CN116516131A - High-strength steel plate and heat treatment process for improving fatigue limit of high-strength steel plate - Google Patents

High-strength steel plate and heat treatment process for improving fatigue limit of high-strength steel plate Download PDF

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Publication number
CN116516131A
CN116516131A CN202310294188.4A CN202310294188A CN116516131A CN 116516131 A CN116516131 A CN 116516131A CN 202310294188 A CN202310294188 A CN 202310294188A CN 116516131 A CN116516131 A CN 116516131A
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steel plate
strength steel
heat treatment
percent
fatigue limit
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Chinese (zh)
Inventor
贾丹
李银华
段海涛
杜宝帅
王晓明
骆小双
李辛庚
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Electric Power Research Institute of State Grid Shandong Electric Power Co Ltd
Wuhan Research Institute of Materials Protection
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Electric Power Research Institute of State Grid Shandong Electric Power Co Ltd
Wuhan Research Institute of Materials Protection
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Priority to CN202310294188.4A priority Critical patent/CN116516131A/en
Publication of CN116516131A publication Critical patent/CN116516131A/en
Pending legal-status Critical Current

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    • 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
    • C21D8/0205—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
    • C21D8/0247—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
    • C22C38/04—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
    • C22C38/18—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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials 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 discloses a high-strength steel plate and a heat treatment process for improving the fatigue limit of the high-strength steel plate, wherein the high-strength steel plate is smelted in a converter and continuously cast into a plate blank of the high-strength steel plate; then heating the slab, hot rolling to a required thickness, and then air cooling to room temperature to obtain a hot rolled steel plate; heating the steel plate to a required temperature, preserving heat for a certain time for annealing treatment, and cooling to room temperature along with a furnace; and then heating the sample from room temperature to 600+/-10 ℃ within 40+/-2 min, preserving heat for 30+/-5 min, then heating the sample from 600 ℃ to 860+/-10 ℃ within 30min, preserving heat for 30+/-5 min, then oil quenching to 580+/-10 ℃, preserving heat for 2.5h at 580+/-10 ℃, and then oil quenching to room temperature to obtain the high-strength steel plate with high fatigue ultimate strength. The invention has simple process, can greatly improve the fatigue limit of the high-strength steel plate, keeps better impact performance and effectively prolongs the service life of the alloy steel.

Description

High-strength steel plate and heat treatment process for improving fatigue limit of high-strength steel plate
Technical Field
The invention belongs to the field of inorganic materials, relates to a steel smelting technology, and in particular relates to a high-strength steel plate and a heat treatment process for improving the fatigue limit of the high-strength steel plate.
Background
Metal materials are one of the most important materials for human development, and from ancient times to date, metal materials play a great role in the life of people. The metal material has the characteristics of high toughness, high hardness strength and the like, so that the metal material is widely applied to the fields of national defense, industry, agriculture, electronic information and the like.
The heat treatment of the metal material plays a role in improving the performance of the metal material, and has the advantages of adjusting the strength, the hardness and the toughness without changing the chemical composition of the metal and improving the processability of the metal. The heat treatment process is also gradually diversified from four-bar fire.
And (3) searching: chinese patent publication No. CN114657472a discloses a marine ultra-high strength low temperature steel with excellent fatigue property and a manufacturing method thereof, comprising: 0.080 to 0.140 percent of C, 0.20 to 0.60 percent of Si, 1.15 to 1.60 percent of Mn, 0.020 to 0.050 percent of Nb, 0.040 to 0.08 percent of V, 0.30 to 0.50 percent of Cu, 0.50 to 0.80 percent of Ni, 0.014 to 0.0170 percent of N, 0.10 to 0.20 percent of Cr, less than or equal to 0.010 percent of P, less than or equal to 0.005 percent of S, 0.015 to 0.035 percent of Als, and the balance of Fe and unavoidable impurities, smelting, continuous casting, heating, rolling and cooling; the microstructure of the produced low-temperature steel is a complex phase structure of ultrafine ferrite, bainite and a small amount of martensite, the room-temperature high-cycle fatigue limit strength is more than 320MPa, the yield strength of the low-temperature steel is more than 500MPa, and the tensile strength is more than 620 MPa. The invention relates to steel materials with high fatigue performance, but does not relate to heat treatment, and the performance is not in the same level.
