CN114892072A - High-strength high-toughness hydrogen-embrittlement-resistant steel plate and component optimization and preparation method thereof - Google Patents
High-strength high-toughness hydrogen-embrittlement-resistant steel plate and component optimization and preparation method thereof Download PDFInfo
- Publication number
- CN114892072A CN114892072A CN202210369916.9A CN202210369916A CN114892072A CN 114892072 A CN114892072 A CN 114892072A CN 202210369916 A CN202210369916 A CN 202210369916A CN 114892072 A CN114892072 A CN 114892072A
- Authority
- CN
- China
- Prior art keywords
- steel plate
- hydrogen
- toughness
- temperature
- strength
- 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.)
- Granted
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- G—PHYSICS
- G16—INFORMATION AND COMMUNICATION TECHNOLOGY [ICT] SPECIALLY ADAPTED FOR SPECIFIC APPLICATION FIELDS
- G16C—COMPUTATIONAL CHEMISTRY; CHEMOINFORMATICS; COMPUTATIONAL MATERIALS SCIENCE
- G16C60/00—Computational materials science, i.e. ICT specially adapted for investigating the physical or chemical properties of materials or phenomena associated with their design, synthesis, processing, characterisation or utilisation
-
- 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
Landscapes
- 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)
- Computing Systems (AREA)
- Theoretical Computer Science (AREA)
- Life Sciences & Earth Sciences (AREA)
- Bioinformatics & Cheminformatics (AREA)
- Bioinformatics & Computational Biology (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses a high-strength high-toughness hydrogen embrittlement-resistant steel plate and a component optimization and preparation method thereof, wherein the steel plate comprises the following chemical components in percentage by mass: c: 0.089-0.108%, Si: 0.067-0.080%, Mn: 0.84-1.05%, Cr: 0.37-0.57%, Ni: 2.10-2.42%, Cu: 0.87 to 1.09%, Mo: 0.52-0.60%, Nb: 0.043-0.056%, and the balance of Fe and inevitable impurities. The quenching temperature of the steel plate is 850-870 ℃, and the tempering temperature is 500-580 ℃. The invention solves the problems that on the premise of controlling cost and ensuring weldability, how to select proper target components to realize high strength with yield strength not lower than 1000MPa and high low-temperature toughness with impact power not lower than 69J at-40 ℃ and hydrogen embrittlement sensitivity less than 20 percent under the process conditions of quenching and high-temperature tempering. The invention can accelerate the development of novel steel materials with high strength, high and low temperature toughness and good hydrogen embrittlement resistance, and has great significance for engineering construction.
Description
Technical Field
The invention relates to a novel high-strength high-toughness hydrogen embrittlement-resistant steel plate and a component optimization and preparation method thereof, and belongs to the technical field of high-strength steel plates.
Background
With the gradual development of large-scale and light-weight engineering equipment, the strength grade of the adopted steel is correspondingly improved. The ultra-high strength steel with the yield strength of 1000MPa grade is adopted to manufacture equipment components of beam structures of engineering machinery, automobile bodies, ocean engineering and the like, and the requirements on the strength can be met, the self weight of the equipment can be reduced, the fuel consumption is reduced, and the working efficiency is improved. Meanwhile, the wall thickness of the steel is reduced, so that the welding difficulty is reduced, the welding efficiency is improved, the center of gravity of the steel structure can be moved downwards, and the safety is improved. The toughness is taken as the comprehensive performance of strength and plasticity, the capability of absorbing deformation of the material in the deformation process is reflected, wherein the impact toughness reflects the resistance of the material to external impact load, and the high impact toughness can prolong the service life of the steel structure in a low-temperature environment.
At present, enterprises for producing high-strength steel plates with yield strength of 1000MPa level in China are gradually increased, and the adopted components and processes are different. But usually, a small amount of micro-alloy elements such as Nb, V, Ti and the like are added on the basis of the carbon steel, and an optimized controlled rolling and controlled cooling process (TMCP technology) and a quenching and tempering process are combined, so that the ultrahigh-strength steel plate meeting the requirements can be produced. Patent documents CN104561827A and CN102560274A disclose high strength steel sheets with a yield strength of 1000MPa grade and a method for manufacturing the same, which use a reheating quenching and tempering process, but the steel sheets have low toughness and poor toughness matching. Patent documents CN106086657A and CN104532156A disclose ultrahigh strength steels with yield strengths greater than 1300MPa, in which the carbon contents respectively reach 0.18 to 0.23% and 0.21 to 0.26%, and the high carbon content increases the welding crack sensitivity of the ultrahigh strength steel, increases the welding cold crack tendency, and increases the welding difficulty.
Due to the harsh use environment and stress conditions of the ultrahigh-strength steel, besides high strength and high toughness, good hydrogen embrittlement resistance is also an important factor influencing the wide application of the high-strength steel, and particularly, the high-strength steel with the yield strength of 1000MPa is very easy to generate hydrogen-induced delayed fracture even under the condition of low hydrogen content, thereby causing serious threats to the safety and reliability of an engineering structure. From production manufacturing to service, hydrogen atoms are ubiquitous, and therefore, strict hydrogen embrittlement sensitivity assessment of high-strength steel is of great importance. The related technical literature for searching steel types with similar strength levels discovers that the high-strength steel reported at present is limited to strong plasticity, and corresponding hydrogen embrittlement sensitivity evaluation is not carried out, so that the service safety cannot be accurately ensured. Therefore, the accelerated development of new steel materials with high strength, high and low temperature toughness and good hydrogen embrittlement resistance is of great significance for engineering construction, and becomes a technical problem to be solved urgently.
