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 238000001816 cooling Methods 0.000 claims description 76
- 229910000734 martensite Inorganic materials 0.000 claims description 37
- 238000005096 rolling process Methods 0.000 claims description 37
- 229910001566 austenite Inorganic materials 0.000 claims description 18
- 238000001953 recrystallisation Methods 0.000 claims description 8
- 238000005266 casting Methods 0.000 claims description 6
- 238000003303 reheating Methods 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 229910052757 nitrogen Inorganic materials 0.000 claims description 3
- 229910052760 oxygen Inorganic materials 0.000 claims description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims description 3
- 229910052717 sulfur Inorganic materials 0.000 claims description 3
- 238000009749 continuous casting Methods 0.000 claims 1
- 238000009628 steelmaking Methods 0.000 claims 1
- 230000009466 transformation Effects 0.000 description 11
- 239000000463 material Substances 0.000 description 10
- 238000012545 processing Methods 0.000 description 10
- 230000008859 change Effects 0.000 description 9
- 230000006835 compression Effects 0.000 description 6
- 238000007906 compression Methods 0.000 description 6
- 238000001514 detection method Methods 0.000 description 5
- 238000010586 diagram Methods 0.000 description 4
- 238000002474 experimental method Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 230000005540 biological transmission Effects 0.000 description 3
- 238000005065 mining Methods 0.000 description 3
- 230000003068 static effect Effects 0.000 description 2
- 230000001174 ascending effect Effects 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 238000004886 process control Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 229910000658 steel phase Inorganic materials 0.000 description 1
- 238000000844 transformation Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D1/62—Quenching devices
- C21D1/673—Quenching devices for die quenching
-
- 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
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—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
- C22C38/04—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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—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
Abstract
The invention relates to low-alloy wear-resistant steel with good bending and forming performance, which comprises the following chemical components in percentage by weight: c: 0.24-0.30, Si: 0.15 to 0.38, Mn: 0.60-1.00, P is less than or equal to 0.013, S is less than or equal to 0.005, Als: 0.045-0.075, Nb: 0.015 to 0.060 wt% and Ti: 0.010 to 0.025, Cr: 0.40 to 0.75, Mo: 0.10 to 0.35, B: 0.0005 to 0.0018, less than or equal to 0.0025O, less than or equal to 0.0045N, less than or equal to 1.7ppm H, and the balance of Fe and inevitable impurities. The heat treatment process comprises gradient heating, constrained quenching and low-temperature tempering; the 1 st stage to the 2 nd stage of gradient heating are rapid heating sections, and the heating temperature in the 1 st stage is 890-930 ℃; the heating temperature in the 2 nd stage is 880-920 ℃; the 3 rd stage is a heat preservation soaking section, and the heat preservation temperature is 870-910 ℃; the first stage of the restraint quenching is restraint quenching of a hydraulic annular press roller, the upper press roller ascends or descends along with the frame, the working stroke is 6-52 mm, and the restraint force is 240-350 MPa; in the stage 2, the hydraulic flat pressing roller is subjected to restraint quenching, the working stroke is 5-52 mm, and the restraint force is 255-360 MPa; in the 3 rd stage, the common flat pressing roller is used for restraining and quenching, the working stroke is 5-52 mm, and the restraining force is 275-370 MPa; the low-temperature tempering temperature is 150-240 ℃. The wear-resistant steel has good toughness, wear resistance and bending forming performance.
Description
Technical Field
The invention relates to low-alloy wear-resistant steel and a production method thereof, in particular to low-alloy wear-resistant steel with good bending and forming performances and a production method thereof.
Background
The low-alloy wear-resistant steel series products have the characteristics of high strength, high hardness, high wear resistance, high low-temperature impact toughness and the like, have certain processing and forming properties, and are rapidly and widely applied to the industries of engineering machinery, mining, agricultural machinery, special vehicle manufacturing, shipbuilding, construction, oil and gas transmission and the like. With the rapid development of the industry in China, various mechanical equipment is continuously complicated, large-sized and light, and higher requirements are put forward on low-alloy high-strength wear-resistant steel for manufacturing the mechanical equipment, namely the low-alloy high-strength wear-resistant steel for manufacturing the equipment has higher hardness and strength and also has good toughness matching and processing forming performance.
Most of the processing and forming processes in the prior art are directed at steel plates with the tensile strength of about 1000MPa, and related processing and forming processes are not found for martensite wear-resistant steel products with the tensile strength of 1100MPa or above. The existing processing and forming method is not suitable for the ultra-high strength martensite wear-resistant steel, and the application range of high-end low-alloy wear-resistant steel products is seriously limited.
The bending property is used for measuring the forming property of the martensite wear-resistant steel, and reflects the advantages and disadvantages of the martensite wear-resistant steel in complex processing and forming such as plastic deformation performance, actual stamping, deep stamping, large-angle bending, rolling, even rolling ring and the like under certain conditions. The uniformity of the microstructure of the wear-resistant steel base material product and the internal stress of the quenched steel plate are main factors influencing the bending and forming performance, and the good bending performance of the base material can expand the application range of the low-alloy martensite wear-resistant steel.
Disclosure of Invention
The invention aims to solve the technical problem of providing low-alloy wear-resistant steel with good bending and forming performance, fine microstructure, uniform crystal grains and low internal stress, and also provides a production method of the low-alloy wear-resistant steel with good bending and forming performance.