The patent document with the publication number of CN 114182174A discloses a production method of a high-strength and high-toughness bridge structural steel plate, which comprises, by weight, 0.03% -0.08% of C, 0.30% -0.50% of Si, 1.50% -2.00% of Mn, less than or equal to 0.015% of P, less than or equal to 0.005% of S, 0.02% -0.05% of Al, 0.008% -0.030% of Ti, 0.03% -0.08% of Nb, 0.30% -0.50% of Cr, less than or equal to 0.20% of Cu, and the balance of Fe and unavoidable impurity elements. The invention produces the steel plate through the processes of thermo-mechanical controlled rolling, multistage controlled cooling, tempering heat treatment and the like, wherein the yield strength is more than or equal to 500MPa, the tensile strength is more than or equal to 630MPa, and the conditional fatigue limit is more than or equal to 500 MPa.
Disclosure of Invention
The invention aims to provide a heat treatment process for improving the fatigue limit of a high-strength steel plate, so that the tensile strength and the fatigue strength of the steel are improved, and meanwhile, the impact toughness of the material is better. The heat treatment temperature is 650-700 ℃, the heat preservation time is 5-10 h, and the furnace cooling is carried out to the room temperature. Then carrying out thermal refining, preserving heat for 30min at 600+/-10 ℃, preserving heat for 30min at 860+/-10 ℃, cooling the oil to 580+/-10 ℃, preserving heat for 2.5h, and cooling the oil to room temperature. The tensile strength of the steel plate after heat treatment reaches 1200MPa, the fatigue limit strength reaches 510MPa, the impact energy reaches 132J, and the service life of the alloy steel is effectively prolonged.
In order to solve the technical problems, the invention adopts the following technical means:
in one aspect, the present invention provides a heat treatment process for improving the fatigue limit of a high strength steel sheet, comprising the steps of:
1) Smelting and continuously casting into a slab of a high-strength steel plate by a converter;
2) And (3) hot rolling: heating the plate blank, hot-rolling to a required thickness, and then air-cooling to room temperature to obtain a steel plate;
3) Annealing heat treatment: heating the steel plate to C1 ℃, preserving heat for a period of time, performing annealing treatment, and cooling to room temperature along with a furnace;
4) Tempering heat treatment: and heating the annealed steel plate from room temperature to B1 ℃ in the time of A1 minutes, preserving heat for A2 minutes, heating the steel plate from B1 ℃ to B2 ℃ in the time of A3 minutes, preserving heat for A4 minutes, then oil quenching to B3 ℃, preserving heat for A5 hours at B3 ℃, and oil quenching to room temperature to obtain the high-strength steel plate with high fatigue limit.
As a preferable technical scheme, in step 1), the slab comprises the following components in percentage by weight:
c:0.25 to 0.35 percent, si:0.10 to 0.40 percent, mn:0.5 to 0.8 percent, ni:1.8 to 2.2 percent, mo:0.3 to 0.5 percent, cr:1.8 to 2.2 percent of Ti:0.010 to 0.020 percent, P is less than or equal to 0.020 percent, S is less than or equal to 0.0020 percent, and the balance is iron and unavoidable impurities.
As a preferable technical scheme, in step 1), the thickness of the slab is not less than 200mm.
As a preferable technical scheme, in the step 2), the heating temperature of the plate blank is 1150-1200 ℃.
As a preferable technical scheme, in the step 3), the value range of the annealing treatment heat preservation temperature C1 is 650-700, and the heat preservation time is 5-10 hours.
As a preferred technical solution, in step 4), the value ranges of A1, A2, A3, A4 and A5 are respectively: 35-45, 25-35, 26-33, 25-35, 2-3; the value ranges of B1, B2 and B3 are respectively as follows: 590-610, 850-870, 570-590.
