CN111334720B - High Al wear-resistant steel strip with good cold formability and production method thereof - Google Patents
High Al wear-resistant steel strip with good cold formability and production method thereof Download PDFInfo
- Publication number
- CN111334720B CN111334720B CN202010238334.8A CN202010238334A CN111334720B CN 111334720 B CN111334720 B CN 111334720B CN 202010238334 A CN202010238334 A CN 202010238334A CN 111334720 B CN111334720 B CN 111334720B
- Authority
- CN
- China
- Prior art keywords
- percent
- wear
- rolling
- cooling
- 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
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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- 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
- C21D11/00—Process control or regulation for heat treatments
- C21D11/005—Process control or regulation for heat treatments for cooling
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- 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
- C21D2211/001—Austenite
-
- 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
- C21D2211/005—Ferrite
-
- 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 a high Al wear-resistant steel strip with good cold forming performance, which is designed by adopting high aluminum components, and comprises the following chemical components in percentage by weight: 0.10 to 0.24 percent of C, 1.0 to 1.5 percent of Si, 1.50 to 2.00 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.010 percent of S, 0.40 to 0.70 percent of Als, Ti: 0.010-0.040%, N is less than or equal to 0.0045%, and the balance is Fe and inevitable residual elements. The controlled rolling and controlled cooling technology is adopted in the steel rolling process, the three-phase metallographic structure of ferrite, martensite and retained austenite is obtained on line through segmented cooling, post-rolling heat treatment is not needed, the process flow is short, and the method is energy-saving and environment-friendly. The wear-resistant steel strip produced by the invention has uniform grain size, stable performance and good cold forming and wear resistance, and can be widely applied to the fields of dumper trucks, concrete mixing tanks, pump trucks, hoppers and the like.
Description
Technical Field
The invention relates to a wear-resistant steel strip, in particular to a high-Al wear-resistant steel strip with good cold forming performance and a production method thereof.
Background
The high-strength wear-resistant steel has the characteristics of high hardness, high wear resistance, easiness in welding, formability, long service life and the like, and is widely applied to the fields of dumper trucks, load-carrying vehicles, concrete mixer trucks, pump trucks, hoppers, mineral machinery and the like. At present, high-strength wear-resistant steel is divided into wear-resistant steel and hot-rolled wear-resistant steel in the traditional process according to a manufacturing method, the wear-resistant steel in the traditional process is obtained by off-line modulation heat treatment after rolling, and the problems of long process flow, high process energy consumption, long delivery cycle and the like exist. The hot-rolled wear-resistant steel is obtained by adopting a one-step production method of controlled rolling and online quenching, and the method has the advantages of short process flow, energy conservation, environmental protection and convenience for large-scale industrial production.
In recent years, with the implementation of national policies of automobile lightweight and environmental protection, the advantages of hot-rolled wear-resistant steel are continuously reflected, the market demand for hot-rolled wear-resistant steel is continuously increased, and various domestic steel mills and research institutions are developing related researches; however, in the prior art, in order to obtain the high strength, high hardness and high hardenability required by the wear-resistant steel, most manufacturers add a large amount of Cr, Ni, Mo and other expensive alloy elements in the component design, so that the material plasticity is reduced while the strength is improved, the welding performance is poor, the risk of material processing cracking and welding quality defect occurrence is increased, and the processing and use of users are affected.
Patent application with publication number CN 106244920a discloses "wear-resistant steel with brinell hardness of 450 grade" and manufacturing method thereof ", which comprises the following chemical components by weight percent: c: 0.17% -0.22%, Si: 0.40% -0.60%, Mn: 1.2-1.45%, P is less than or equal to 0.01%, S is less than or equal to 0.005%, Cr: 0.6-0.85%, Ni is less than or equal to 0.1%, Mo is less than or equal to 0.1%, Als: 0.02-0.05%, less than or equal to 0.015% of Ti, less than or equal to 0.02% of V, less than or equal to 0.004% of B, and the balance of iron and inevitable impurities; the technology of off-line quenching and low-temperature tempering is adopted, the technology is complex, the process energy consumption is high, and the delivery period is long in the traditional manufacturing method of wear-resistant steel. In addition, the wear-resistant steel produced by the method has the defects of high strength, insufficient plasticity, elongation within 12.0 percent and easy cracking in large-deformation cold working.