Disclosure of Invention
In order to solve the problems of the prior art, the invention aims to overcome the defects of the prior art, and provides a high-strength high-toughness hydrogen embrittlement-resistant steel plate, and a component optimization and preparation method thereof, so that the problems of high strength with yield strength not lower than 1000MPa, high low-temperature toughness with impact power not lower than 69J at-40 ℃ and hydrogen embrittlement sensitivity not higher than 20% under the process conditions of quenching and high-temperature tempering by selecting appropriate target components on the premise of controlling cost and ensuring weldability are solved. The invention improves the comprehensive performance of the high-strength high-toughness hydrogen embrittlement-resistant steel plate and realizes the short-period research and development of novel high-strength high-toughness hydrogen embrittlement-resistant steel plate materials.
In order to achieve the purpose of the invention, the invention adopts the following technical scheme:
the high-strength high-toughness hydrogen-embrittlement-resistant steel plate comprises the following main components in percentage by mass:
c: 0.089-0.110%, Si: 0.06-0.08%, Mn: 0.80-1.10%, Cr: 0.35-0.60%, Ni: 2.0-2.50%, Cu: 0.85-1.10%, Mo: 0.50-0.60%, Nb: 0.04-0.06%, and the balance of Fe and inevitable impurities; preparing a cast ingot by adopting a smelting process, and then carrying out hot rolling, quenching and high-temperature tempering heat treatment; when hot rolling is carried out, rolling the steel plate to a thickness of not more than 14mm through multiple hot rolling, controlling the initial rolling temperature to be 1150-1200 ℃, and controlling the final rolling temperature to be 950-1000 ℃; and during heat treatment, controlling the quenching temperature to be 850-870 ℃, cooling to room temperature after quenching, then controlling the tempering temperature to be 500-580 ℃, carrying out tempering heat treatment, and then air-cooling to room temperature to obtain the high-strength high-toughness hydrogen-embrittlement-resistant steel plate.
Preferably, the high-strength high-toughness hydrogen-embrittlement-resistant steel plate comprises the following main components in percentage by mass:
c: 0.089-0.108%, Si: 0.067-0.080%, Mn: 0.84-1.05%, Cr: 0.37-0.57%, Ni: 2.10-2.42%, Cu: 0.87 to 1.09%, Mo: 0.52-0.60%, Nb: 0.043-0.056%, and the balance of Fe and inevitable impurities.
Preferably, the yield strength of the high-strength high-toughness hydrogen-embrittlement-resistant steel plate is not lower than 1000MPa, the tensile strength is not lower than 1000MPa, the elongation is not lower than 15%, the impact toughness at minus 40 ℃ is not lower than 69J, and the hydrogen-embrittlement sensitivity index HEI is not higher than 20%.
Further preferably, the yield strength of the high-strength high-toughness hydrogen embrittlement-resistant steel plate is not less than 1042MPa, the tensile strength is not less than 1079MPa, the elongation is not less than 15.8%, the impact toughness at-40 ℃ is not less than 82J, and the hydrogen embrittlement sensitivity index HEI is not more than 15.4%.
The invention relates to a preparation method of a high-strength high-toughness hydrogen embrittlement-resistant steel plate, which is characterized in that a smelting process is adopted to prepare an ingot, and then hot rolling, quenching and high-temperature tempering heat treatment are carried out; when hot rolling is carried out, rolling the steel plate to a thickness of not more than 14mm through multiple hot rolling, controlling the initial rolling temperature to be 1150-1200 ℃, and controlling the final rolling temperature to be 950-1000 ℃; during heat treatment, controlling the quenching temperature to be 850-870 ℃, cooling to room temperature after quenching, then controlling the tempering temperature to be 500-580 ℃, carrying out tempering heat treatment, and then air-cooling to room temperature to obtain the high-strength high-toughness hydrogen-embrittlement-resistant steel plate;
the prepared high-strength high-toughness hydrogen-embrittlement-resistant steel plate mainly comprises the following chemical components in parts by weight:
c: 0.089-0.110%, Si: 0.06-0.08%, Mn: 0.80-1.10%, Cr: 0.35-0.60%, Ni: 2.0-2.50%, Cu: 0.85-1.10%, Mo: 0.50-0.60%, Nb: 0.04-0.06%, and the balance of Fe and inevitable impurities.
Preferably, the smelting process adopts a vacuum induction smelting furnace for smelting, then an ingot is prepared, the ingot is cut into steel blocks with the thickness of not less than 40mm, and the steel blocks are used as hot rolled steel.
Preferably, the heat treatment process comprises the steps of heating the hot rolled steel plate to 850-870 ℃ in a single-phase region, preserving heat for at least 25min, then carrying out water quenching, cooling to room temperature, heating to 500-580 ℃ and preserving heat for at least 35min, and then carrying out air cooling to room temperature.
