CN113755762A - Low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel and preparation method thereof - Google Patents

Low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel and preparation method thereof Download PDF

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CN113755762A
CN113755762A CN202111097367.6A CN202111097367A CN113755762A CN 113755762 A CN113755762 A CN 113755762A CN 202111097367 A CN202111097367 A CN 202111097367A CN 113755762 A CN113755762 A CN 113755762A
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steel
temperature
precipitated phase
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strength steel
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CN113755762B (en
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韩培德
寻懋年
刘鹏
张玺成
齐治畔
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Taiyuan University of Technology
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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/28—Normalising
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite
    • 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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  • Heat Treatment Of Steel (AREA)

Abstract

The invention belongs to the technical field of ultra-fine dispersion precipitated phase high-strength steel and a preparation method thereof, and particularly relates to low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel and a preparation method thereof, which solve the technical problems in the background technology. The method exerts the precipitation strengthening effect of the V (C, N) precipitated phase, so that the precipitated phase can be uniformly and dispersedly distributed in the matrix, the dispersion strengthening effect is achieved, and the high-strength and high-plasticity high-strength steel is prepared.

Description

Low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel and preparation method thereof
Technical Field
The invention belongs to the technical field of ultra-fine dispersion precipitated phase high-strength steel and a preparation method thereof, and relates to a low-V microalloyed precipitated phase, in particular to low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel and a preparation method thereof.
Background
The performance of steel is improved by adding different alloy elements into the steel, which is a common process at the present stage, and the properties of different alloy elements are utilized to enable the alloy elements to play respective roles in the steel, so that the performance of the steel can be improved. However, because of different melting points of various elements, a certain amount of alloying elements added into steel may cause that the alloying elements are difficult to be completely dissolved in the steel, and easily form a part which is not beneficial to improving mechanical properties together with other tissues in the steel, for example, some V cannot be completely dissolved back into the steel due to not reaching the optimal melting temperature of V during melting, and the effect of adding V during melting is difficult to be exerted. Generally, steel is deformed to generate more nucleation sites to induce nucleation and precipitation to form ultra-fine dispersed precipitated phases, and is subjected to pretreatment and then rapid cooling at a certain speed to increase the solid solubility of elements such as V, and simultaneously, the steel billet is normalized and reheated to make crystal grains fine and alleviate the influence of inclusions such as MnS.
Through the examination of the existing documents and patents, the steel performance is improved by adding micro-alloying elements and adopting a controlled rolling and cooling technology or changing the content of C in the steel on the basis of the components of the carbon-manganese structural steel, so that the steel can be regulated and controlled, and the required mechanical properties can be further achieved. In fact, how to make dissolved alloy elements disperse and finely precipitate through a heat treatment process is the key for trace alloy elements to play a strengthening role, however, after the elements added in the smelting process are dissolved back into steel, researches on the precipitation rules of subsequent precipitated phases, particularly the correlation among the precipitation temperature, the precipitation time, the precipitated phase characteristics and the like are few.
Disclosure of Invention
The invention aims to solve the technical problems in the background technology and provides low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel and a preparation method thereof. Through scientific optimization design of components and subsequent heat treatment on the smelted steel billet, alloy elements added in the steel can play a role of the steel, so that the effects of fineness, dispersion and precipitation strengthening are achieved, the low-V microalloyed ultra-fine dispersion precipitation phase high-strength steel with high strength, high plasticity and other mechanical properties taken into consideration is prepared, the mechanical property requirement of the steel required in production, processing and application is met, the economic cost is reduced, and the safety coefficient is improved.
The technical means for solving the technical problems of the invention is as follows: the low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel is composed of the following elements in percentage by mass: c: 0.03 to 0.35%, Si: 0.70-1.10%, Mn: 1.55-1.75%, V: 0.06-0.30%, N: 0.012-0.035%, Cr: 0.15-0.45%, P is less than or equal to 0.035%, S is less than or equal to 0.025%, and the balance of Fe and inevitable impurities. The yield strength of the high-strength-plasticity low-V microalloyed superfine dispersion precipitated phase high-strength steel reaches more than 750MPa, the tensile strength is more than 950MPa, and the elongation is 15-20%.