The patent with publication number CN108034890A discloses 'a low-alloy medium-manganese wear-resistant steel hot-rolled plate and a preparation method thereof', which comprises the following chemical components in percentage by weight: c: 0.6% -0.8%, Si: 0.1% -0.2%, Mn: 4.5-4.9%, P is less than or equal to 0.02%, S is less than or equal to 0.02%, Cr: 3.0% -3.5%, Cu: 0.4-1.0 percent, and the balance of Fe and impurities. The patent technology has the defects that the content of C is high, the strength is excessive, the cold forming performance is insufficient, and the welding performance is influenced by excessively high carbon equivalent; the Cu element is added into the steel without adding an alloy element for inhibiting Cu heat cracking, so that the Cu heat cracking phenomenon is easily generated in the casting and rolling processes, the production difficulty is increased, and the product percent of pass is influenced.
The patent with publication number CN103255341A discloses 'a high-strength high-toughness hot-rolled wear-resistant steel and a manufacturing method thereof', which comprises the following chemical components in percentage by weight: c: 0.20% -0.50%, Si: 0.8% -2.0%, Mn: 1.5-3.0%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Al: 0.02% -0.08%, N is less than or equal to 0.006%, O is less than or equal to 30ppm, Ti: 0.005% -0.015%, Ni: 0.5% -2.0%, and the sum of Mn and Ni is 3.2% -3.6%, and the balance is Fe and unavoidable impurities. The strengthening principle adopts the phase change induction effect to enhance the hardness and the wear resistance of the wear-resistant steel, the phase change induction effect can only play a good role under the condition of load impact in the mode, and the wear resistance under the condition of no load impact is similar to that of the common low-alloy high-strength steel.
Disclosure of Invention
The invention aims to solve the technical problem of providing a high-Al wear-resistant steel strip with good cold forming property and a production method thereof, and hot-rolled wear-resistant steel with low cost, high strength, high hardness and good cold forming property is produced on a conventional hot continuous rolling production line, and the hot-rolled wear-resistant steel strip does not need post-rolling heat treatment, has short process flow, and is energy-saving and environment-friendly.
The technical scheme for solving the technical problems is as follows:
the high Al wear-resistant steel strip with good cold forming performance comprises the following chemical components in percentage by weight: 0.10 to 0.24 percent of C, 1.0 to 1.5 percent of Si, 1.50 to 2.00 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.010 percent of S, 0.40 to 0.70 percent of Als, Ti: 0.010-0.040%, N is less than or equal to 0.0045%, and the balance is Fe and inevitable residual elements.
The production method of the high Al wear-resistant steel strip with good cold formability comprises the following production processes of continuous casting, slab heating, rolling, cooling and coiling: in the slab continuous casting process, the continuous casting billet comprises the following chemical components in percentage by weight: 0.10 to 0.24 percent of C, 1.0 to 1.5 percent of Si, 1.50 to 2.00 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.010 percent of S, 0.40 to 0.70 percent of Als, Ti: 0.010-0.040%, N is less than or equal to 0.0045%, and the balance is Fe and inevitable residual elements.
In the cooling process, laminar cooling adopts a sectional cooling mode, the first-stage cooling rate is 20-50 ℃/s, the intercooling temperature is 630-690 ℃, the air cooling heat preservation time is 5-10s, then the second-stage cooling is carried out, the second-stage cooling rate is 35-60 ℃/s, the steel strip is cooled to be below 150 ℃ and coiled, and the three-phase structure of 10-20% of ferrite, 75-90% of martensite and 1-8% of residual austenite is obtained on line.
In the rolling process, 3+5 passes of rough rolling are adopted, the final reduction rate of 2 passes is controlled to be 20-30%, the cumulative reduction rate of the rough rolling is controlled to be 70-85%, a heat-insulating cover is used in a middle roller way, the cumulative reduction rate of finish rolling is controlled to be 60-80%, and the final rolling temperature is controlled to be 850-.
In the slab heating process, the slab heating time is 180-.