In another aspect, the present invention provides a high strength steel sheet having a high fatigue limit strength, obtained by using any one of the heat treatment processes described above.
The high-strength steel plate has the following functions:
c: carbon is a critical element affecting cast steel strength, hardness, toughness, hardenability, and wear resistance. The high-carbon martensite formed after heat treatment has high hardness but low toughness, and cracks are easy to form during heat treatment, and the high-carbon martensite has low carbon content, low hardness and poor wear resistance.
Si: silicon does not form carbides in steel but exists in ferrite or austenite in the form of a solid solution. It can raise the strength of solid solution in steel and avoid the plastic and toughness of steel plate from deteriorating obviously.
Mn: the manganese element can improve the strength and hardness of the steel and obviously improve the hardenability. But at high contents, the low temperature toughness of the steel will be reduced.
Ti: titanium is a strong N element, and fine TiN particles can effectively prevent austenite grains from growing up when a slab is reheated, and can improve the impact toughness of a welding heat affected zone.
Mo: fine grains of steel, improved hardenability and heat strength, and sufficient strength and creep resistance at high temperatures. The red hardness can be improved and the temper brittleness can be inhibited in tool steel.
Ni: nickel can effectively improve the hardenability of steel, has a certain solid solution strengthening effect, can obviously improve the low-temperature toughness of steel, and the addition of Ni can improve the hot brittleness and is beneficial to the toughness.
Cr: chromium is a medium strength carbide forming element. The strength, hardness and wear resistance are significantly improved, but the plasticity and toughness are reduced at the same time. Can improve the oxidation resistance and corrosion resistance of steel. The temperatures of A3 and A1 are raised and the GS line moves to the upper left.
P: phosphorus is a harmful element in steel, and when the phosphorus content in the steel is excessive, the tempering brittleness and cold brittleness of the material are increased, namely, the impact toughness is reduced, and the brittle transition temperature is increased. In low alloy steels and austenitic steels with higher carbon content, phosphorus also promotes the generation of hot cracks, so that the content of phosphorus should be reduced as much as possible, and the content is controlled to be less than or equal to 0.020% for cost consideration.
S: sulfur is a harmful element in steel, and increases hot brittleness of the steel, and exists in the form of sulfide inclusions in the steel, which has adverse effects on plasticity, toughness, welding performance, thickness direction performance, fatigue performance and corrosion resistance of the steel, so that the content of the sulfur is reduced as much as possible and controlled to be less than or equal to 0.0020%.
The invention reasonably configures the contents of Ni, mo and Cr elements, increases the stability of supercooled austenite through Mo element, inhibits the diffusion and transformation of iron and carbon atoms, and delays gamma Fe →α Fe Phase transition; cr element reduces the bainite transformation starting temperature of the steel, so that the bainite transformation is performed at a lower temperature; the Ni element prolongs the transformation incubation period of pearlite, reduces the nucleation rate and the growth rate of the pearlite, delays and even inhibits the combined action of the pearlite transformation, and reduces the critical cooling rate of martensite transformation, thereby effectively improving the hardenability of steel and reducing the high-temperature tempering brittleness of the steel.
The invention aims to ensure that the steel plate is under high pressure at high temperature of hot rolling by controlling the thickness of the plate blank to be not less than 200mm, so that grains are fully crushed.
The invention designs annealing treatment after hot rolling and keeps the temperature for a long time, so as to eliminate tissue defects, thin and uniform the tissue, reduce internal stress, improve the plasticity and toughness of steel pieces, and prepare for subsequent quenching and tempering.
The method is characterized in that the temperature difference of the test piece is reduced by heating to about 600 ℃ and preserving heat for a certain time in the tempering stage, so that the phase change is prepared for the phase change, the phase change is uniformly carried out on the whole section of the test piece instead of directly heating to the quenching temperature, and the generation of larger tissue stress can be avoided.
