CN114855098A - High-strength medium manganese steel for engineering machinery and preparation method thereof - Google Patents

High-strength medium manganese steel for engineering machinery and preparation method thereof Download PDF

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Publication number
CN114855098A
CN114855098A CN202210429563.7A CN202210429563A CN114855098A CN 114855098 A CN114855098 A CN 114855098A CN 202210429563 A CN202210429563 A CN 202210429563A CN 114855098 A CN114855098 A CN 114855098A
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steel
cooling
strength
preparation
engineering machinery
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董营
杜林秀
高秀华
吴红艳
高彩茹
孙超
段东明
李东晖
陶振
刘韬
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Northeastern University China
Nanjing Iron and Steel Co Ltd
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Northeastern University China
Nanjing Iron and Steel Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0242—Flattening; Dressing; Flexing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • 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
    • C22C38/06—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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C21D2211/001—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
    • C21D2211/008—Martensite

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The invention belongs to the technical field of metal materials, and particularly relates to high-strength medium manganese steel for engineering machinery and a preparation method thereof. The technical scheme of the invention is as follows: a high-strength medium manganese steel for engineering machinery comprises the following chemical components in percentage by weight: c: 0.05-0.1%, Mn: 4.5-7.0%, Si: 0.6-1.0%, Al: 0.05-0.3%, Cr: 0.15 to 0.40%, Ni: 0.10 to 0.20%, Mo: 0.20-0.50%, Cu + B: 0.15-0.55%, S: < 0.006%, P: less than 0.01 percent, and the balance of Fe and other inevitable impurities. The high-strength medium manganese steel for engineering machinery and the preparation method thereof provided by the invention can regulate and control the characteristics of original austenite, the phase transformation in the cooling process and the internal state of a martensite structure, and realize the short-flow preparation with controllable steel plate yield ratio on the premise of ensuring high strength.