Preferably, the alloy consists of the following elements in percentage by mass: c: 0.05 to 0.33%, Si: 0.70-0.95%, Mn: 1.60-1.75%, V: 0.11 to 0.18%, N: 0.018-0.030%, Cr: 0.15-0.45%; p is less than or equal to 0.025 percent, S is less than or equal to 0.025 percent, and the balance of Fe and inevitable impurities. The high-strength steel obtained by proportioning the element components in the proportion has better various performances.
The invention aims to solve the technical problems: the preparation method comprises the steps of taking the element components according to the nominal component proportion, mixing the element components, smelting to obtain a steel billet, treating the smelted steel billet through a conventional heating furnace process or a straight rolling process, heating the steel ingot cooled to room temperature after treatment, preserving heat at a certain temperature for a certain time to enable V to be completely dissolved into the steel ingot, cooling at a certain temperature and preserving heat for a certain time to enable V to be completely separated out to form a V (C, N) uniform and fine dispersed precipitated phase, and thus the low-V microalloyed ultra-fine dispersed precipitated phase high-strength steel is provided. V (C, N) is vanadium carbonitride, and the preparation method of the invention adopts the control of the content, size and distribution of V (C, N) precipitated phases and refines crystal grains through normalizing treatment, so that the high-strength plastic low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel with yield strength of more than 750MPa, tensile strength of more than 950MPa and elongation of 15-20% can be obtained. The added V elements in the nominal components can be completely dissolved into the steel through the re-dissolution of V, any impurities and residual V elements are not remained, in addition, the heat preservation is carried out for a certain time at a certain temperature during cooling, the V (C, N) precipitated phase can be uniformly dispersed and precipitated, the obtained precipitated phase is small and uniformly distributed near a grain boundary, the precipitation strengthening effect of the V (C, N) precipitated phase is exerted, and the mechanical property of the steel is improved from the microstructure.
The invention has the beneficial effects that: the invention provides a high-strength plastic low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel with yield strength of more than 750Mpa, tensile strength of more than 950Mpa and elongation of 15-20%; the invention also provides a preparation method of the low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel, which exerts the precipitation strengthening effect of the V (C, N) precipitated phase to ensure that the precipitated phase can be uniformly and dispersedly distributed in a matrix to achieve the dispersion strengthening effect, and the low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel with high strength and high plasticity is prepared and obtained, and has the advantages of low application cost, simple heat treatment process and strong economic applicability.
Drawings
FIG. 1 is a metallographic structure diagram of a high-strength steel in comparative example 1 in the present invention without heat treatment.
FIG. 2 is a metallographic structure diagram of a low V microalloyed ultra-fine dispersion precipitated phase high strength steel obtained in example 1 of the present invention.
FIG. 3 is a metallographic structure of the low V microalloyed ultra-fine dispersion precipitated phase high strength steel obtained in example 2 of the present invention.
FIG. 4 is a metallographic structure diagram of a low V microalloyed ultra-fine dispersion precipitated phase high strength steel obtained in example 3 of the present invention.
FIG. 5 is a metallographic structure diagram of a low V microalloyed ultra-fine dispersion precipitated phase high strength steel obtained in example 4 of the present invention.
Detailed Description
Referring to fig. 1 to 5, a low V microalloyed ultra-fine dispersion precipitated phase high strength steel and a method for manufacturing the same according to the present invention will be described in detail.
Comparative example 1: taking the components containing various elements according to the proportion, mixing, smelting, and then continuously casting a plate blank into an ingot, wherein the weight ratio of the chemical components of the components is controlled as follows: c: 0.17%, Si: 0.81%, Mn: 1.64%, V: 0.145%, N: 0.0183%, Cr: 0.21%, S: 0.024%, P: 0.014%, the balance being Fe; producing a steel billet by a conventional heating furnace process, wherein the heating temperature of the steel billet is 1197 ℃, the tapping temperature of the steel billet is 1143 ℃, the initial rolling temperature is 1093 ℃, and the final rolling temperature is 1047 ℃; the direct rolling process comprises the steps that the initial rolling temperature of a steel billet is 1035 ℃, and the final rolling temperature is 1003 ℃; and then, air-cooling the produced steel billet to room temperature to obtain a steel ingot without normalizing heat treatment, wherein the metallographic structure of the obtained steel ingot is shown in figure 1.
Example 1: taking the element components according to the nominal component proportion, wherein the mass percent of each element component is as follows: c: 0.03%, Si: 0.70%, Mn: 1.5%, V: 0.06%, N: 0.012%, Cr: 0.15%, P: 0.035%, S: 0.025 percent and the balance of Fe, and the element components are mixed and smelted by adopting a steel smelting process to obtain a billet, and then the smelted billet is treated by a conventional heating furnace process, wherein the conventional heating furnace process is to carry out pre-heat treatment on the smelted billet and then cool the billet to room temperature in the air; in the conventional heating furnace process, the heating temperature of a steel billet is 1150 ℃, the tapping temperature of the steel billet is 1100 ℃, the initial rolling temperature is 1000 ℃, and the final rolling temperature is 950 ℃; after treatment, the steel ingot cooled to room temperature is heated, the temperature is maintained at 960 ℃ for 2 hours so that V can be completely dissolved into the steel ingot, then the temperature is maintained at 500 ℃ for 3 hours so that V can be completely precipitated to form a uniformly dispersed fine precipitated phase of V (C, N), so that the low-V microalloyed ultra-fine dispersed precipitated phase high-strength steel is provided, and the metallographic structure of the high-strength steel prepared in example 1 is shown in FIG. 2.