The technical scheme adopted by the invention for solving the technical problems is as follows:
the low-alloy wear-resistant steel with good bending and forming performances comprises the following chemical components in percentage by weight: c: 0.24% -0.30%, Si: 0.15-0.38%, Mn: 0.60-1.00%, P is less than or equal to 0.013%, S is less than or equal to 0.005%, Als: 0.045-0.075%, Nb: 0.015% -0.060%, Ti: 0.010-0.025%, Cr: 0.40% -0.75%, Mo: 0.10% -0.35%, B: 0.0005 to 0.0018 percent, less than or equal to 0.0025 percent of O, less than or equal to 0.0045 percent of N, less than or equal to 1.7ppm of H, and the balance of Fe and inevitable impurities.
The low-alloy wear-resistant steel with good bending and forming performances preferably comprises the following chemical components in percentage by weight: c: 0.25% -0.28%, Si: 0.18-0.35%, Mn: 0.70-0.85%, P is less than or equal to 0.012%, S is less than or equal to 0.003%, Als: 0.045% -0.060%, Nb: 0.020-0.040%, Ti: 0.012-0.018%, Cr: 0.43% -0.68%, Mo: 0.13% -0.30%, B: 0.0008 to 0.0015 percent, less than or equal to 0.0025 percent of O, less than or equal to 0.0040 percent of N, less than or equal to 1.5ppm of H, and the balance of Fe and inevitable impurities.
According to the production method of the low-alloy wear-resistant steel with good bending and forming performances, the heat treatment process comprises gradient heating, constraint quenching and low-temperature tempering, so that fine and uniform martensite microstructures and low internal stress low-alloy wear-resistant steel are obtained;
the gradient heating is to divide the heat treatment heating furnace into 3 stages according to the heating area, wherein the 1 st stage to the 2 nd stage are rapid heating stages, the heating rate is more than or equal to 90 ℃/min, and the heating temperature in the 1 st stage is 890-930 ℃; the heating temperature of the 2 nd stage is 880-920 ℃; the 3 rd stage is a heat preservation and soaking stage, and the heat preservation temperature is 870-910 ℃;
the restrained quenching is to divide the roller type quenching machine into 3 stages according to a cooling area, the first stage is the restrained quenching of the hydraulic annular press roller, the hydraulic annular press roller is cooled into 1-4 areas, the upper press roller of the hydraulic annular press roller ascends or descends along with the frame to control the stroke, the working stroke range of the upper press roller is 6-52 mm, and the restraining force range of the upper press roller of the hydraulic annular press roller exerted on the quenched steel plate is 240-350 MPa; the second stage is the restraint quenching of the hydraulic flat pressing roller, the range of the working stroke of the hydraulic flat pressing roller is 5 mm-52 mm, and the range of the restraint force applied to the quenched steel plate by the hydraulic flat pressing roller is 255 MPa-360 MPa; the 3 rd stage is the restraint quenching of the common flat pressing roller, the quenching cooling is from the 9 th area to the tail area, the working stroke range of the common flat pressing roller is 5mm to 52mm, and the restraint force range of the common flat pressing roller applied to the quenched steel plate is 275MPa to 370 MPa;
the low-temperature tempering temperature is 150-240 ℃.
In the production method of the low-alloy wear-resistant steel with good bending and forming performances, the 1 st stage of gradient heating is heating the 1-4 areas, the heating rate is 100-110 ℃/min, the heat preservation time coefficient is 0.4-0.7 min/mm, the heat preservation time is 2.4-35 min, the surface and core temperature gradient is 100-150 ℃, the steel is rapidly heated to the required temperature at a large heating rate and a low heat preservation time coefficient, a large temperature gradient is formed on the surface and the core of the plate and strip, the heat is rapidly transferred to the core, and the heat efficiency is improved by about 15% compared with that of the common process; the stage 2 is heating 5-8 areas, the heating rate is 90-100 ℃/min, the heat preservation time coefficient is 0.5-0.8 min/mm, the heat preservation time is 3.0-40 min, the surface and core temperature gradient is 40-100 ℃, and the surface and core temperature gradient is reduced while the surface temperature and the core heat transmission of the plate and strip are gradually stabilized; the 3 rd stage is heating the 9 th area to the tail area, the heat preservation time coefficient is 1.0min/mm to 1.3min/mm, the heat preservation time is 6.0min to 65min, the temperature gradient of the surface and the core is +/-3 ℃, the temperature gradient in the thickness direction, the width direction and the length direction of the plate and strip is mainly eliminated, the temperature uniformity of the whole plate reaches +/-3 ℃, and the uniformity of the microstructure and the stable mechanical property are ensured.
In the production method of the low-alloy wear-resistant steel with good bending and forming performances, in the tempering procedure, the heat preservation time coefficient is 3.0 min/mm-4.0 min/mm, and the heat preservation time is 18 min-200 min; the low-temperature tempering process ensures that the microstructure and the mechanical property are not changed while the internal stress in the steel plate is fully released, so that the low-alloy wear-resistant steel with fine and uniform martensite microstructure and low internal stress is obtained, and the product has good bending forming performance while having good toughness and wear resistance.
In the production method of the low-alloy wear-resistant steel with good bending and forming performances, in the casting blank reheating process, the casting blank reheating temperature range is 1100-1160 ℃, the soaking period time is 35-55 minutes, and the temperature gradient is eliminated.
According to the production method of the low-alloy wear-resistant steel with good bending forming performance, the rolling control procedure adopts double-rolling-process controlled rolling, namely the rolling control of a rough rolling austenite recrystallization region and the rolling control of a finish rolling austenite non-recrystallization region, the rolling temperature of the rough rolling austenite recrystallization region is 1050-970 ℃, and the rolling temperature of the finish rolling austenite non-recrystallization region is 920-830 ℃; and after controlled rolling, the steel grade is slowly cooled by air cooling to obtain the original low internal stress hot rolled steel plate.