The invention discloses a component screening method of a high-strength high-toughness hydrogen-embrittlement-resistant steel plate, which selects target components on the premise of controlling cost and ensuring weldability, and comprises the following steps:
a. drawing up the range of the chemical components of the base body of the target steel plate:
the main chemical components and the proportion of the components are preliminarily drawn up according to the mass percentage:
c: 0.05 to 0.11%, Si: 0.05 to 0.09%, Mn: 0.50-1.10%, Cr: 0.30-0.60%, Ni: 1.0-2.50%, Cu: 0.70-1.10%, Mo: 0.50-0.60%, the balance being Fe and unavoidable impurities;
b. determining characteristic parameters and writing a program file for developing integrated batch computation:
utilizing a Thermo-Calc calculation software package, adopting a TC-Python interface thereof to write a program file which can be developed to calculate characteristic parameters under different components and temperature conditions by using Python language, wherein the characteristic parameter 1 is T 0 Temperature, representing the temperature at which the free energies of austenite and ferrite are equal, the characteristic parameter 2 being AC and representing T 0 The carbon content in austenite at temperature; the key instructions in the program file comprise that thermodynamic data are read, and thermodynamic calculation of characteristic parameters 1 and 2 of different alloy systems is completed; automatic assignment of alloy components and temperature is realized by adopting a cycle statement, and batch calculation is completed; limiting the calculation error range to obtain effective data, and finishing the output of the calculation result;
c. determining calculation conditions, operating a calculation program to screen components:
setting the calculation step length of each alloy element based on the component range determined in the step a, and obtaining T by adopting the program file I for calculating the characteristic parameter 1 and the characteristic parameter 2 in the step b 0 And the result of the calculation of AC, keeping T low 0 On the basis of temperature, selecting points with high AC values as target components;
d. calculating the segregation energy of hydrogen atoms by applying a first principle, and determining the microalloy elements:
the first principle is adopted to calculate the partial energy (E) of hydrogen atoms at the carbide/matrix interface MC ) Calculating and comparing the bias energy of carbide NbC, TiC, VC/matrix interfaces corresponding to the Nb, V and Ti microalloy elements to be selected, and selecting the microalloy element in the carbide with the minimum bias energy as an alloy addition element to optimize the matrix chemical composition of the target steel plate drawn in the step a;
e. screening the steel substrate and microalloy components:
and d, determining microalloy elements according to the step d, adding the determined microalloy elements into the base chemical components of the drawn target steel plate, and re-determining the base chemical components and component proportion range of the target steel plate for preparing the target high-strength high-toughness hydrogen-embrittlement-resistant steel plate.
Preferably, in said step d, the addition of Nb, V and Ti micro-alloying elements can produce precipitation strengthening and fine grain strengthening effects, however, Ti easily combines with nitrogen to form square TiN or Ti (C, N) particles, affecting ductility and toughness. In addition, NbC, VC and TiC all have strong adsorption capacity to hydrogen atoms, and can be used as a hydrogen trap to capture the hydrogen atoms, so that the diffusion segregation of hydrogen is inhibited, and the hydrogen brittleness resistance of the steel is improved. The invention adopts a first principle to calculate the partial energy of hydrogen atoms at a carbide/matrix interface. The segregation energy determined from the semi-coherent misfit dislocation interface can be found: e NbC (-0.99eV)＜E TiC (-0.52eV)＜E VC (-0.31eV), namely the NbC/Fe interface has the smallest energy required for hydrogen absorption, namely the strongest hydrogen absorption capacity, and can effectively inhibit the diffusion of hydrogen atoms in the steel. In addition, the invention innovatively calculates the change of partial energy when Nb-V and Nb-Ti are added compositely by adopting a first principle, namely the partial energy of hydrogen atoms at a semi-coherent (Nb, V) C/Fe interface and a (Nb, Ti) C/Fe interface is calculated to be-0.42 eV and-0.34 eV, so that NbC has stronger adsorption force on the hydrogen atoms than (Nb, V) and (Nb, Ti) C, and the hydrogen brittleness resistance of the steel is improved. Therefore, Nb microalloying is added to improve the overall properties of the steel.
After the optimization of the components of the high-strength high-toughness hydrogen-embrittlement-resistant steel plate is completed, the target experimental steel is prepared according to the optimized matrix and microalloy components. The novel high-strength high-toughness hydrogen embrittlement-resistant steel plate with yield strength of over 1000MPa, impact energy of over 69J at minus 40 ℃ and hydrogen embrittlement sensitivity of less than 20% can be obtained by smelting, hot rolling, quenching and high-temperature tempering heat treatment, wherein the quenching temperature is 850-870 ℃, and the tempering temperature is 500-580 ℃.
The principle of the invention is as follows:
a method for screening components of a high-strength high-toughness hydrogen-embrittlement-resistant steel plate screens matrix components and microalloy components by thermodynamic calculation and first-nature principle calculation of characteristic parameters on the premise of ensuring weldability and reducing cost, so that the novel high-strength high-toughness hydrogen-embrittlement-resistant steel plate with yield strength of over 1000MPa, impact power of over 69J at-40 ℃ and hydrogen embrittlement sensitivity of less than 20% is obtained.
The high-strength and high-toughness steel is developed from common carbon steel, and alloy elements such as Ni, Cr, Mo, Si, Mn, Cu and the like are usually added to achieve the expected performance. The carbon content is increased, so that the strength can be obviously improved, but the service performance such as weldability is reduced, the nickel content is increased, the strong plasticity is favorably improved, and the cost is increased. C, Ni, Mn, Cu are austenite-forming elements, Si, Cr, Mo are ferrite-forming elements, and T is a rare earth element 0 The temperature marks the temperature at which the free energy of ferrite and the free energy of austenite are equal, and the austenite forming element can cause the temperature to be reduced, which means that the strength of martensite obtained after quenching is improved, and the ferrite forming element can play the opposite role; however, T 0 The carbon content (AC) in austenite increases at temperature due to the presence of ferrite-forming elements, which leads to improved austenite stability and is beneficial to ensuring ductility and toughness. It can be seen that T is used 0 The temperature and the AC can be used as characteristic parameters to comprehensively evaluate the influence of different alloy components on the toughness of the experimental steel.
As mentioned above, the addition of Nb, V and Ti microalloy elements can not only produce the effects of precipitation strengthening and fine grain strengthening, but also act as hydrogen traps to inhibit the diffusion of hydrogen and improve the hydrogen brittleness resistance of the steel. Therefore, the segregation energy of hydrogen atoms at the carbide/matrix interface is taken as another characteristic parameter, and the calculation of Nb, V, Ti and composite carbide is carried out by adopting the first principle, so that the influence of different microalloy elements on the hydrogen embrittlement resistance of the experimental steel can be evaluated.
Based on the method, the invention adopts Thermo-Calc calculation software package to develop the alloy T with different components 0 Temperature and T 0 Batch calculation of the carbon content AC in austenite at temperature, in T 0 And (4) selecting the components of the matrix by taking the lower temperature and the higher AC as targets, and determining ideal microalloy elements by adopting a first principle calculation and taking the lowest segregation energy as a target.