The temperature is controlled to 860+/-10 ℃ and kept for 30+/-5 min, because austenite nucleation, growth, dissolution of carbide and homogenization of components will occur at the temperature, the processes are diffusion migration of iron, carbon and alloy elements, so that a certain time is required, in the initial stage, austenite crystal nuclei are firstly formed at the interface of ferrite and cementite, and are diffused under the gradient of carbon concentration, so that the austenite growth is promoted, the process is more complete when the time is longer, but the temperature is longer, austenite crystal grains can grow, the performance of steel is adversely affected, and in the invention, the grain size is controlled to prepare for subsequent rapid cooling by controlling the alloy elements and the temperature.
The oil quenching is selected because the cooling speed of the oil quenching is mild relative to the water quenching, so that the test piece is not easy to crack and deform.
The tempering is carried out for 2.5 hours at 580+/-10 ℃ so as to obtain tempered sorbite with high-temperature tempered structure, and the toughness and the coordination of the steel plate can be adjusted so as to obtain good comprehensive mechanical properties.
The invention ensures the purity of the steel billet through the design of lower S, P content, and simultaneously ensures the basic performance of the steel billet by matching with alloy elements with proper content, and the designed long-time annealing process avoids the problems of uneven strength, unmatched toughness, cracking and the like caused by the structural defects (segregation, cracks, coarse structure and the like) caused by directly carrying out the quenching and tempering after rolling. Heating to a certain temperature and preserving heat for a certain time after annealing, successfully avoids the problem that the surface is transformed into austenite after being heated too fast, and the transformation products are inconsistent due to inconsistent structure caused by the fact that the core is also pearlite and ferrite structure. After sufficient tissue preparation, quenching and tempering are carried out, carbon segregation in martensite, martensite decomposition, transformation of residual austenite, transformation of carbide, aggregation length of cementite and a-phase recovery and recrystallization are carried out, and the residual internal stress of the test steel is also continuously eliminated. Obtaining tempered sorbite tissue with good strength and toughness. The process effectively solves the problems of low strength or over-high strength, poor toughness, low fatigue strength and part failure caused by uneven structure when the high alloy structural steel is used as a part. The invention has simple components and common hot rolling process, and effectively improves the comprehensive performance of the steel plate.
Drawings
FIG. 1 is a flow chart of a heat treatment process for improving the fatigue limit in an embodiment of the invention.
Detailed Description
The present invention will be described in detail below:
table 1 is a list of values for each example and comparative example of the present invention;
table 2 is a list of the main process parameters for each example and comparative example of the present invention;
table 3 shows a list of performance tests for each example and comparative example of the present invention.
The embodiments of the invention are produced according to the following steps:
the method comprises the following steps:
1) Smelting in a converter and continuously casting into a plate blank with the thickness not less than 200 mm;
2) And (3) hot rolling: heating a casting blank to 1150-1200 ℃ for rolling: rolling the steel plate to a required thickness; then air cooling to room temperature;
3) Annealing heat treatment: the temperature is controlled between 650 and 700 ℃, the heat preservation time is 5 to 10 hours, and the furnace cooling is carried out to the room temperature;
4) Tempering heat treatment: heating the sample from room temperature to 600+/-10 ℃ within 40+/-2 min, preserving heat for 30+/-5 min, then heating the sample from 600 ℃ to 860+/-10 ℃ within 30min, preserving heat for 30+/-5 min, then quenching oil to 580+/-10 ℃, preserving heat for 2.5h at 580+/-10 ℃, and quenching oil to room temperature to obtain the high-strength steel plate with high fatigue limit strength.