According to the production method of the low-alloy wear-resistant steel with good bending and forming performances, the thickness range of the produced wear-resistant steel plate is 6-50 mm, the original austenite grain size of the steel plate is 13.3-7.9 mu m at the positions 1/4 and 1/2 along the thickness direction surface, and the average size of the martensite lath bundle is 0.6585-0.9453 mu m; the tensile strength of the wear-resistant steel is more than or equal to 1400MPa, the surface Brinell hardness is more than or equal to 480HBW, the impact toughness at 60 ℃ below zero is more than or equal to 40J, the elongation A50 is more than or equal to 16.4%, the steel plate is bent at 3-180 degrees, the bending diameter D is 1.0-9.0H, H represents the thickness of the steel plate, the steel plate is not cracked when bent, and the bending angle straightness is 0.1 mm/full length of the steel plate-2.0 mm/full length of the steel plate.
In the industrial production process at home and abroad, a heat treatment heating furnace is generally composed of 14-16 heating zones, the furnace length of the heating furnace is generally 70-90 m, the heat treatment heating furnace is uniformly divided into 14-16 zones according to the total length, the length of each zone is the same, but the heating temperature of each zone is different. The common heating method is to divide the heating zone into two stages, namely a heating section and a heat preservation section; the heating zone in the process of the invention is accurately divided into three stages: the 1 st heating stage is heating areas 1 to 4; the 2 nd heating stage is heating 5-8 areas; the 3 rd stage is a heat preservation and soaking stage and is a heating 9-16 area.
The quenching cooling process generally comprises 3 aspects, namely, the quenching cooling process has high-strength cooling capacity and ensures that a quenching plate obtains required microstructure and mechanical properties; secondly, the quenching cooling has high uniformity, and the requirements of flatness and mechanical property uniformity of the quenching plate strip are met; and thirdly, the multifunctional high-precision quenching process is provided, and the requirements of temperature-controlled quenching and complex heat treatment are met. The length of the quenching cooling section is usually between 20 and 30 meters, the quenching cooling section is uniformly divided into 12 to 15 zones according to the total length, the length of each zone is the same, but the cooling process and the cooling function of each zone are different. Generally, the 1-8 areas are rapid cooling sections, rapid cooling is usually performed at a cooling rate (the cooling rate is confirmed according to a static CCT curve) which is greater than or equal to a martensite formation cooling rate, the cooling temperature range is from Ac3+ 30-60 ℃ to a martensite phase transformation starting point, rapid cooling of a steel plate in a high-temperature stage of a main purpose avoids other phase transformations such as bainite and pearlite, a uniform martensite structure is obtained, and the hardness and the wear resistance of the steel plate are ensured, and the 1-8 areas have large internal stress due to temperature change, microstructure change, volume change and the like, so that the steel plate has large influence on the aspects of appearance size, processing forming and the like. Generally, the 9-tail region is a medium-low speed cooling section, the cooling temperature range is from the martensite phase transformation point to the normal temperature (or the martensite project ending temperature), the 9-tail region is a martensite forming region, and the steel plate has a dominant internal stress due to the change of the microstructure, the volume change and the like, so that the aspects of appearance size, processing forming and the like are greatly influenced.
The common cooling method is to divide the cooling area into two stages, namely a high-pressure cooling section and a low-pressure cooling section; the cooling zone is accurately divided into three stages in the process of the invention: the first stage is hydraulic annular press roller restraint quenching, which is a quenching cooling zone 1-4; the 2 nd stage is the restraint quenching of the hydraulic flat pressing roller, and is a quenching cooling 5-8 area; the 3 rd stage is the restraining quenching of a common flat press roller, and is a quenching cooling 9-15 area. The main purpose is to realize a constraint quenching process, ensure that the plate and strip have good quenching flatness, promote the internal stress release of the plate and strip to obtain a low internal stress product and obtain good bending forming performance.
The gradient heating heat treatment process disclosed by the invention has the advantages that the heating temperature and the heat preservation time are accurately controlled in a segmented manner, the complete austenitization of the steel plate is ensured, the heating time and the heat preservation time coefficient at different stages are matched, fine and uniform original austenite grains are obtained, and the toughness and plasticity of the steel plate are improved.
The restraint quenching function is as follows: in the rapid cooling area, the plate and strip materials have large internal stress, the hydraulic annular compression roller, the hydraulic flat compression roller and the common flat compression roller act on the upper surface and the lower surface of the plate and strip materials with large roller pressure, the constraint force is set to be more than or equal to the yield strength of the steel plate in the high-temperature section during quenching, the external constraint force is applied in the quenching process, the plate and strip materials are guaranteed to have good quenching flatness, the internal stress of the plate and strip materials is promoted to be released, low-internal-stress products are obtained, and good bending forming performance is obtained.
The basis of the core control process of the invention is: (1) firstly, measuring the phase change transformation rules of the component system at different isothermal times and different cooling rates by using a DIL805L phase change expander, and formulating a heat treatment process according to the detection result; (2) carrying out a series of 'temperature gradient' heating heat treatment experiments by using a box type resistance heat treatment heating furnace to obtain the original austenite grain size and the corresponding martensite lath size under the component system and the process condition under the series of temperature gradient heating temperatures and series of heat preservation coefficients; (3) measuring the high-temperature stress-strain curve of the steel plate subjected to heat treatment under the component system on a WDW-300 universal mechanical experiment machine, and formulating the parameters of the constraint quenching process.