Description

High-strength medium manganese steel for engineering machinery and preparation method thereof
Technical Field
The invention belongs to the technical field of metal materials, and particularly relates to high-strength medium manganese steel for engineering machinery and a preparation method thereof.
Background
Engineering equipment is generally used in relatively complicated and variable environments, the operation objects and conditions of the engineering equipment have particularity, products of the engineering equipment are also in trend of large-scale, light-weight, heavy load and the like, and therefore, the requirements on the performances of the steel for the engineering machinery, such as hardness, toughness, weldability and the like, are high. The development of steel for engineering machinery in China is late, and in recent 30 years, with the development of a thermal machinery control theory and the introduction of an engineering machinery manufacturing technology, the steel for engineering machinery gradually replaces low-grade engineering steel mainly comprising Q235 and 16Mn and gradually meets international rails. However, the steel for high-strength engineering equipment in China still cannot meet the requirements, and particularly, special steel in the aspect of large-scale equipment core components still needs to be imported for a long time, so that the development of the domestic engineering machinery industry is restricted.
At present, the traditional high-strength steel for engineering machinery is prepared by microalloying and quenching and tempering, and the performance requirements of Q690 and above are met by precipitation strengthening, fine grain strengthening, phase change strengthening and the like. However, because a large amount of alloy elements are required to be added into the material, and the carbon content is relatively high, the welding difficulty and the preparation cost are increased, and meanwhile, the corresponding heat treatment process is relatively complex, and the production efficiency and the additional value are reduced.
Disclosure of Invention
The invention provides high-strength medium manganese steel for engineering machinery and a preparation method thereof, which can regulate and control the characteristics of original austenite, phase transformation in the cooling process and the internal state of a martensite structure and realize the short-flow preparation with controllable steel plate yield ratio on the premise of ensuring high strength.
The technical scheme of the invention is as follows:
a high-strength medium manganese steel for engineering machinery comprises the following chemical components in percentage by weight: c: 0.05-0.1%, Mn: 4.5-7.0%, Si: 0.6-1.0%, Al: 0.05-0.3%, Cr: 0.15-0.40%, Ni: 0.10-0.20%, Mo: 0.20-0.50%, Cu + B: 0.15-0.55%, S: < 0.006%, P: less than 0.01 percent, and the balance of Fe and other inevitable impurities.
The preparation method of the high-strength medium manganese steel for the engineering machinery comprises the following steps:
step 1, heating and hot rolling of steel billets:
forging the ingot of the chemical composition into a steel billet with a specified thickness, heating the steel billet to 1100-1250 ℃ along with a furnace, and preserving heat for 1-3 hours to homogenize elements of the steel billet; then air-cooling to a rolling temperature, and hot-rolling the heated steel billet for 7-13 times to a steel plate with a target thickness of 4-16 mm, wherein the total rolling reduction rate is 84-96%, and the final rolling temperature is controlled to be 750-950 ℃;
and step 2, controlling cooling:
cooling the hot-rolled steel plate to 650-300 ℃ at the speed of 5-30 ℃/s, then curling, and slowly cooling to room temperature; finally, lath martensite and film-shaped retained austenite complex phase structure are obtained.
Further, according to the preparation method, the thickness of the steel billet is 100 mm.
Further, according to the preparation method, the single-pass reduction rate is 10-25%.
Further, in the preparation method, in the step 2, the average cooling speed of the curled steel coil in the cooling process from 650 ℃ to 350 ℃ is less than 1.3 ℃/min, and the average cooling speed in the cooling process from 350 ℃ to room temperature is less than 0.1 ℃/min.
Further, in the preparation method, the microstructure of the steel plate is lath martensite and residual austenite.
Further, according to the preparation method, the yield strength of the steel plate is 690-910 MPa, the tensile strength is 1100-1250 MPa, the Vickers hardness is 330-380 HV, the elongation is 15% -20%, and the impact energy of a sample with the thickness of 2.5mm is more than 20J when the sample is tested at-40 ℃.
The invention has the beneficial effects that:
1. the cost is low. The process adopts the waste heat after rolling for heat treatment, and does not need to add an additional heat treatment process, thereby effectively reducing the energy consumption and improving the additional value of the steel plate. In addition, the low-cost C, Mn element is used as a main component, the dosage of the alloy element is reasonably controlled, and the production cost is lower than that of other products of the same grade.
2. The steel plate has excellent comprehensive performance and can realize controllable yield ratio under the condition of high tensile strength of more than 1.1 GPa. Mn element obviously expands an austenite phase region, improves the hardenability of the material, and leads the material to only have martensite transformation under the slow cooling of 0.1 ℃/min to obtain a high-strength martensite matrix and a proper amount of retained austenite structure. The material has the excellent mechanical properties of yield strength of 690-910 MPa, tensile strength of 1150-1250 MPa, and impact energy of a sample with the thickness of 2.5mm of more than 20J tested at-40 ℃.
3. The steel plate is simple in preparation process, wide in process window and easy to realize industrialization. By combining the phase change characteristics, the material can realize the curling of the hot rolled steel plate in a wider temperature range of 300-650 ℃ and a wider cooling speed range of 5-30 ℃/s, and is easy to control in industrial fields.
4. The high-temperature curling process can obviously reduce the curling difficulty of the medium plate, improve the internal stress inside the tissue and effectively reduce the straightening difficulty in the use process of the product.
5. In the slow cooling process, supersaturated carbon elements in the transformed martensite are diffused into untransformed austenite, so that the thermal stability of the transformed martensite is remarkably improved, part of austenite can be stabilized to room temperature, and finally a lath martensite matrix and a proper amount of residual austenite tissues are obtained. In the plastic deformation process, the martensite provides high strength, the residual austenite is induced by stress/strain to generate martensite transformation, and the stress concentration is effectively relaxed, so that the work hardening capacity of the material is greatly improved, and the excellent mechanical property matched with the high-strength ductility and toughness is obtained.
Drawings
FIG. 1 is a schematic view of a production process;
FIG. 2 is a metallographic structure chart of the experimental steel in example 2;
FIG. 3 is an SEM structural view of the experimental steel in example 3;
FIG. 4 is a TEM structural view of the experimental steel in example 3.
Detailed Description
The equipment for observing the metallographic structure in the embodiment of the invention is a come DMIRM-2500M metallographic microscope;
the equipment for observing the SEM tissue in the embodiment of the invention is a Zeiss Ultra55 scanning electron microscope;
the equipment for observing TEM tissues in the embodiment of the invention is Tecnai G of FEI company 2 F20 field emission transmission electron microscope.
Example 1
The high-strength medium manganese steel plate for the engineering machinery with the thickness of 16mm is prepared by the following process steps:
step 1: heating and hot rolling of steel billets:
the steel billet comprises the following chemical components in percentage by weight: 0.08% of C, Mn: 7.0%, Si: 0.75%, Al: 0.20%, Cr: 0.32%, Ni: 0.16%, Mo: 0.38%, Cu + B: 0.15%, S: 0.005%, P: 0.01%, and the balance of Fe and other unavoidable impurities. Heating the billet steel to 1100 ℃ along with the furnace, and preserving heat for 3 h; then hot rolling is carried out for 7 times to reach the target thickness of 16mm, and the total rolling reduction rate is 84%; the finishing temperature was 860 ℃.
Step 2: and (3) controlling cooling:
the hot rolled steel sheet was cooled to 650 ℃ at a rate of 5 ℃/s, followed by coiling and slow cooling to room temperature. Finally, lath martensite and film-shaped retained austenite complex phase structure are obtained.
The mechanical property of the experimental steel is detected, the yield strength of the experimental steel is 690MPa, the tensile strength is 1150MPa, the Vickers hardness is 330HV, the elongation is 20%, and the impact energy of a sample with the thickness of 2.5mm is 27J measured at minus 40 ℃.
Example 2
The high-strength medium manganese steel plate for the engineering machinery with the thickness of 10mm is prepared by the following process steps:
step 1: heating and hot rolling of steel billets:
the steel billet comprises the following chemical components in percentage by weight: 0.05% of C, Mn: 5.5%, Si: 0.60%, Al: 0.05%, Cr: 0.40%, Ni: 0.20%, Mo: 0.20%, Cu + B: 0.34%, S: 0.006%, P: 0.008% and the balance of Fe and other inevitable impurities. Heating the billet steel to 1200 ℃ along with the furnace, and preserving heat for 2 h; then hot rolling is carried out for 9 times to reach the target thickness of 10mm, and the total rolling reduction rate is 90%; the finishing temperature was 950 ℃.
Step 2: and (3) controlling cooling:
the hot rolled steel sheet was cooled to 450 ℃ at a rate of 20 ℃/s, followed by coiling and slow cooling to room temperature. Finally, lath martensite and film-shaped retained austenite complex phase structure are obtained. As shown in fig. 2, it can be seen that the prior austenite exhibits a typical equiaxed recrystallized morphology, resulting in a fine lath martensite matrix.
The mechanical property of the experimental steel is detected, the yield strength of the experimental steel is 850MPa, the tensile strength is 1180MPa, the Vickers hardness is 365HV, the elongation is 18 percent, and the impact energy of a sample with the thickness of 2.5mm is tested at minus 40 ℃ to be 24J.
Example 3
The preparation method of the high-strength medium manganese steel plate for the engineering machinery with the thickness of 4mm comprises the following process steps:
step 1: heating and hot rolling of steel billets:
the steel billet comprises the following chemical components in percentage by weight: 0.1% of C, Mn: 4.5%, Si: 1.0%, Al: 0.3%, Cr: 0.15%, Ni: 0.10%, Mo: 0.50%, Cu + B: 0.55%, S: 0.004%, P: 0.007% and the balance of Fe and other inevitable impurities. Heating the billet to 1250 ℃ along with the furnace, and preserving heat for 1 h; then hot rolling is carried out for 11 times to reach the target thickness of 4mm, and the total rolling reduction rate is 96%; the finishing temperature was 750 ℃.
Step 2: and (3) controlling cooling:
the hot rolled steel sheet was cooled to 300 ℃ at a rate of 30 ℃/s, followed by coiling and slow cooling to room temperature. Finally, lath martensite and film-shaped retained austenite complex phase structure are obtained. As shown in fig. 3 and 4, in the low-temperature rolling, the prior austenite presents a typical flat deformation type shape, and fine lath martensite and a proper amount of residual austenite structure are obtained.
The mechanical property of the experimental steel is detected, the yield strength of the experimental steel is 910MPa, the tensile strength is 1250MPa, the Vickers hardness is 380HV, the elongation is 15 percent, and the impact energy of a sample with the thickness of 2.5mm is measured at minus 40 ℃ to be 20J.