According to the production method of the high-Al wear-resistant steel strip with good cold formability, in the continuous casting process, the temperature of molten steel entering a ladle is controlled to be 1505-1545 ℃, the superheat degree delta T =10-30 ℃, the steel strip is pulled at a constant pulling speed of 0.9-1.3m/min, the solidification tail end of a casting blank is subjected to dynamic soft reduction, the reduction total amount is not less than 6mm, and argon protection casting is carried out in the whole process to prevent outside air from entering; hoisting the billet into a stack position surrounded by the hot billet for slow cooling within 10 minutes after the billet is off line, wherein the slow cooling time is more than or equal to 48 hours; the constant pulling speed is kept during casting to ensure that the casting is stable and reduce liquid level fluctuation slag entrapment, and the solidification tail end is provided with enough dynamic soft reduction to break columnar crystals, so that the grains are refined in the recrystallization process, and the inner quality and the component segregation of the steel billet are improved.
The finished product thickness of the high Al wear-resistant steel strip with good cold forming performance is 2.5-12.0 mm; the yield strength is more than or equal to 600MPa, the tensile strength is more than or equal to 900MPa, the elongation is more than or equal to 14.0 percent, and the Brinell hardness HBW is between 200 and 400; cold bending property: the bending pressure head is bent by 120 degrees normally when the diameter of the bending pressure head is 5 times of the thickness.
The invention mainly bases on the design of components:
c: the carbon plays a role in interstitial solid solution strengthening, the strength, hardness and hardenability of the steel are ensured, the C can form TiC precipitation with small dispersion with Ti, the strength of the steel is improved, and the wear resistance is also improved; however, too high carbon causes deterioration of plasticity, toughness and weldability, and therefore, it is preferable to control the C content to 0.10wt% to 0.24 wt% in the present invention.
Si and Mn: the invention adopts the design of Mn component in high Si, and has three main reasons: firstly, Si deoxidizes molten steel, and forms silicate together with calcium and aluminum to improve steel quality; secondly, the critical cooling speed of the steel can be reduced by the manganese, and the hardenability of the steel can be greatly improved by the mutual coordination of Mn and Si; and Mn is an austenite stabilizing element, delays the transformation from austenite to pearlite, enlarges the process window and is beneficial to tissue regulation. However, too high Si increases the brittleness of steel, decreases the impact toughness, and affects the surface quality, and excessive Mn tends to form severe center segregation and to deteriorate the uniformity of the structure. Therefore, Si in the present invention is preferably controlled to 1.0wt% to 1.5 wt%, and Mn is preferably controlled to 1.50 wt% to 2.00 wt%.
Al: the invention creatively adopts the high Al design, on one hand, the aluminum plays a role in deoxidation in molten steel smelting, on the other hand, due to the consideration of structure property regulation and control, the proper amount of aluminum is added into the steel, so that an austenite region can be reduced, a ferrite phase transformation window is expanded, ferrite with a certain proportion can be obtained by controlling cooling, the cold forming property and the impact toughness of the steel are improved, but the excessive Al can form large-size Al2O3Inclusion reduces the low-temperature impact property of the steel plate and increases the risk of cold machining cracking. In addition, too high Al lowers the self-corrosion potential of the steel and lowers the corrosion resistance. Therefore, the Al content in the present invention is preferably controlled to be between 0.4wt% and 0.7 wt%.
Ti: the invention plays a role in precipitation strengthening and grain refinement, Ti is an element formed by strong carbon and nitrogen compounds, the carbide TiC particles are fine and have extremely high hardness, and the hardness and the wear resistance of the steel plate can be effectively improved by dispersing and distributing the carbide TiC particles in the matrix of the steel plate. Proper amount of Ti is added into the steel to form fine titanium carbonitride, which can effectively inhibit the growth of crystal grains during heating and play a role in refining the crystal grains. However, too high Ti combines with N to form coarse TiN inclusions, which degrade the low temperature toughness and fatigue properties of the steel sheet. Therefore, the addition amount of Ti in the invention is controlled between 0.010wt% and 0.040 wt%.