The invention has the beneficial effects that:
the thickness range of the wear-resistant steel plate produced by the invention is 6-50 mm; the microstructure is fine lath martensite, and the corresponding prior austenite grain size is graded as follows: 9.5 to 11.0 grades, the original austenite grain size of the steel plate is 13.3 to 7.9 mu m along the thickness direction surface, 1/4 and 1/2 positions, the average size of martensite lath bundles is 0.6585 to 0.9453 mu m, and the microstructure is fine and uniform; the wear-resistant steel has good toughness matching and good wear resistance, the tensile strength is more than or equal to 1400MPa, the surface Brinell hardness is more than or equal to 480HBW, the impact toughness at minus 60 ℃ is more than or equal to 40J, and the elongation A50 is more than or equal to 16.4%. The steel plate is bent at 3-180 degrees, the bending diameter D is 1.0-9.0H, H represents the thickness of the steel plate, the steel plate is not cracked when being bent, and the bending angle straightness is 0.1-2.0 mm/full length of the steel plate.
The wear-resistant steel product produced by the process disclosed by the invention not only has good toughness, wear resistance and normal-temperature elongation, but also has excellent bending forming performance, so that the martensite wear-resistant steel meets the complex processing forming of normal-temperature plastic deformation, stamping, deep stamping, large-angle bending, rolling, even rolling ring circle and the like, and the application of the low-alloy martensite wear-resistant steel to various industries with good forming performance requirements, such as engineering machinery industry, mining, agricultural machinery, special vehicle manufacturing, shipbuilding, building, oil and gas conveying and the like, is expanded.
Drawings
FIG. 1 shows the transformation law of high-grade wear-resistant steel phase change, namely a static CCT curve, under the composition system of the invention;
FIG. 2 is a high-temperature stress-strain curve of a steel plate under the chemical composition system;
FIG. 3 is a schematic diagram showing the division of the heating furnace for heat treatment according to the present invention into three heating stages;
FIG. 4 is a schematic diagram of the division of three quench cooling sections of the present invention;
FIG. 5 is a view of a microstructure of a martensite morphology after heat treatment in example 1 of the present invention;
FIG. 6 is a view of a microstructure of a martensite morphology after heat treatment in example 2 of the present invention;
FIG. 7 is a view of the microstructure of martensite morphology after heat treatment in example 3 of the present invention;
FIG. 8 is a microstructure view of martensite morphology after heat treatment in example 4 of the present invention;
FIG. 9 is a microstructure diagram of martensite morphology after heat treatment in example 5 of the present invention.
Labeled as: heating zone 1, heating stage 2, soaking stage 3, soaking stage 4, cooling zone 5, quenching cooling 1 stage 6, quenching cooling 2 stage 7, and quenching cooling 3 stage 8.
Detailed Description
The basis of the core control process of the invention is: (1) firstly, measuring the phase transformation rules of the component system with different isothermal times and different cooling rates by using a DIL805L phase transformation dilatometer, wherein the experimental results are shown in Table 1 and figure 1, the Table 1 and figure 1 show that Ac3 (the complete austenitizing temperature of the steel plate) is 827 ℃, in order to ensure that the complete austenitizing in the thickness direction and the length direction of the steel plate is sufficient and uniform, the quenching heat treatment heating is carried out, the heat preservation temperature is 30-60 ℃ above Ac3, the martensite phase transformation starts when the cooling rate reaches 20 ℃/s, the martensite starting transformation temperature is 415 ℃, the martensite starting transformation temperature is gradually reduced from 415 ℃ to 379 ℃ along with the increase of the cooling rate, and the martensite transformation ending temperature is gradually reduced from 246 ℃ to 232 ℃, and the heat treatment process is formulated according to the detection results; (2) secondly, a series of temperature gradient heating heat treatment experiments are carried out by utilizing a box type resistance heat treatment heating furnace, the component system, the original austenite grain size and the corresponding martensite lath size under the process condition under the series of temperature gradient heating temperatures and the series of heat preservation coefficients are obtained, and the detection result is shown in table 2. (3) And finally, measuring a high-temperature stress-strain curve of the steel plate subjected to heat treatment under the component system on a WDW-300 universal mechanical experiment machine, and formulating constraint quenching process parameters. The results of the measurements are shown in FIG. 2. Fig. 2 shows a high-temperature stress-strain curve of the wear-resistant steel plate under the component system at 500 ℃, 600 ℃, 750 ℃ and 850 ℃, and according to stress (yield strength) detection values at different temperatures, the constraint force of the constraint quenching process in the cooling process is set, namely the constraint force is set to be greater than or equal to the yield strength of the steel plate in the high-temperature quenching process, so that the low-internal-stress product is obtained by promoting the internal stress release of the steel plate and the strip while ensuring good quenching flatness of the steel plate and the strip, and good bending formability is obtained.
TABLE 1 phase transition law of different isothermal times and different cooling rates of the component system
TABLE 2 the change rule of martensite form (percentage content detection precision 90%) of the composition system, the production process and the series tempering process
According to the findings in Table 2, the stage 3 heating temperature is equal to the "target temperature" range, preferably 870 ℃ to 910 ℃.