Example 2: taking the element components according to the nominal component proportion, wherein the mass percent of each element component is as follows: c: 0.032%, Si: 0.8%, Mn: 1.60%, V: 0.08%, N: 0.020%, Cr: 0.25%, P: 0.030%, S: 0.020 percent of Fe and the balance of Fe, mixing the element components, smelting by adopting a steel smelting process to obtain a billet, and then treating the smelted billet by adopting a conventional heating furnace process, wherein the conventional heating furnace process is to carry out pre-heat treatment on the smelted billet and then cool the billet to room temperature in the air; in the conventional heating furnace process, the heating temperature of a steel billet is 1170 ℃, the tapping temperature of the steel billet is 1110 ℃, the initial rolling temperature is 1050 ℃, and the final rolling temperature is 980 ℃; after treatment, the steel ingot cooled to room temperature is heated, the temperature is maintained at 1030 ℃ for 1h so that V can be completely dissolved into the steel ingot, then the temperature is maintained at 530 ℃ for 1h so that V can be completely precipitated to form a uniformly dispersed fine precipitated phase of V (C, N), so that the low-V microalloyed ultra-fine dispersed precipitated phase high-strength steel is provided, and the metallographic structure of the high-strength steel prepared in example 2 is shown in FIG. 3.
Example 3: taking the element components according to the nominal component proportion, wherein the mass percent of each element component is as follows: c: 0.033%, Si: 0.9%, Mn: 1.70%, V: 0.10%, N: 0.030%, Cr: 0.35%, P: 0.025%, S: 0.015 percent and the balance of Fe, mixing the element components, smelting by adopting a steel smelting process to obtain a steel billet, and then treating the smelted steel billet by adopting a conventional heating furnace process, wherein the conventional heating furnace process is to carry out pre-heat treatment on the smelted steel billet and then cool the steel billet to room temperature in the air; in the conventional heating furnace process, the heating temperature of a steel billet is 1180 ℃, the tapping temperature of the steel billet is 1130 ℃, the initial rolling temperature is 1080 ℃, and the final rolling temperature is 1000 ℃; and heating the steel ingot cooled to room temperature after treatment, keeping the temperature at 1060 ℃ for 0.5h to ensure that V can be completely dissolved into the steel ingot, and keeping the temperature at 600 ℃ for 0.5h to ensure that V can be completely precipitated to form a uniformly dispersed fine precipitated phase of V (C, N) so as to provide the low-V microalloyed ultra-fine dispersed precipitated phase high-strength steel, wherein the metallographic structure of the high-strength steel prepared in example 3 is shown in FIG. 4.
Example 4: taking the element components according to the nominal component proportion, wherein the mass percent of each element component is as follows: c: 0.35%, Si: 1.10%, Mn: 1.75%, V: 0.30%, N: 0.035%, Cr: 0.45%, P: 0.015%, S: 0.010 percent and the balance of Fe, mixing the element components, smelting by adopting a steel smelting process to obtain a billet, and then treating the smelted billet by a conventional heating furnace process, wherein the conventional heating furnace process is to carry out pre-heat treatment on the smelted billet and then cool the billet to room temperature in the air; in the conventional heating furnace process, the heating temperature of a steel billet is 1200 ℃, the tapping temperature of the steel billet is 1150 ℃, the initial rolling temperature is 1100 ℃, and the final rolling temperature is 1050 ℃; after treatment, the steel ingot cooled to room temperature is heated, the temperature is maintained at 1000 ℃ for 1.5h so that V can be completely dissolved into the steel ingot, and then the temperature is maintained at 570 ℃ for 2h so that V can be completely precipitated to form a uniformly dispersed fine precipitated phase of V (C, N), so that the low-V microalloyed ultra-fine dispersed precipitated phase high-strength steel is provided, wherein the metallographic structure of the high-strength steel prepared in example 4 is shown in FIG. 5.
In embodiments 1 to 4, the conventional heating furnace process may be replaced with a direct rolling process; in the direct rolling process, the initial rolling temperature of the billet is 950-1050 ℃, and the final rolling temperature is 900-1050 ℃.
It can be seen from comparison of fig. 1 and fig. 2 to 5 that the microstructure after heat treatment is changed greatly, ferrite and pearlite are refined obviously, which shows that V can be dissolved into the steel ingot completely after treatment, and then V can be precipitated completely by cooling and keeping the temperature for a certain time at a certain temperature to form V (C, N) uniform dispersed fine precipitate pinning grain boundaries, so as to provide the low-V microalloyed ultra-fine dispersed precipitate high-strength steel.
While the preferred embodiments of the present invention have been illustrated and described, it will be understood by those skilled in the art that various changes in form and details may be made therein without departing from the spirit and scope of the invention as defined by the appended claims.