The traditional research and development mode of the steel materials carries out component optimization according to the thought of a trial and error method to obtain the expected performance, and the method has long time consumption, high cost and low efficiency and seriously restricts the research and development progress of new steel. The invention can realize scientific design and verification of target components of the novel high-strength high-toughness hydrogen-embrittlement-resistant steel plate by applying phase diagram thermodynamic calculation and first principle calculation, and completes short-period preparation, thereby being original work of the invention.
Compared with the prior art, the invention has the following obvious and prominent substantive characteristics and remarkable advantages:
1. the novel high-strength high-toughness hydrogen embrittlement-resistant steel plate designed by the invention has reasonable components, high strength, high toughness and good hydrogen embrittlement resistance, can be applied to harsh use environments and stress conditions, accurately ensures the service safety, and develops the application field of the novel high-strength high-toughness hydrogen embrittlement-resistant steel plate;
2. the invention can accelerate the development of a novel steel material with high strength, high and low temperature toughness and good hydrogen embrittlement resistance, and has great significance for engineering construction;
3. the method is simple and easy to implement, low in cost and suitable for popularization and application.
Drawings
FIG. 1 shows the data point calculation results in the screening process of the matrix composition according to the present invention.
FIG. 2DFT calculation about (001) α-Fe /(001) MC Three highly symmetric exemplary atomic structure diagrams of the interface.
Detailed Description
The invention relates to a high-strength high-toughness hydrogen-embrittlement-resistant steel plate, which comprises the following main components in percentage by mass:
c: 0.089-0.110%, Si: 0.06-0.08%, Mn: 0.80-1.10%, Cr: 0.35-0.60%, Ni: 2.0-2.50%, Cu: 0.85-1.10%, Mo: 0.50-0.60%, Nb: 0.04-0.06%, and the balance of Fe and inevitable impurities;
preparing a cast ingot by adopting a smelting process, and then carrying out hot rolling, quenching and high-temperature tempering heat treatment; when hot rolling is carried out, rolling the steel plate to a thickness of not more than 14mm through multiple hot rolling, controlling the initial rolling temperature to be 1150-1200 ℃, and controlling the final rolling temperature to be 950-1000 ℃; and during heat treatment, controlling the quenching temperature to be 850-870 ℃, cooling to room temperature after quenching, then controlling the tempering temperature to be 500-580 ℃, carrying out tempering heat treatment, and then air-cooling to room temperature to obtain the high-strength high-toughness hydrogen-embrittlement-resistant steel plate.
In the following embodiments, the high-strength high-toughness hydrogen embrittlement-resistant steel plate comprises the following main components in percentage by mass:
c: 0.089-0.108%, Si: 0.067-0.080%, Mn: 0.84-1.05%, Cr: 0.37-0.57%, Ni: 2.10-2.42%, Cu: 0.87 to 1.09%, Mo: 0.52-0.60%, Nb: 0.043-0.056%, and the balance of Fe and inevitable impurities.
The above-described scheme is further illustrated below with reference to specific embodiments, which are detailed below:
in this embodiment, the components of the high-strength high-toughness hydrogen embrittlement-resistant steel plate are optimized and the preparation method is as follows:
in the embodiment, research and development work of novel high-strength high-toughness hydrogen embrittlement-resistant steel plates is carried out based on integrated computing material engineering technology, and T is innovatively selected 0 Temperature being a characteristic quantity 1, T 0 The method comprises the following steps of taking the carbon element content AC in austenite at a temperature as a characteristic parameter 2, adopting commercial calculation software Thermo-Calc and an interface program, carrying out optimization on matrix alloy components by utilizing phase diagram thermodynamic calculation, and calculating the interaction between hydrogen atoms and microalloy carbide by combining a first nature principle to determine ideal microalloy elements, and specifically comprises the following steps:
a. the chemical composition range of the matrix of the experimental steel plate is drawn up:
the steel plate comprises the following chemical components in percentage by mass: c: 0.05 to 0.11%, Si: 0.05 to 0.09%, Mn: 0.50-1.10%, Cr: 0.30-0.60%, Ni: 1.0-2.50%, Cu: 0.70-1.10%, Mo: 0.50-0.60%, the balance being Fe and unavoidable impurities;
wherein, the Ni content is lower, which is beneficial to reducing the production cost; the carbon content is less than 0.11 percent, and 0.11 percent is the upper limit of the carbon content of the easy welding area in the Graville diagram. The carbon equivalent in the composition range is calculated by adopting the formula (1), and the carbon equivalent in the composition range is found to be between 0.18 and 0.33, and the composition range is just positioned in an easy welding area in a Graville diagram, so that the welding of a large structure is facilitated;
C eq ＝C+Si/30+(Cu+Mn+Cr)/20+Ni/60+Mo/15+V/10+5B (1)
b. determining characteristic parameters and writing a program file for developing integrated batch calculation:
utilizing a Thermo-Calc calculation software package, writing a program file which can calculate characteristic parameters under the conditions of different components and temperatures by adopting a TC-Python interface and using Python language, wherein the characteristic parameter 1 is T 0 Representing the temperature at which the austenite and ferrite Gibbs free energies are equal, with the characteristic parameter 2 being AC and representing T 0 The carbon content in austenite at temperature; the written program file can read thermodynamic data in TC software, namely a TCFE10 database, complete thermodynamic calculation of characteristic parameters 1 and 2 of different alloy systems to obtain T 0 And the law of variation of AC with composition;