In the cooling process, a sectional cooling technology is adopted to obtain a ferrite + martensite + retained austenite three-phase structure on line, post-rolling heat treatment is not needed, the process flow is shortened, and the cost and the energy consumption are reduced, and the main basis is as follows:
the sectional cooling technology mainly relates to two-section cooling, wherein pro-eutectoid ferrite with a certain proportion is obtained in the first-section cooling through reasonable allocation of cooling speed, inter-cooling temperature and air cooling time, and then the remaining austenite is converted into a martensite structure through rapid concentrated cooling in the second-section cooling, so that a ferrite + martensite + residual austenite three-phase structure is finally obtained. In the cooling process, the control of the first-stage cooling rate, the intercooling temperature and the air cooling time is key, the first-stage cooling rate is too slow, the intercooling temperature is too high, the air cooling time is too short, the formed pro-eutectoid ferrite is less, the martensite proportion is too high, the steel strength is too high, and the cold forming and impact properties are not good; on the contrary, the ratio of martensite formed is low, the strength and hardness of the steel are insufficient, and the wear resistance is insufficient. Therefore, in the cooling process, the first-stage cooling rate is controlled to be 20-50 ℃/s, the intercooling temperature is 630-.
The invention has the beneficial effects that:
1) the invention adopts the high Al design of 0.4wt% -0.7 wt% in the components, avoids using expensive alloys such as Cr, Mo, Ni and the like, and the addition of a proper amount of Al can reduce an austenite region, enlarge a process window, be beneficial to regulating and controlling the structure performance and effectively improve the cold forming performance of steel. The elongation of the wear-resistant steel with high Al design reaches more than 14 percent, the elongation of the wear-resistant steel produced by the prior art is mostly within 12 percent, and the wear-resistant steel is easy to crack in the cold machining process.
2) The continuous casting process provided by the invention has the advantages that the tundish temperature, the superheat degree and the drawing speed are subjected to standard control in the casting process, and the steel purity is improved. The dynamic soft reduction technology is adopted at the solidification tail end of the casting blank, the reduction total amount is more than or equal to 6mm, and the segregation of the internal quality and the components of the steel billet can be effectively improved.
3) The steel rolling process adopts a one-step production method of controlled rolling and sectional cooling, obtains a ferrite, martensite and retained austenite three-phase structure on line by controlled rolling and sectional cooling technologies, does not need post-rolling heat treatment, and has the advantages of short process flow, energy saving, environmental protection and convenience for large-scale industrial production.
4) The metallographic structure of the hot-rolled wear-resistant steel produced according to the invention is composed of ferrite, martensite and retained austenite, the hardness-hardness ratio is moderate, the yield strength is more than or equal to 600MPa, the tensile strength is more than or equal to 900MPa, the elongation is more than or equal to 14.0%, the Brinell hardness is between 200 and 400 HBW, the steel is bent by 120 degrees without cracks when a bending pressure head with the thickness of 5 times is adopted, the steel has good cold forming performance, and can be widely applied to the hot door fields of dump trucks, concrete mixing tanks, pump trucks and the like.
Drawings
FIG. 1 is a metallographic photograph of the wear resistant steel strip produced in example 1 at 1/2 mm thickness;
FIG. 2 is a metallographic photograph of the wear resistant steel strip produced in example 2 at 1/2 mm thickness;
FIG. 3 is a metallographic photograph of the wear resistant steel strip produced in accordance with example 3 at 1/2 mm thickness;
FIG. 4 is a metallographic photograph of the wear resistant steel strip produced in example 4 at 1/2 thick;
FIG. 5 is a metallographic photograph of the wear resistant steel strip produced in accordance with example 5 taken at 1/2 mm thick;
FIG. 6 is a metallographic photograph of the wear resistant steel strip produced in example 6 at 1/2 thick.
Detailed Description
In order to better explain the invention, the main content of the invention is further clarified below with reference to specific examples.
The invention relates to a high Al wear-resistant steel strip with good cold formability and a production method thereof, wherein the chemical composition control is shown in Table 1, and the production process flow comprises the following steps: continuous casting → heating of the slab → rolling → cooling → coiling.
TABLE 1 chemical composition control of abrasion resistant steels (unit: wt%)
In the continuous casting process, the temperature of the tundish is between 1505 and 1545 ℃, the superheat degree delta T =10-30 ℃, the casting is carried out at a constant pulling speed of 0.9-1.3m/min, dynamic soft reduction is carried out at the solidification tail end of the sector section, the total reduction is more than or equal to 6mm, the columnar crystals of the casting blank are effectively crushed, the grains are refined in the recrystallization process, the looseness and the component segregation of the casting blank are improved, the argon protection casting is carried out in the whole process, and the external air is prevented from entering.