The thickness range of the steel plate produced by the process is 6 mm-50 mm;
fig. 3 shows that each circle represents a heating zone, and the heating zone comprises a heating zone 1, a heating zone 2, a heating zone 3, a heating zone 4, a heating zone 5, a heating zone 6, a heating zone 7, a heating zone 8, a heating zone 9, a heating zone 10, a heating zone 11, a heating zone 12, a heating zone 13, a heating zone 14, a heating zone 15 and a heating zone 16 (tail zone) in sequence from left to right; the length of each zone is the same; the gradient heating of the invention is to accurately divide the heat treatment heating furnace into three stages according to the heating area: a 1 st heating stage 2, a 2 nd heating stage 3 and a 3 rd soaking stage 4; wherein the 1 st to the 2 nd stages are rapid heating stages, the heating rate is more than or equal to 90 ℃/min, and the heating temperature of the 1 st heating stage 2 is 890-930 ℃; the heating temperature of the heating stage 2 and the heating stage 3 is 880-920 ℃; the heat preservation temperature of the 3 rd soaking stage 4 is 870-910 ℃.
The heating stage 2 of the 1 st heating stage is a heating 1 area to a heating 4 area, the heating rate is 100 ℃/min to 110 ℃/min, the heat preservation time coefficient is 0.4min/mm to 0.7min/mm, the heat preservation time is 2.4min to 35min, the temperature gradient of the surface and the core is 100 ℃ to 150 ℃, the required temperature is quickly heated at a large heating rate and a low heat preservation time coefficient, a large temperature gradient is formed on the surface and the core of the plate and strip, the heat is quickly transferred to the core, and the heat efficiency is improved by about 15 percent compared with that of the common process; the heating stage 2 is heating 5-8 areas, the heating rate is 90-100 ℃/min, the heat preservation time coefficient is 0.5-0.8 min/mm, the heat preservation time is 3.0-40 min, the surface and core temperature gradient is 40-100 ℃, and the surface and core temperature gradient is reduced while the surface temperature and the core heat transmission of the plate and strip are gradually stabilized; the 3 rd stage is heating the 9 th area to the tail area, the heat preservation time coefficient is 1.0min/mm to 1.3min/mm, the heat preservation time is 6.0min to 65min, the temperature gradient of the surface and the core is +/-3 ℃, the temperature gradient in the thickness direction, the width direction and the length direction of the plate and strip is mainly eliminated, the temperature uniformity of the whole plate reaches +/-3 ℃, and the uniformity of the microstructure and the stable mechanical property are ensured. The heating rate of the heat treatment heating method is relatively high, and in the 3 rd soaking stage 4, because the steel plate has a large temperature gradient from inside to outside in the thickness direction, heat can be transferred from inside to outside and from outside to inside simultaneously, so that the speed is high, the energy consumption is low, and the uniformity is relatively good.
Fig. 4 shows that each circle represents a cooling zone, and the cooling zone 1, the cooling zone 2, the cooling zone 3, the cooling zone 4, the cooling zone 5, the cooling zone 6, the cooling zone 7, the cooling zone 8, the cooling zone 9, the cooling zone 10, the cooling zone 11, the cooling zone 12, the cooling zone 13, the cooling zone 14, and the cooling zone 15 (tail zone) are sequentially arranged from left to right; the length of each zone is the same; the restrained quenching of the invention is to divide the roller quenching machine into 3 stages according to the cooling area, and the main purpose is to effectively control the plate shape flatness during quenching cooling while meeting the requirement of common quenching cooling: in the 1 st stage 6 of quenching cooling, the hydraulic annular press roller is used for restraining quenching, the upper press roller is used for quenching cooling 1 to 4 areas, the stroke of the upper press roller is controlled along with the ascending or descending of the frame, the working stroke range of the hydraulic annular press roller in the 1 st stage is 6-52 mm, and the restraining force range of the hydraulic annular press roller in the 1 st stage, which is applied to a quenched steel plate, is 240-350 MPa; the quenching cooling stage 2 is that the hydraulic flat pressing roller restrains quenching, the quenching cooling is 5 to 8 areas, the working stroke range of the hydraulic flat pressing roller at stage 2 is 5 to 52mm, and the restraint force range applied to the quenching steel plate by the hydraulic flat pressing roller at stage 2 is 255 to 360 MPa; the quenching cooling stage 3 is that the common flat pressing roller is subjected to constraint quenching, the quenching cooling stage 3 is from a 9 region to a tail region, the working stroke range of the common flat pressing roller at the stage 3 is 5 mm-52 mm, and the constraint force range applied to a quenched steel plate by the common flat pressing roller at the stage 3 is 275 MPa-370 MPa; the main purpose is to realize a constraint quenching process, ensure that the plate and strip have good quenching flatness, promote the internal stress release of the plate and strip to obtain a low internal stress product and obtain good bending forming performance.
The invention is further illustrated and specifically described by the following five examples:
step 1:
the low-alloy wear-resistant steels with the thicknesses of 6mm, 16mm, 25mm, 35mm and 50mm are respectively produced in the embodiments 1-5, and the components and the mass percentages of the wear-resistant steels in the 5 embodiments are listed in the table 3:
table 3: composition and mass percentage content of wear-resistant steel
Step 2:
in the examples 1 to 5, the reheating temperature range of the casting blank is 1100 to 1160 ℃, the soaking period time is 35 to 55min, the rough rolling temperature range is 1050 to 970 ℃, and the finish rolling temperature range is 920 to 830 ℃. And after controlled rolling, the steel grade is slowly cooled to room temperature by air cooling.
Table 4: examples 1 to 5 Process parameters of Low-alloy wear-resistant steels at Rolling stage
And step 3:
the heat treatment processes of the embodiments 1 to 5 include gradient heating, constrained quenching and low-temperature tempering, so that fine and uniform martensite microstructures and low-alloy wear-resistant steel with low internal stress are obtained, and good bending performance is obtained.