TABLE 1 chemical composition (wt%) of each example and comparative example of the present invention
Implementation of the embodiments Thickness of (L) C Si Mn P S Cr Ti Mo Ni
Example(s) mm
1 12.5 0.25 0.30 0.6 0.011 0.0010 2.2 0.010 0.30 1.9
2 14.0 0.28 0.22 0.68 0.010 0.0020 1.9 0.011 0.35 2.0
3 18.0 0.30 0.33 0.65 0.015 0.0010 2.0 0.010 0.45 2.0
4 26.0 0.32 0.40 0.56 0.020 0.0011 1.8 0.015 0.50 1.8
5 30.0 0.35 0.33 0.80 0.010 0.0015 2.0 0.020 0.40 2.2
Comparative 1 14.0 0.25 0.22 0.68 0.010 0.0020 2.5 0.002 0.35 2.5
Comparative example 2 28.0 0.35 0.40 0.55 0.010 0.0011 2.0 0.011 0.45 1.8
TABLE 2 list of the main process parameters for each example and comparative example of the present invention
TABLE 3 Performance results list for various examples and comparative examples of the present invention
As can be seen from table 3: the 5 steel sheets produced in examples 1 to 5 were superior to those without the two processes in terms of fatigue limit and impact properties of the steel sheets subjected to the long-time annealing treatment and the quenching stage heating.
The above embodiments are only for illustrating the present invention, and are not limiting of the present invention. While the invention has been described in detail with reference to the embodiments, those skilled in the art will appreciate that various combinations, modifications, and substitutions can be made thereto without departing from the spirit and scope of the invention as defined in the appended claims.

Claims (7)

1. A heat treatment process for improving the fatigue limit of a high-strength steel plate, which is characterized by comprising the following steps of:
1) Smelting and continuously casting into a slab of a high-strength steel plate by a converter;
2) And (3) hot rolling: heating the slab, hot-rolling to a required thickness, and then air-cooling to room temperature to obtain a steel plate;
3) Annealing heat treatment: heating the steel plate to C1 ℃, preserving heat for a period of time, performing annealing treatment, and cooling to room temperature along with a furnace;
4) Tempering heat treatment: and heating the annealed steel plate from room temperature to E1 ℃ in the time of D1 min, preserving heat for D2 min, heating the steel plate from E1 ℃ to E2 ℃ in the time of D3 min, preserving heat for D4 min, then oil quenching to E3 ℃, preserving heat for D5 h at E3 ℃, and oil quenching to room temperature to obtain the high-strength steel plate with high fatigue limit.
2. The heat treatment process for improving the fatigue limit of a high-strength steel sheet according to claim 1, wherein: in the step 1), the slab comprises the following components in percentage by weight:
c:0.25 to 0.35 percent, si:0.10 to 0.40 percent, mn:0.5 to 0.8 percent, ni:1.8 to 2.2 percent, mo:0.3 to 0.5 percent, cr:1.8 to 2.2 percent of Ti:0.010 to 0.020 percent, P is less than or equal to 0.020 percent, S is less than or equal to 0.0020 percent, and the balance is iron and unavoidable impurities.
3. The heat treatment process for improving the fatigue limit of a high-strength steel sheet according to claim 2, wherein: in the step 1), the thickness of the plate blank is not less than 200mm.
4. The heat treatment process for improving the fatigue limit of a high-strength steel sheet according to claim 2, wherein: in the step 2), the heating temperature of the plate blank is 1150-1200 ℃.
5. The heat treatment process for improving the fatigue limit of a high-strength steel sheet according to claim 2, wherein: in the step 3), the value range of the annealing treatment heat preservation temperature C1 is 650-700, and the heat preservation time is 5-10 hours.
6. The heat treatment process for improving the fatigue limit of a high-strength steel sheet according to claim 2, wherein: in the step 4), the value ranges of D1, D2, D3, D4 and D5 are respectively as follows: 35-45, 25-35, 26-33, 25-35, 2-3; the value ranges of E1, E2 and E3 are respectively as follows: 590-610, 850-870, 570-590.
7. A high strength steel sheet having a high fatigue limit strength, which is obtained by the heat treatment process according to any one of claims 1 to 6.
CN202310294188.4A 2023-03-23 2023-03-23 High-strength steel plate and heat treatment process for improving fatigue limit of high-strength steel plate Pending CN116516131A (en)

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