Claims (10)

1. The low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel is characterized by comprising the following elements in percentage by mass: c: 0.03 to 0.35%, Si: 0.70-1.10%, Mn: 1.55-1.75%, V: 0.06-0.30%, N: 0.012-0.035%, Cr: 0.15-0.45%, P is less than or equal to 0.035%, S is less than or equal to 0.025%, and the balance of Fe and inevitable impurities.
2. The low-V microalloyed ultra-fine dispersion precipitated phase high strength steel as claimed in claim 1, characterized by consisting of the following elements in mass percent: c: 0.05 to 0.33%, Si: 0.70-0.95%, Mn: 1.60-1.75%, V: 0.11 to 0.18%, N: 0.018-0.030%, Cr: 0.15-0.45%; p is less than or equal to 0.025 percent, S is less than or equal to 0.025 percent, and the balance of Fe and inevitable impurities.
3. The method for preparing a low-V microalloyed ultra-fine dispersed precipitated phase high-strength steel as claimed in claim 1, wherein the method comprises the steps of taking the element components according to the nominal component proportion, mixing the element components, smelting to obtain a steel billet, treating the smelted steel billet by a conventional heating furnace process or a direct rolling process, heating the steel ingot cooled to room temperature after treatment, keeping the temperature for a certain time at a certain temperature to enable V to be completely dissolved in the steel ingot, cooling at a certain temperature and keeping the temperature for a certain time to enable V to be completely precipitated, and forming a V (C, N) uniformly dispersed fine precipitated phase to provide the low-V microalloyed ultra-fine dispersed precipitated phase high-strength steel.
4. The method of claim 3, wherein the conventional furnace process comprises pre-heat treating the melted slab, followed by cooling in air to room temperature; in the conventional heating furnace process, the heating temperature of the billet is 1150-1200 ℃, the tapping temperature of the billet is 1100-1150 ℃, the starting temperature is 1000-1100 ℃, and the finishing temperature is 950-1050 ℃.
5. The method of claim 3, wherein the initial rolling temperature of the steel billet in the direct rolling process is 950 ℃ to 1050 ℃ and the final rolling temperature is 900 ℃ to 1050 ℃.
6. The preparation method of the low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel as claimed in claim 4 or 5, wherein the temperature at which V can be completely dissolved into the steel ingot is 960-1060 ℃, and the heat preservation time is 0.5-2 h.
7. The preparation method of the low-V microalloyed ultra-fine dispersion precipitated phase high strength steel as claimed in claim 6, wherein the temperature at which V can be completely dissolved into the steel ingot is 960-1030 ℃, and the heat preservation time is 0.5-1 h.
8. The method for preparing a low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel as claimed in claim 7, wherein the temperature at which V can be completely precipitated and form a V (C, N) uniformly dispersed fine precipitated phase is 500-600 ℃, and the holding time is 0.5-3 h.
9. The method for preparing a low-V microalloyed ultra-fine dispersion precipitated phase high strength steel as claimed in claim 8, wherein the temperature at which V can be completely precipitated and form a V (C, N) uniformly dispersed fine precipitated phase is 530 ℃ to 570 ℃, and the holding time is 0.5h to 1 h.
10. The method for preparing the low-V microalloyed ultra-fine dispersion precipitated phase high strength steel as claimed in claim 9, wherein the steel blank is smelted by a steel smelting process.
CN202111097367.6A 2021-09-18 2021-09-18 Low-V microalloyed ultra-fine dispersion precipitated phase high-strength steel and preparation method thereof Active CN113755762B (en)

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CN110835670A (en) * 2019-09-30 2020-02-25 鞍钢股份有限公司 High-wear-resistance high-hardness easy-cutting high-end mirror surface plastic die steel and preparation method thereof
CN111074152A (en) * 2019-12-21 2020-04-28 钢铁研究总院 Hierarchical controlled cooling process for 600 MPa-grade high-strength anti-seismic weather-resistant hot-rolled steel bars

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH10204529A (en) * 1997-01-24 1998-08-04 Sumitomo Metal Ind Ltd Building seamless steel pipe excellent in fire resistance
CN102534367A (en) * 2011-12-02 2012-07-04 北京科技大学 Steel for superhigh-strength hot rolling automobile structure and preparation method thereof
CN106957991A (en) * 2017-05-08 2017-07-18 钢铁研究总院 A kind of precipitation Controlled cooling process of hot-rolled microalloy reinforcing bar
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