The control parameters of the gradient heating heat treatment process of examples 1 to 5 are shown in Table 5:
TABLE 5 control parameters for gradient heat treatment process of examples 1 to 5
The gradient heating heat treatment process controls the heating temperature and the heat preservation time accurately in a segmented manner, ensures the complete austenitization of the steel plate, simultaneously matches the heating time and the heat preservation time coefficient of different stages, obtains fine and uniform original austenite grains, and improves the toughness and plasticity of the steel plate.
(2) And a constraint quenching heat treatment process, namely accurately dividing the roller type quenching machine into 3 stages according to a cooling area, wherein the quenching cooling stage 1 is hydraulic annular press roller constraint quenching, the quenching cooling stage 2 is hydraulic flat press roller constraint quenching, and the quenching cooling stage 3 is common flat press roller constraint quenching. The control parameters of the constrained quenching process are shown in table 6:
table 6 control parameters for the constrained quench heat treatment process of examples 1-5
The effect of the restraint quenching is as follows: in the rapid cooling area, the plate and strip materials have large internal stress, the hydraulic annular compression roller, the hydraulic flat compression roller and the common flat compression roller act on the upper surface and the lower surface of the plate and strip materials with large roller pressure, the constraint force is set to be more than or equal to the yield strength of the steel plate in the high-temperature section during quenching, the external constraint force is applied in the quenching process, the plate and strip materials are guaranteed to have good quenching flatness, the internal stress of the plate and strip materials is promoted to be released, low-internal-stress products are obtained, and good bending forming performance is obtained.
(3) A low-temperature tempering process:
the tempering temperature is 150-240 ℃, the temperature-keeping time coefficient range is 3.0 min/mm-4.0 min/mm, the temperature-keeping time range is 18 min-200 min, the low-temperature tempering process ensures that the internal stress in the steel plate is fully released, but the microstructure and the mechanical property are not changed, the low-alloy wear-resistant steel with fine and uniform martensite microstructure and low internal stress is obtained, and the product has good toughness and wear resistance and good bending forming performance. The low temperature tempering process parameters of examples 1 to 5 are shown in table 7.
Table 7 examples 1-5 low temperature tempering process parameters
| Examples | Thickness mm | Tempering temperature DEG C | Temperature keeping time coefficient min/mm | |
| 1 | 6 | 150 | 4.0 | 24 |
| 2 | 16 | 180 | 4.0 | 64 |
| 3 | 25 | 200 | 3.5 | 87.5 |
| 4 | 35 | 220 | 3.5 | 122.5 |
| 5 | 50 | 240 | 3.0 | 150 |
And 4, step 4:
tables 8 and 9 show the good microstructure and mechanical properties of the low alloy wear resistant steel products produced in examples 1 to 5.
Table 8 microstructure of low alloy wear resistant steel products produced in examples 1 to 5
TABLE 9 mechanical Properties of the low-alloy wear-resistant steel products produced in examples 1 to 5
Table 8 shows that the prior austenite grains of examples 1 to 5 are rated from 9.5 to 11.0, and the steel sheet has, in the thickness direction: the original austenite grain size at the surface, 1/4 and 1/2 positions is 13.3-7.9 μm, and FIGS. 5-9 are microstructure diagrams corresponding to examples 1-5, and are fine lath martensite, and it can be seen from Table 8 that the average size of the martensite lath bundle is 0.6585-0.9453 μm, and the microstructure is fine and uniform.
Table 9 shows that the wear-resistant steel produced by the process has good toughness matching and good wear resistance, the tensile strength is more than or equal to 1400MPa, the surface Brinell hardness is more than or equal to 480HBW, the impact toughness at minus 60 ℃ is more than or equal to 40J, and the elongation A50 is more than or equal to 16.4%. The steel plate is bent at 3-180 degrees, the bending diameter D is 1.0-9.0H, H represents the thickness of the steel plate, the steel plate is not cracked when being bent, and the bending angle straightness is 0.1-2.0 mm/full length of the steel plate.
The wear-resistant steel product produced by the process disclosed by the invention not only has good toughness, wear resistance and normal-temperature elongation, but also has excellent bending forming performance, so that the martensite wear-resistant steel meets the complex processing forming of normal-temperature plastic deformation, stamping, deep stamping, large-angle bending, rolling, even rolling ring circle and the like, and the application of the low-alloy martensite wear-resistant steel to various industries with good forming performance requirements, such as engineering machinery industry, mining, agricultural machinery, special vehicle manufacturing, shipbuilding, building, oil and gas conveying and the like, is expanded.