Claims (7)

1. The high-strength medium manganese steel for engineering machinery is characterized by comprising the following chemical components in percentage by weight: c: 0.05-0.1%, Mn: 4.5-7.0%, Si: 0.6-1.0%, Al: 0.05-0.3%, Cr: 0.15-0.40%, Ni: 0.10-0.20%, Mo: 0.20 to 0.50%, Cu + B: 0.15-0.55%, S: < 0.006%, P: less than 0.01 percent, and the balance of Fe and other inevitable impurities.
2. The method for preparing high-strength medium manganese steel for construction machinery according to claim 1, comprising the steps of:
step 1, heating and hot rolling of steel billets:
forging the ingot of the chemical composition into a steel billet with a specified thickness, heating the steel billet to 1100-1250 ℃ along with a furnace, and preserving heat for 1-3 hours to homogenize elements of the steel billet; then air-cooling to a rolling temperature, and hot-rolling the heated steel billet for 7-13 times to a steel plate with a target thickness of 4-16 mm, wherein the total rolling reduction rate is 84-96%, and the final rolling temperature is controlled to be 750-950 ℃;
and step 2, controlling cooling:
cooling the hot-rolled steel plate to 650-300 ℃ at the speed of 5-30 ℃/s, then curling, and slowly cooling to room temperature; finally, lath martensite and film-shaped retained austenite complex phase structure are obtained.
3. The method of claim 2 wherein said steel slab has a thickness of 100 mm.
4. The method according to claim 2, wherein the single-pass reduction ratio is 10 to 25%.
5. The method as claimed in claim 2, wherein in the step 2, the average cooling rate of the coiled steel coil is less than 1.3 ℃/min during the cooling process from 650 ℃ to 350 ℃, and the average cooling rate is less than 0.1 ℃/min during the cooling process from 350 ℃ to room temperature.
6. The method according to claim 2, wherein the microstructure of the steel sheet is lath martensite and retained austenite.
7. The preparation method according to claim 2, wherein the steel plate has a yield strength of 690-910 MPa, a tensile strength of 1100-1250 MPa, a Vickers hardness of 330-380 HV, an elongation of 15-20%, and an impact energy of a 2.5mm thick sample of more than 20J measured at-40 ℃.
CN202210429563.7A 2022-04-22 2022-04-22 High-strength medium manganese steel for engineering machinery and preparation method thereof Pending CN114855098A (en)

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