The production method of the steel rolling process is implemented on a Handover 2250 conventional hot continuous rolling production line, and the 2250 main rolling line equipment comprises: 4 furnaces, 2 roughing mills (i.e., R1 mill and R2 mill), 7 finishing mills (i.e., F1-F7 mill), 1 laminar cooling unit, and 3 sub-grade coilers.
The whole rolling process adopts two-stage rolling, the one-stage rolling is complete recrystallization rolling, the rough rolling adopts 3+5 passes of rolling, namely 3 passes of R1 rolling and 5 passes of R2 rolling, the equipment capability is fully exerted by utilizing the favorable conditions of the rough rolling under high temperature and high pressure, the reduction rate of the last two passes is controlled between 20 percent and 30 percent, and the accumulated reduction rate of the rough rolling is controlled between 70 percent and 85 percent, so that austenite grains are refined in the processes of repeated deformation, recrystallization and recovery. The two-stage rolling is non-recrystallization rolling, and is mainly completed in the finish rolling, the reduction rate is increased in the stage to further refine austenite grains, so that a large amount of deformation bands and dislocation are accumulated in the grains, enough nucleation points are provided for subsequent phase change, the finish rolling accumulated reduction rate is controlled to be 60-80% by considering finish rolling plate shape control and equipment capacity, and the finish rolling temperature is controlled according to 850-910 ℃.
The laminar cooling adopts sectional cooling, the laminar cooling adopts a sectional cooling mode, the first-section cooling rate is 20-50 ℃/s, the inter-cooling temperature is 630-. The main rolling process parameters of the wear-resistant steel are shown in the table 2.
TABLE 2 main rolling process parameters of wear-resistant steels
The wear-resistant steel with the thickness of 2.5-12.0mm produced according to the invention has the yield strength of 761-825MPa and the tensile strength of 1068-1215MPa, and adopts A50The elongation after gauge length breaking is 14.2-16.8%. When the bending pressure head with the thickness of 5 times is adopted in the cold bending test, no crack or fracture occurs when the temperature is 160 DEG and 180 DEG, and the cold bending performance is good. The surface Brinell hardness is in HBW 291-.
The structures of the wear-resistant steels produced by the six examples are shown in figures 1-6, and the metallographic structure is composed of three phases of ferrite, martensite and retained austenite, wherein the proportion of ferrite is 10% -20%, the proportion of martensite is 75% -90%, and the retained austenite is 1% -8%.
TABLE 3 mechanical Properties of abrasion-resistant steels
The samples of examples 1-6 were tested for abrasive wear at 0.089-0.116g/h, while comparative examples 1 (Q345B) and 2 (700L) had wear rates of 0.42g/h and 0.23g/h, respectively, as compared to Table 4. Tests show that the wear-resistant steel has better wear resistance than the traditional low-alloy high-strength steel under the same working condition.
TABLE 4 abrasion test comparison of abrasion resistant steels and Low-alloy high-strength steels
Claims (4)
1. The high Al wear-resistant steel strip with good cold forming performance is characterized in that: the weight percentage of the chemical components is as follows: 0.10 to 0.15 percent of C, 1.25 to 1.5 percent of Si, 1.50 to 2.00 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.010 percent of S, 0.51 to 0.70 percent of Als, Ti: 0.010-0.040%, N is less than or equal to 0.0045%, and the balance is Fe and inevitable residual elements, the steel strip is hot-rolled wear-resistant steel, a metallographic structure consists of three phases of ferrite, martensite and residual austenite, the thickness of the steel strip is 2.5-12.0mm, and the mechanical property is as follows: the yield strength is more than or equal to 600MPa, the tensile strength is more than or equal to 900MPa, the elongation is more than or equal to 14.0 percent, and the Brinell hardness HBW: 200-400; cold bending property: bending the pressure head by 120 degrees normally when the diameter of the pressure head is bent by 5 times; the high-Al wear-resistant steel strip is produced by the following method: comprises the production processes of continuous casting, slab heating, rolling, cooling and coiling; in the rolling procedure, 3+5 passes of rough rolling are adopted, the reduction rate of the last 2 passes is controlled to be between 20% and 30%, the accumulated reduction rate of the rough rolling is controlled to be between 70% and 85%, a heat preservation cover is used in a middle roller way, the accumulated reduction rate of the finish rolling is controlled to be between 60% and 80%, and the final rolling temperature is controlled to be 850-; in the cooling procedure, laminar cooling adopts a sectional cooling mode, the first-section cooling rate is 20-50 ℃/s, the intercooling temperature is 630-.