Claims (4)
1. A production method of low-alloy wear-resistant steel with good bending and forming performance comprises the working procedures of steel making, continuous casting, casting blank reheating, controlled rolling, controlled cooling and heat treatment, wherein the wear-resistant steel comprises the following chemical components in percentage by weight: c: 0.24% -0.30%, Si: 0.15-0.38%, Mn: 0.60-1.00%, P is less than or equal to 0.013%, S is less than or equal to 0.005%, Als: 0.045-0.075%, Nb: 0.015% -0.060%, Ti: 0.010-0.025%, Cr: 0.40% -0.75%, Mo: 0.10% -0.35%, B: 0.0005 to 0.0018 percent, less than or equal to 0.0025 percent of O, less than or equal to 0.0045 percent of N, less than or equal to 1.7ppm of H, and the balance of Fe and inevitable impurities; the method is characterized in that: the thickness range of the wear-resistant steel plate is 6 mm-50 mm, the original austenite grain size of the steel plate is 13.3 mu m-7.9 mu m along the thickness direction surface, 1/4 and 1/2 positions, and the average size of martensite lath bundles is 0.6585 mu m-0.9453 mu m; the tensile strength of the wear-resistant steel is more than or equal to 1400MPa, the surface Brinell hardness is more than or equal to 480HBW, the impact toughness at minus 60 ℃ is more than or equal to 40J, and the elongation A50 is more than or equal to 16.4%; the steel plate is not cracked when being bent at 3-180 degrees, the bending diameter D = 1.0H-9.0H, and H represents the thickness of the steel plate; the bending angle straightness is 0.1 mm/full steel plate length to 2.0 mm/full steel plate length;
the heat treatment process comprises gradient heating, constraint quenching and low-temperature tempering;
the gradient heating is to divide the heat treatment heating furnace into 3 stages according to the heating area, wherein the 1 st stage to the 2 nd stage are rapid heating stages, the heating rate is more than or equal to 90 ℃/min, and the heating temperature in the 1 st stage is 890-930 ℃; the heating temperature of the 2 nd stage is 880-920 ℃; the 3 rd stage is a heat preservation and soaking stage, and the heat preservation temperature is 870-910 ℃;
the restrained quenching is to divide the roller type quenching machine into 3 stages according to a cooling area, the first stage is the restrained quenching of the hydraulic annular press roller, the hydraulic annular press roller is cooled into 1-4 areas, the upper press roller of the hydraulic annular press roller ascends or descends along with the frame to control the stroke, the working stroke range of the upper press roller is 6-52 mm, and the restraining force range of the upper press roller of the hydraulic annular press roller exerted on the quenched steel plate is 240-350 MPa; the second stage is the restraint quenching of the hydraulic flat pressing roller, the range of the working stroke of the hydraulic flat pressing roller is 5 mm-52 mm, and the range of the restraint force applied to the quenched steel plate by the hydraulic flat pressing roller is 255 MPa-360 MPa; the 3 rd stage is the restraint quenching of the common flat pressing roller, the quenching cooling is from the 9 th area to the tail area, the working stroke range of the common flat pressing roller is 5mm to 52mm, and the restraint force range of the common flat pressing roller applied to the quenched steel plate is 275MPa to 370 MPa;
the low-temperature tempering temperature is 150-240 ℃, the heat preservation time coefficient is 3.0 min/mm-4.0 min/mm, and the heat preservation time is 18 min-200 min.
2. The method for producing a low alloy wear resistant steel with good bending formability according to claim 1, wherein: the 1 st stage of gradient heating is heating the 1-4 areas at a heating rate of 100-110 ℃/min, a heat preservation time coefficient of 0.4-0.7 min/mm, a heat preservation time of 2.4-35 min and a surface and core temperature gradient of 100-150 ℃; the stage 2 is heating 5-8 areas, the heating rate is 90-100 ℃/min, the heat preservation time coefficient is 0.5-0.8 min/mm, the heat preservation time is 3.0-40 min, and the surface and core temperature gradient is 40-100 ℃; the 3 rd stage is heating the 9 th to the last zones, the heat preservation time coefficient is 1.0min/mm to 1.3min/mm, the heat preservation time is 6.0min to 65min, and the surface and core temperature gradient is +/-3 ℃.
3. The method for producing a low alloy wear resistant steel with good bending formability according to claim 2, wherein: in the casting blank reheating process, the reheating temperature of the casting blank is 1100-1160 ℃, and the soaking period time is 35-55 min.
4. The method for producing a low alloy wear resistant steel with good bending formability according to claim 3, wherein: the controlled rolling procedure adopts double-rolling-process controlled rolling, namely controlled rolling in a rough rolling austenite recrystallization region and controlled rolling in a finish rolling austenite non-recrystallization region, wherein the rolling temperature of the rough rolling austenite recrystallization region is 1050-970 ℃, and the rolling temperature of the finish rolling austenite non-recrystallization region is 920-830 ℃ in a finish rolling second rolling process; and after controlled rolling, slowly cooling by air cooling to obtain the original low internal stress hot rolled steel plate.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010476171.7A CN111471931B (en) | 2020-05-29 | 2020-05-29 | Low-alloy wear-resistant steel with good bending and forming performance and production method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010476171.7A CN111471931B (en) | 2020-05-29 | 2020-05-29 | Low-alloy wear-resistant steel with good bending and forming performance and production method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN111471931A CN111471931A (en) | 2020-07-31 |
| CN111471931B true CN111471931B (en) | 2022-01-25 |
Family
ID=71765209