realizing automatic assignment of alloy components and temperature by adopting a loop statement in a python program, namely assigning the alloy element content and the temperature successively according to the calculation step length in the following table 1 to finish batch calculation, limiting the calculation error range to obtain effective data and finishing the output of a calculation result;
c. determining calculation conditions, operating a calculation program to screen components:
dividing the ranges of the alloy elements by a certain step length based on the component ranges determined in the step a, calculating the total of 4 × 3 × 4 × 3 × 4 × 2 × 3 of the component points to 3456 as shown in table 1, inputting the component ranges and the step lengths by adopting a program file for integrally calculating the characteristic parameters 1 and 2 in the step b, and finally obtaining 3456 groups of T 0 And the calculation result of the AC to obtain a calculation value set of the characteristic parameters, wherein the calculation result is shown in figure 1;
at low maintenance of T 0 On the basis of temperature, points with high AC values were selected as target components, as shown in the circle in fig. 1;
TABLE 1 calculation step Table for each alloy element
| C | Si | Mn | Cu | Ni | Cr | Mo |
| 0.05 | 0.05 | 0.5 | 0.7 | 1 | 0.4 | 0.5 |
| 0.07 | 0.07 | 0.7 | 0.9 | 1.5 | 0.6 | 0.55 |
| 0.09 | 0.09 | 0.9 | 1.1 | 2 | 0.6 | |
| 0.11 | 1.1 | 2.5 |
d. Calculating the segregation energy of hydrogen atoms by applying a first principle, and determining the microalloy elements:
based on the Density Functional Theory (DFT), calculated by adopting the first principle (001) α-Fe /(001) MC The interface interacts with hydrogen to deeply understand the capture behavior of hydrogen, and M represents Nb, V and Ti microalloy elements;
this example is obtained by focusing on the Baker-Nusting (N-B) orientation relationship ((001) Fe ||(001) MC and[100] Fe ||[110] MC ) To calculate the capture effect of coherent and semi-coherent interfaces between alpha-Fe and MC carbide on hydrogen atoms;
FIG. 2 shows the DFT calculation about (001) α-Fe /(001) MC Three highly symmetric typical atomic structures of the interface:
(I) Fe-on-C configuration, wherein the Fe atom is located above the C atom;
(II) the Fe-on-M configuration, wherein the Fe atom is located above the Nb atom;
(III) a bridged configuration in which the Fe atom has two C atoms and two Nb atoms as nearest neighbors;
the hydrogen is determined in three configurations through DFT calculation, namely alpha-Fe, VC and TiCThe bias energy at the NbC interface, results are shown in table 2; visible hydrogen is in (001) α-Fe /(001) NbC The bias energy in the bridging configuration of the interface is the lowest, namely the effect of capturing hydrogen atoms by NbC is the most obvious;
in addition, the invention selects the bridging configuration with the lowest segregation energy, the interaction of the Nb-V composite carbide (Nb, V) C and the Nb-Ti composite carbide (Nb, Ti) C with hydrogen is calculated, the calculation result is shown in the table 2, and the hydrogen atom is (001) α-Fe /(001) NbC The segregation energy of the interface is the lowest, which shows that the capture effect of NbC on hydrogen atoms is the strongest, and 0.04-0.06% of Nb is added to improve the hydrogen embrittlement resistance of the steel;
TABLE 2 list of segregation energies of hydrogen atoms at (001) α -Fe/(001) MC interface
| Hydrogen trapping interface | Configuration(s) | Partial energy of hydrogen atom (eV) |
| (001)Fe/(001)TiC | Fe-on-C | -0.29 |
| Fe-on-Ti | -0.48 | |
| Bridge | -0.52 | |
| (001)Fe/(001)VC | Fe-on-C | -0.12 |
| Fe-on-V | -0.39 | |
| Bridge | -0.31 | |
| (001)Fe/(001)NbC | Fe-on-C | -0.18 |
| Fe-on-Nb | -0.58 | |
| Bridge | -0.99 | |
| (001)Fe/(001)(Nb,V)C | Bridge | -0.42 |
| (001)Fe/(001)(Nb,Ti)C | Bridge | -0.34 |
This example uses the principle of first sex to calculate the hydrogen atom at the carbide/matrix boundaryPartial energy of surface (E) MC ) The results show that NbC (-0.99eV)＜E TiC (-0.52eV)＜E VC (-0.31eV), namely the NbC/Fe interface has the minimum energy required for hydrogen absorption, namely the strongest hydrogen absorption capacity, and can effectively inhibit the segregation of hydrogen atoms in the steel to the grain boundary;
furthermore, in the embodiment, the segregation energies of hydrogen atoms at the semi-coherent (Nb, V) C/Fe interface and the (Nb, Ti) C/Fe interface are respectively-0.42 eV and-0.34 eV, so that NbC has stronger adsorption force to the hydrogen atoms than (Nb, V) C and (Nb, Ti) C, and is more beneficial to improving the hydrogen brittleness resistance of the steel, and therefore, the Nb microalloy is added to improve the comprehensive performance of the steel;
e. preparing experimental steel according to the screened matrix and microalloy components:
preparing an ingot by adopting a 20kg vacuum induction smelting furnace, and then cutting a steel block with the thickness of 40mm for hot rolling; rolling the steel plate to 14mm by multiple hot rolling, wherein the initial rolling temperature is 1150-1200 ℃, and the final rolling temperature is 950-1000 ℃; the target components and measured components are shown in table 3;
TABLE 3 composition (wt.%) and carbon equivalent of steel plate tested in this example
The hot-rolled experimental steel plate is heated to 850-870 ℃ single-phase region, is kept for 25min, is water-quenched to room temperature, is heated to 500-580 ℃ for 35min, is air-cooled to room temperature, and finally can obtain excellent performances of yield strength more than 1000MPa, impact toughness more than 69J at-40 ℃ and hydrogen embrittlement sensitivity less than 20%, wherein the heat treatment process and the performances of the experimental steel plate are shown in Table 4:
table 4 shows the heat treatment process and mechanical property table of the experimental steel plate of this example
As is clear from the data in Table 4, the yield strength of the test steels prepared by using the preferred compositions of this example was 1000MPa or more and the impact toughness at-40 ℃ was 69J or more.