2. A method for producing a high Al wear resistant steel strip with good cold formability according to claim 1 comprising the production steps of continuous casting, slab heating, rolling, cooling and coiling, characterized in that: in the rolling procedure, 3+5 passes of rough rolling are adopted, the reduction rate of the last 2 passes is controlled to be between 20% and 30%, the accumulated reduction rate of the rough rolling is controlled to be between 70% and 85%, a heat preservation cover is used in a middle roller way, the accumulated reduction rate of the finish rolling is controlled to be between 60% and 80%, and the final rolling temperature is controlled to be 850-; in the cooling procedure, laminar cooling adopts a sectional cooling mode, the first-section cooling rate is 20-50 ℃/s, the intercooling temperature is 630-.
3. A method of producing a high Al wear resistant steel strip with good cold formability according to claim 2, wherein: in the slab heating process, the slab heating time is 180-.
4. A method of producing a high Al wear resistant steel strip with good cold formability according to claim 2 or 3, characterized in that: in the continuous casting process, the temperature of molten steel entering a ladle is controlled at 1505-1545 ℃, the superheat degree delta T =10-30 ℃, the casting is pulled at a constant pulling speed of 0.9-1.3m/min, the solidification tail end of the casting blank is subjected to dynamic soft reduction, and the reduction total amount is more than or equal to 6 mm; and hoisting the steel billet into the stack position surrounded by the hot billet for slow cooling within 10 minutes after the steel billet is off-line, wherein the slow cooling time is not less than 48 hours.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010238334.8A CN111334720B (en) | 2020-03-30 | 2020-03-30 | High Al wear-resistant steel strip with good cold formability and production method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010238334.8A CN111334720B (en) | 2020-03-30 | 2020-03-30 | High Al wear-resistant steel strip with good cold formability and production method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN111334720A CN111334720A (en) | 2020-06-26 |
| CN111334720B true CN111334720B (en) | 2022-03-25 |
Family
ID=71180454
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010238334.8A Active CN111334720B (en) | 2020-03-30 | 2020-03-30 | High Al wear-resistant steel strip with good cold formability and production method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111334720B (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112176256A (en) * | 2020-09-27 | 2021-01-05 | 邯郸钢铁集团有限责任公司 | High-impact-toughness automobile beam steel belt and production method thereof |
| CN112760560A (en) * | 2020-12-17 | 2021-05-07 | 包头钢铁（集团）有限责任公司 | NM300 wear-resistant steel for 1100 MPa-strength low-yield-ratio concrete mixer truck and preparation method thereof |
| CN115198188A (en) * | 2022-07-11 | 2022-10-18 | 山西太钢不锈钢股份有限公司 | Low-cost HB 400-grade double-phase wear-resistant hot-rolled coil and preparation method and application thereof |
Family Cites Families (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4917186B2 (en) * | 2009-05-11 | 2012-04-18 | 新日本製鐵株式会社 | Hot-rolled steel sheet, hot-dip galvanized steel sheet excellent in punching workability and fatigue characteristics, and manufacturing method thereof |
| EP2762592B1 (en) * | 2011-09-30 | 2018-04-25 | Nippon Steel & Sumitomo Metal Corporation | High-strength hot-dipped galvanized steel sheet and high-strength alloyed hot-dipped galvanized steel sheet, each having tensile strength of 980 mpa or more, excellent plating adhesion, excellent formability and excellent bore expanding properties, and method for producing same |
| JP2014043629A (en) * | 2012-08-28 | 2014-03-13 | Nippon Steel & Sumitomo Metal | Hot rolled steel sheet |
| JP6390249B2 (en) * | 2014-08-04 | 2018-09-19 | 新日鐵住金株式会社 | High-strength hot-rolled steel sheet with excellent hole expandability, its manufacturing method, and hole expandability evaluation method |
| CN104532126B (en) * | 2014-12-19 | 2017-06-06 | 宝山钢铁股份有限公司 | A kind of super high strength hot rolled Q＆P steel of low yield strength ratio and its manufacture method |