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010476171.7A Active CN111471931B (en) | 2020-05-29 | 2020-05-29 | Low-alloy wear-resistant steel with good bending and forming performance and production method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111471931B (en) |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FI20115599A (en) * | 2011-06-15 | 2012-12-16 | Rautaruukki Oyj | PROCEDURE FOR MANUFACTURING A STEEL PRODUCT AND A STEEL PRODUCT |
| CN103789655A (en) * | 2014-01-16 | 2014-05-14 | 北京科技大学 | Method for producing Nb alloying high-strength wear-resisting steel plate through on-line quenching |
| CN106756489A (en) * | 2016-12-14 | 2017-05-31 | 武汉钢铁股份有限公司 | 450 grades of anti-crack high-strength abrasion-proof steels of Brinell hardness and its manufacture method |
| CN108034886A (en) * | 2017-11-15 | 2018-05-15 | 东北大学 | A kind of low-density lightweight body of tipper carriage wear-resisting steel plate and preparation method thereof |
| CN108517465A (en) * | 2018-05-15 | 2018-09-11 | 马钢(集团)控股有限公司 | A kind of niobium titanium chromium-boron alloy abrasion-resistant stee and preparation method thereof |
| CN108715976A (en) * | 2018-05-25 | 2018-10-30 | 山东钢铁股份有限公司 | A kind of Ti-Zr-C granules reinforced wear resistances steel and preparation method thereof |
| JP2019044206A (en) * | 2017-08-30 | 2019-03-22 | Ｊｆｅスチール株式会社 | Thick walled antifriction steel sheet, manufacturing method thereof, and manufacturing method of antifriction member |
| CN110964979A (en) * | 2019-12-05 | 2020-04-07 | 邯郸钢铁集团有限责任公司 | Wear-resistant steel with good forming performance for dumper carriage and production method thereof |
-
2020
- 2020-05-29 CN CN202010476171.7A patent/CN111471931B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FI20115599A (en) * | 2011-06-15 | 2012-12-16 | Rautaruukki Oyj | PROCEDURE FOR MANUFACTURING A STEEL PRODUCT AND A STEEL PRODUCT |
| CN103789655A (en) * | 2014-01-16 | 2014-05-14 | 北京科技大学 | Method for producing Nb alloying high-strength wear-resisting steel plate through on-line quenching |
| CN106756489A (en) * | 2016-12-14 | 2017-05-31 | 武汉钢铁股份有限公司 | 450 grades of anti-crack high-strength abrasion-proof steels of Brinell hardness and its manufacture method |
| JP2019044206A (en) * | 2017-08-30 | 2019-03-22 | Ｊｆｅスチール株式会社 | Thick walled antifriction steel sheet, manufacturing method thereof, and manufacturing method of antifriction member |
| CN108034886A (en) * | 2017-11-15 | 2018-05-15 | 东北大学 | A kind of low-density lightweight body of tipper carriage wear-resisting steel plate and preparation method thereof |
| CN108517465A (en) * | 2018-05-15 | 2018-09-11 | 马钢(集团)控股有限公司 | A kind of niobium titanium chromium-boron alloy abrasion-resistant stee and preparation method thereof |
| CN108715976A (en) * | 2018-05-25 | 2018-10-30 | 山东钢铁股份有限公司 | A kind of Ti-Zr-C granules reinforced wear resistances steel and preparation method thereof |
| CN110964979A (en) * | 2019-12-05 | 2020-04-07 | 邯郸钢铁集团有限责任公司 | Wear-resistant steel with good forming performance for dumper carriage and production method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN111471931A (en) | 2020-07-31 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN110904319B (en) | Manufacturing process of high-carbon tool steel SK85 cold-rolled wide steel strip | |
| JP5712302B2 (en) | Manufacturing method of foreign parts | |
| CN110184525B (en) | High-strength Q500GJE quenched and tempered steel plate for building structure and manufacturing method thereof | |
| CN101492787B (en) | Medium-high-carbon microalloy non-hardened and tempered steel and controlled forging and cooling process | |
| Pachurin et al. | Economical preparation of 40X steel for cold upsetting of bolts. | |
| CN112553538B (en) | Low-hardness 20CrMnTi round steel | |
| CN102400038A (en) | Hot-rolled dual-phase steel and production method thereof | |
| CN102691018A (en) | Low-compression ratio super-strength steel plate for ocean engineering and manufacturing method thereof | |
| CN109207858B (en) | Production method of low-alloy ultrahigh-strength steel Q1100E sheet | |
| CN110918642A (en) | Production control method for improving bending degree of 42CrMo bar | |
| US10557183B2 (en) | Work hardenable yield ratio-controlled steel and method of manufacturing the same | |
| CN114293111B (en) | 1.1GPa grade sheet layer-alternated martensite-ferrite dual-phase steel and preparation method thereof | |
| CN107475623A (en) | A kind of hot forming high-strength steel and its processing method | |
| CN110252804A (en) | The production method of hot continuous rolling production thin gauge ultra-low-carbon steel | |
| CN102965591A (en) | High-strength steel rolling hot-forming technology | |
| CN111471931B (en) | Low-alloy wear-resistant steel with good bending and forming performance and production method thereof | |
| CN111549300A (en) | Steel with yield strength of 800MPa for engineering machinery and preparation method thereof | |
| CN111575609A (en) | Steel with high strength, good plasticity and toughness for engineering machinery and preparation method thereof | |
| CN109047692B (en) | Ultrathin high-strength steel plate capable of being used at-60 ℃ and manufacturing method thereof | |
| CN111304413A (en) | Spring flat steel and preparation method thereof | |
| CN102936695A (en) | High-strength low-temperature pressure vessel steel plate and production method thereof | |
| CN114107637A (en) | Preparation method of steel with yield strength of 890MPa grade for rare earth engineering machinery | |
| CN102766807A (en) | Boron contained bainite steel plate and manufacturing method thereof | |
| CN107419174B (en) | Economical high-carbon steel and its manufacturing method | |
| CN115216701B (en) | Low-compression-ratio lamellar tearing resistant Q960 high-strength steel and preparation 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 | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20240328 Address after: 056015 Fuxing Road 232, Fuxing District, Hebei, Handan Patentee after: HANDAN IRON & STEEL GROUP Co.,Ltd. Country or region after: China Patentee after: Handan Branch of Hegang Co.,Ltd. Patentee after: Hangang Nengjia Steel Co.,Ltd. Address before: 056015 Fuxing Road 232, Fuxing District, Hebei, Handan Patentee before: HANDAN IRON & STEEL GROUP Co.,Ltd. Country or region before: China Patentee before: Handan Branch of Hegang Co.,Ltd. |