Combined cathodic hydrogen charging, electrolyte: 0.2mol/LH 2 SO 4 +0.5g/L thiourea; hydrogen charging time: 24 h; current density: 2mA/cm 2 . And slow stretching (strain rate: 1X 10) -5 /s) test evaluation of hydrogen embrittlement sensitivity was performed on test steels quenched at 860 c + tempered at 500 c, and the properties before and after charging with hydrogen were evaluated as shown in table 5:
from the data in table 5, it can be seen that the hydrogen embrittlement sensitivity indexes of the experimental steels are all less than 20%.
TABLE 5 comparison table of slow tensile properties before and after hydrogen charging after tempering at 500 ℃ for steel plates of this example
Steel grades of similar chemical composition were selected as comparative examples, the chemical composition and carbon equivalent being shown in table 6: compared with the comparative example, the carbon equivalent of the steel grade designed by the invention is equivalent to the carbon equivalent of the steel grade, and is even lower.
TABLE 6 comparative example Components and carbon equivalent Table
Table 7 shows the mechanical properties of the inventive examples compared with those of comparative examples 1 to 5. It can be seen that comparative example 1 has a lower carbon content and thus an undesirable yield strength. Comparative example 2 the yield strength was improved by Nb-Ti composite addition on the basis of comparative example 1, but the toughness was significantly reduced. Comparative examples 3 and 4 are also low carbon compositions, but 6-7% Ni is added to compensate for the strength loss, increasing the production cost. The comparative example 3 adopts Nb-V composite addition, increases the yield strength of the steel, but has extremely low toughness. Comparative example 4 has an unsatisfactory yield strength, but a good toughness. Comparative example 5, in which the carbon content was increased and the V-Ti composite addition was used, was superior in yield strength and toughness, but the higher carbon content may result in decreased weldability. The steel grade with lower carbon and nickel contents designed by the invention obtains ideal strength and low-temperature toughness.
TABLE 7 comparison table of mechanical properties
In addition, the hydrogen embrittlement resistance of the examples was compared with comparative examples 5 to 8 of high-strength steels of the same strength grade, as shown in Table 8.
TABLE 8 hydrogen embrittlement resistance comparison table
From the above results, the hydrogen embrittlement sensitivity of the present examples is less than 20%, and the hydrogen embrittlement resistance is good. And after electrochemical pre-charging, the four comparative examples with the same strength grade are subjected to slow stretching at a low strain rate to show that the plasticity loss is up to 35-60%, and the hydrogen embrittlement resistance is low. The comparative example 8 adopts Nb-V composite addition, and the content of the microalloy element is larger than that of the Nb microalloy element in the invention example, but the hydrogen brittleness sensitivity index is 37.0 percent, and the hydrogen brittleness resistance is lower than that of the steel of the patent. The embodiment solves the problem that how to select proper target components on the premise of controlling cost and ensuring weldability so as to realize high strength with yield strength of more than 1000MPa, high low-temperature toughness with impact work at-40 ℃ of more than 69J and excellent performance with hydrogen brittleness sensitivity of less than 20 percent under the quenching and high-temperature tempering process conditions. The steel designed by the embodiment has reasonable components, and the novel high-strength high-toughness hydrogen embrittlement-resistant steel plate disclosed by the invention has high strength, high toughness and good hydrogen embrittlement resistance, can be applied to harsh use environments and stress conditions, accurately ensures the service safety, and develops the application field of the novel high-strength high-toughness hydrogen embrittlement-resistant steel plate; the method of the embodiment of the invention has great significance for engineering construction by accelerating the development of the novel iron and steel material with high strength, high and low temperature toughness and good hydrogen embrittlement resistance.
In summary, the following steps: the embodiment innovatively provides the component optimization and the preparation method of the novel high-strength high-toughness hydrogen embrittlement-resistant steel plate, the comprehensive performance of high strength, high toughness and excellent hydrogen embrittlement resistance is achieved while the cost is controlled and the weldability is guaranteed, and the novel high-strength high-toughness hydrogen embrittlement-resistant steel plate has obvious application reference values in the fields of material design research and engineering construction.
The embodiments of the present invention have been described with reference to the accompanying drawings, but the present invention is not limited to the embodiments, and various changes and modifications can be made according to the purpose of the invention, and any changes, modifications, substitutions, combinations or simplifications made according to the spirit and principle of the technical solution of the present invention shall be equivalent substitutions, as long as the purpose of the present invention is met, and the present invention shall fall within the protection scope of the present invention without departing from the technical principle and inventive concept of the present invention.
Claims (8)
1. The high-strength high-toughness hydrogen-embrittlement-resistant steel plate is characterized by comprising the following main components in percentage by mass:
c: 0.089-0.110%, Si: 0.06-0.08%, Mn: 0.80-1.10%, Cr: 0.35-0.60%, Ni: 2.0-2.50%, Cu: 0.85-1.10%, Mo: 0.50-0.60%, Nb: 0.04-0.06%, and the balance of Fe and inevitable impurities; preparing a cast ingot by adopting a smelting process, and then carrying out hot rolling, quenching and high-temperature tempering heat treatment; when hot rolling is carried out, rolling the steel plate to a thickness of not more than 14mm through multiple hot rolling, controlling the initial rolling temperature to be 1150-1200 ℃, and controlling the final rolling temperature to be 950-1000 ℃; and during heat treatment, controlling the quenching temperature to be 850-870 ℃, cooling to room temperature after quenching, then controlling the tempering temperature to be 500-580 ℃, carrying out tempering heat treatment, and then air-cooling to room temperature to obtain the high-strength high-toughness hydrogen-embrittlement-resistant steel plate.