| MX2017015266A (en) * | 2015-06-17 | 2018-02-19 | Nippon Steel & Sumitomo Metal Corp | Steel sheet and manufacturing method. |
| WO2018115936A1 (en) * | 2016-12-21 | 2018-06-28 | Arcelormittal | Tempered and coated steel sheet having excellent formability and a method of manufacturing the same |
| WO2018115935A1 (en) * | 2016-12-21 | 2018-06-28 | Arcelormittal | Tempered and coated steel sheet having excellent formability and a method of manufacturing the same |
| JP6699711B2 (en) * | 2017-11-28 | 2020-05-27 | Ｊｆｅスチール株式会社 | High-strength steel strip manufacturing method |
| CN107881417B (en) * | 2017-11-29 | 2019-08-27 | 东北大学 | A kind of low yield strength ratio martensite-ferrite-austenite multi-phase wear-resistant steel plate and its manufacturing method |
-
2020
- 2020-03-30 CN CN202010238334.8A patent/CN111334720B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN111334720A (en) | 2020-06-26 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101768698B (en) | Low cost yield strength 700MPA level non-tempering processing high strength steel plate and manufacturing method thereof | |
| CN111996441B (en) | TiC enhanced martensite wear-resistant steel plate with high toughness and good bending performance and manufacturing method thereof | |
| CN111334720B (en) | High Al wear-resistant steel strip with good cold formability and production method thereof | |
| CN111455278A (en) | Thick hot-rolled high-strength steel plate coil with excellent low-temperature toughness and for 800MPa cold forming and manufacturing method thereof | |
| CN108929986B (en) | High-strength wear-resistant hot rolled steel plate for automobile braking and production process thereof | |
| CN104694822A (en) | High-strength hot rolled steel plate with 700 MPa grade yield strength and manufacturing method thereof | |
| CN109957712A (en) | A kind of soft X70M line steel hot rolling coiled sheet and its manufacturing method | |
| CN110684925A (en) | High-strength wear-resistant corrosion-resistant hot-rolled steel strip and production method thereof | |
| CN110106322B (en) | High-strength steel for thin engineering machinery and plate shape control method | |
| CN111424211B (en) | Weather-resistant steel for wide 700 MPa-grade hot-rolled container and manufacturing method thereof | |
| CN111607735B (en) | Hot-rolled wear-resistant steel with Brinell hardness of more than or equal to 420 and production method thereof | |
| CN112831731A (en) | Online quenching complex phase structure hot-rolled wear-resistant steel and preparation method thereof | |
| US20230125540A1 (en) | Tempering-free wear-resistant hot rolled strip and method for producing same | |
| CN112226673A (en) | Hot rolled steel plate with 650 MPa-grade tensile strength and manufacturing method thereof | |
| WO2022022040A1 (en) | Low temperature-resistant hot-rolled h-type steel for 355mpa marine engineering and preparation method therefor | |
| CN109518074A (en) | A kind of economical high tenacity 800MPa grades of beam steels and its production method | |
| WO2020108595A1 (en) | Hot-rolled high-strength steel plate with high surface quality and low yield ratio and manufacturing method therefor | |
| CN108315662A (en) | A kind of yield strength 900MPa level hot rolled steel plates and its production technology | |
| CN112795731A (en) | Cold-rolled steel plate for lampshade and production method thereof | |
| CN102418047B (en) | Non-quenched and tempered fatigue-resistant steel plate and manufacturing method thereof | |
| CN111534746B (en) | Weather-resistant steel for wide 450 MPa-grade hot-rolled container and manufacturing method thereof | |
| JP2022550329A (en) | Double phase steel with high hole expandability and method for producing the same | |
| CN114000068B (en) | Low-nitrogen ultrahigh-strength hot-rolled steel strip with thickness of 4-10mm and production method thereof | |
| CN110938771A (en) | Hot-rolled steel plate for wheel with tensile strength of 630MPa and manufacturing method thereof | |
| CN114231826A (en) | Production method of Q420qE bridge structural steel plate |
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 |