2. The high-strength high-toughness hydrogen-embrittlement-resistant steel plate as claimed in claim 1, comprises the following main components by mass percent:
c: 0.089-0.108%, Si: 0.067-0.080%, Mn: 0.84-1.05%, Cr: 0.37-0.57%, Ni: 2.10-2.42%, Cu: 0.87 to 1.09%, Mo: 0.52-0.60%, Nb: 0.043-0.056%, and the balance of Fe and inevitable impurities.
3. The high strength, high toughness, hydrogen embrittlement resistant steel sheet of claim 1, wherein: the yield strength is not lower than 1000MPa, the tensile strength is not lower than 1000MPa, the elongation is not lower than 15%, the impact toughness at minus 40 ℃ is not lower than 69J, and the hydrogen embrittlement sensitivity index HEI is not higher than 20%.
4. The high strength high toughness hydrogen embrittlement resistant steel sheet as claimed in claim 3, wherein: the yield strength is not lower than 1042MPa, the tensile strength is not lower than 1079MPa, the elongation is not lower than 15.8%, the impact toughness at minus 40 ℃ is not lower than 82J, and the hydrogen embrittlement sensitivity index HEI is not higher than 15.4%.
5. The preparation method of the high-strength high-toughness hydrogen embrittlement-resistant steel plate as claimed in claim 1, wherein a smelting process is adopted to prepare an ingot, and then hot rolling, quenching and high-temperature tempering heat treatment are carried out; when hot rolling is carried out, rolling the steel plate to a thickness of not more than 14mm through multiple hot rolling, controlling the initial rolling temperature to be 1150-1200 ℃, and controlling the final rolling temperature to be 950-1000 ℃; during heat treatment, controlling the quenching temperature to be 850-870 ℃, cooling to room temperature after quenching, then controlling the tempering temperature to be 500-580 ℃, carrying out tempering heat treatment, and then air-cooling to room temperature to obtain the high-strength high-toughness hydrogen-embrittlement-resistant steel plate;
the prepared high-strength high-toughness hydrogen-embrittlement-resistant steel plate mainly comprises the following chemical components in parts by weight:
c: 0.089-0.110%, Si: 0.06-0.08%, Mn: 0.80-1.10%, Cr: 0.35-0.60%, Ni: 2.0-2.50%, Cu: 0.85-1.10%, Mo: 0.50-0.60%, Nb: 0.04-0.06%, and the balance of Fe and inevitable impurities.
6. The method for preparing the high-strength high-toughness hydrogen-embrittlement-resistant steel plate according to claim 5, wherein: the smelting process adopts a vacuum induction smelting furnace for smelting, then an ingot is prepared, the ingot is cut into steel blocks with the thickness of not less than 40mm, and the steel blocks are used as hot rolled steel.
7. The method for preparing the high-strength high-toughness hydrogen-embrittlement-resistant steel plate according to claim 6, wherein: the heat treatment process is that the hot rolled steel plate is heated to 850-870 ℃ in a single-phase region, heat preservation is carried out for at least 25min, then water quenching is carried out, the temperature is reduced to the room temperature, then the hot rolled steel plate is heated to 500-580 ℃ and heat preservation is carried out for at least 35min, and then air cooling is carried out to the room temperature.
8. A component optimization method for the high-strength high-toughness hydrogen-embrittlement-resistant steel plate as claimed in claim 1, wherein selecting target components under the premise of controlling cost and ensuring weldability includes the steps of:
a. drawing up the range of the chemical components of the base body of the target steel plate:
the main chemical components and the proportion of the components are preliminarily drawn up according to the mass percentage:
c: 0.05 to 0.11%, Si: 0.05 to 0.09%, Mn: 0.50-1.10%, Cr: 0.30-0.60%, Ni: 1.0-2.50%, Cu: 0.70-1.10%, Mo: 0.50-0.60%, the balance being Fe and unavoidable impurities;
b. determining characteristic parameters and writing a program file for developing integrated batch computation:
utilizing a Thermo-Calc calculation software package, writing a program file which can be developed to calculate characteristic parameters under the conditions of different components and temperatures by adopting a TC-Python interface and using Python language, wherein the characteristic parameter 1 is T 0 Temperature, representing the temperature at which the free energies of austenite and ferrite are equal, the characteristic parameter 2 being AC and representing T 0 The carbon content in austenite at temperature; the key instructions in the program file comprise that thermodynamic data are read, and thermodynamic calculation of characteristic parameters 1 and 2 of different alloy systems is completed; automatic assignment of alloy components and temperature is realized by adopting a cycle statement, and batch calculation is completed; limiting the calculation error range to obtain effective data, and finishing the output of the calculation result;
c. determining calculation conditions, operating a calculation program to screen components:
setting the calculation step length of each alloy element based on the component range determined in the step a, and obtaining T by adopting the program file I for calculating the characteristic parameters 1 and 2 in the step b 0 And the result of the calculation of AC, keeping T low 0 On the basis of temperature, selecting points with high AC values as target components;
d. calculating the segregation energy of hydrogen atoms by applying a first principle, and determining the microalloy elements:
the first principle is adopted to calculate the partial energy (E) of hydrogen atoms at the carbide/matrix interface MC ) Calculating and comparing the bias energy of carbide NbC, TiC, VC/matrix interfaces corresponding to the Nb, V and Ti microalloy elements to be selected, and selecting the microalloy element in the carbide with the minimum bias energy as an alloy addition element to optimize the matrix chemical composition of the target steel plate drawn in the step a;
e. screening the steel substrate and microalloy components:
and d, determining microalloy elements according to the step d, adding the determined microalloy elements into the base chemical components of the drawn target steel plate, and re-determining the base chemical components and component proportion range of the target steel plate for preparing the target high-strength high-toughness hydrogen-embrittlement-resistant steel plate.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210369916.9A CN114892072B (en) | 2022-04-08 | 2022-04-08 | High-strength high-toughness hydrogen embrittlement-resistant steel plate and component optimization and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210369916.9A CN114892072B (en) | 2022-04-08 | 2022-04-08 | High-strength high-toughness hydrogen embrittlement-resistant steel plate and component optimization and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN114892072A true CN114892072A (en) | 2022-08-12 |
| CN114892072B CN114892072B (en) | 2023-06-09 |
Family
ID=82715094
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210369916.9A Active CN114892072B (en) | 2022-04-08 | 2022-04-08 | High-strength high-toughness hydrogen embrittlement-resistant steel plate and component optimization and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN114892072B (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN116586819A (en) * | 2023-07-17 | 2023-08-15 | 成都先进金属材料产业技术研究院股份有限公司 | Welding wire molten steel and welding wire for welding low-pressure hydrogen transmission pipeline and preparation method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20150225822A1 (en) * | 2012-09-19 | 2015-08-13 | Jfe Steel Corporation | Abrasion resistant steel plate having excellent low-temperature toughness and excellent corrosive wear resistance |
| US20190055620A1 (en) * | 2016-02-25 | 2019-02-21 | The Japan Steel Works, Ltd. | Cu-containing low-alloy steel having excellent balance between strength and low-temperature toughness and method for producing same |
| CN113897552A (en) * | 2021-10-12 | 2022-01-07 | 上海大学 | 30 GPa% |
-
2022
- 2022-04-08 CN CN202210369916.9A patent/CN114892072B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20150225822A1 (en) * | 2012-09-19 | 2015-08-13 | Jfe Steel Corporation | Abrasion resistant steel plate having excellent low-temperature toughness and excellent corrosive wear resistance |
| US20190055620A1 (en) * | 2016-02-25 | 2019-02-21 | The Japan Steel Works, Ltd. | Cu-containing low-alloy steel having excellent balance between strength and low-temperature toughness and method for producing same |
| CN113897552A (en) * | 2021-10-12 | 2022-01-07 | 上海大学 | 30 GPa% |
Non-Patent Citations (1)
| Title |
|---|
| NING ZHAO等: "Strengthening-toughening mechanism of cost-saving marine steel plate with 1000 MPa yield strength", 《MATERIALS SCIENCE & ENGINEERING A》 * |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN116586819A (en) * | 2023-07-17 | 2023-08-15 | 成都先进金属材料产业技术研究院股份有限公司 | Welding wire molten steel and welding wire for welding low-pressure hydrogen transmission pipeline and preparation method thereof |
| CN116586819B (en) * | 2023-07-17 | 2023-10-13 | 成都先进金属材料产业技术研究院股份有限公司 | Welding wire molten steel and welding wire for welding low-pressure hydrogen transmission pipeline and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN114892072B (en) | 2023-06-09 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CA2962472C (en) | High-toughness hot-rolled high-strength steel with yield strength of grade 800 mpa and preparation method thereof | |
| JP5344454B2 (en) | Steel for warm working, warm working method using the steel, and steel and steel parts obtained thereby | |
| CN112048675A (en) | Low-yield-ratio granular bainite high-strength steel plate used in low-temperature environment and manufacturing method thereof | |
| JP2023514864A (en) | Controlled yield ratio steel and its manufacturing method | |
| CN109536850B (en) | High-strength-toughness low-yield-ratio thick steel plate and production process thereof | |
| CN107904504B (en) | A kind of delivery of normalizing state can Large Heat Input Welding EH36 special heavy plate and preparation method | |
| CN109182916B (en) | High-performance super-thick steel plate for wind power and production method thereof | |
| CN113249645B (en) | High-ductility and ultrahigh-strength ductile steel and preparation method thereof | |
| CN108624809A (en) | Excellent seawater corrosion resistance, anti-fatigue performance and the brittle ultrahigh-strength steel plates of environment resistant and its manufacturing method | |
| CN109338219B (en) | Super-thick steel plate for wind power flange and production method thereof | |
| CN108385023A (en) | High-strength high-toughness steel for nuclear power voltage stabilizer and manufacturing method thereof | |
| CN107502835A (en) | A kind of weather-proof angle steel of steel tower high-strength and high ductility and preparation method thereof | |
| CN106086657A (en) | A kind of yield strength ultra high-strength structural steel plate more than 1300MPa and preparation method thereof | |
| JP2016509129A (en) | High strength steel plate and manufacturing method thereof | |
| CN107746937A (en) | High-strength high-toughness steel plate and its manufacture method for nuclear power pressure equipment | |
| CN102021474A (en) | Anti-seismic H-type steel and production method thereof | |
| CN114892072B (en) | High-strength high-toughness hydrogen embrittlement-resistant steel plate and component optimization and preparation method thereof | |
| CN108342649A (en) | A kind of quenched steel for high strength pressure vessel and production method of acid corrosion-resistant | |
| CN103667921B (en) | The uniform high-strong toughness Plate Steel of through-thickness performance and production method thereof | |
| CN109207847B (en) | Low-carbon equivalent high-hole-expansion-rate 1180 MPa-grade cold-rolled steel plate and manufacturing method thereof | |
| CN106319356A (en) | High manganese hot-dip galvanized steel sheet containing rare earth and manufacture method thereof | |
| CN114381658A (en) | 800 MPa-grade low-welding-crack-sensitivity steel plate and manufacturing method thereof | |
| JP4687554B2 (en) | Steel plate for quenched member, quenched member and method for producing the same | |
| CN102634727B (en) | High-toughness steel for engineering machine and production method thereof by using TMCP (Thermal Mechanical Control Processing) | |
| CN114752850B (en) | High-strength steel plate with yield strength of 785MPa and manufacturing 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 |