CN108018503B - Layered superfine crystal dual-phase ferrite/martensite steel and preparation method thereof - Google Patents
Layered superfine crystal dual-phase ferrite/martensite steel and preparation method thereof Download PDFInfo
- Publication number
- CN108018503B CN108018503B CN201711217801.3A CN201711217801A CN108018503B CN 108018503 B CN108018503 B CN 108018503B CN 201711217801 A CN201711217801 A CN 201711217801A CN 108018503 B CN108018503 B CN 108018503B
- Authority
- CN
- China
- Prior art keywords
- martensite
- phase
- steel
- ferrite
- dual
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—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
- 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
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Landscapes
- 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
A lamellar superfine crystal dual-phase ferrite/martensite steel and its preparing process features that the ferrite and austenite with lath characteristics are obtained by heating the initial martensite structure in two-phase region, the structure is refined, more phase interfaces are introduced to the material, the fine grain process is accelerated, and the refined grains are accelerated1‑A3The method has the advantages of simple process and strong controllability, can obviously reduce the rolling deformation in the preparation process of the superfine dual-phase steel, and can prepare the superfine dual-phase steel with large section size at the same time.
Description
Technical Field
The invention belongs to the technical field of preparing superfine grained ferrite/martensite dual-phase steel, and particularly relates to layered superfine grained dual-phase ferrite/martensite steel and a preparation method thereof.
Background
The dual-phase steel has excellent mechanical and processing properties, is widely applied to the automobile industry, and plays an important role in weight reduction and energy conservation. The performance of dual-phase steel depends mainly on the ratio of ferrite to martensite, and the improvement of the performance is limited only by means of composition design and process improvement, and grain refinement is considered as an effective means for solving the problem, for example, Dierk Raabe et al ("Deformions and fractions in fine-and ultra-fine-grained transferred/textured dual-phase steel and the effect of formation, Acta Materialia,2011.59(2): p.658-670") refine the grains from 12.4 μm to 1.2 μm, increase the material yield strength from 445MPa to 525MPa, and increase the tensile strength from 870MPa to 1037 MPa. At present, the preparation method of the ultra-fine crystal dual-phase steel reported in the literature is divided into a one-step method and a two-step method. Mukherjee proposes a one-step method for preparing ultra-fine Dual-Phase steel based on deformation induced ferrite transformation principle, and adopts the process to refine grains to about 1 μm ("Grain reference in Dual-Phase Steels, metallic & Materials transformations A,2009.40(9): p.2145-2159" and "crystalline company of novel and structural Processing for Dual-Phase Steels, Materials & Manufacturing Processes,2007.22(4): p.511-515"); xuhaiwei et al ("fine grain two-phase low carbon steel texture control based on dynamic phase transformation, Metal Science, 2006.42(10): p.1101-1108") and Korea scholar et al ("fluorescence of transformation induced transformation on grain refinement of dual phase steel, Materials Science & Engineering A,2002.323(1): p.148-159") also refined the grains to 2-4 μm, respectively, using this method; based on the technology, the Kite et al (the development of low-cost hot-rolled ultra-fine crystal dual-phase steel with the pressure of over 700MPa, the research and study on the quality control technology, shape, dimension precision and surface quality control and improvement, 2010) develops the Nb microalloying technology, increases the recrystallization temperature and is beneficial to the generation of deformation induced ferrite phase change. The ultra-fine Dual-phase Steels reported in The literature are mostly prepared by a two-step process, which comprises two steps of large plastic deformation refined grains and two-phase zone short-time heating quenching to obtain a Dual-phase Structure, wherein The processes of lamination rolling ("channeling for plastic deformation by means of phase-two structured and structured pressing, perpendicular Material, 2005.52(6): p.433-437"), High-pressure torsion ("The mechanism of deformation for nano-structured and distributed pressing of property in a polar material, which leads to High pressure pressing, Acta Material, 2003.51(18): p.5555-5570"), equal channel extrusion ("ultra-crystallized-textured vision of cold rolling, which leads to High temperature of Microstructure, which processes, which are, processes, acta Materials, 2007.55(7): p.2337-2350 ") and high deformation warm rolling (" Effect of grain refining to 1 μm on strain hardness of dual-phase steels, Materials Science & Engineering a,2010.527 (29-30): p.7832-7840 ") are commonly used for grain refinement, by which grains can be efficiently refined to around 1 μm.
Although both of the above-mentioned methods are effective for producing ultra-fine dual-phase steel, these methods are far from practical use. The deformation induced ferrite phase transition technology has extremely strict requirements on the rolling process, requires large deformation, high deformation rate and cooling rate after rolling, and still faces difficulty in industrial production. The large-deformation and two-phase-region short-time heating quenching process can only prepare the superfine-grained two-phase steel material with smaller cross-sectional dimension, because the process method requires larger plastic deformation and the final dimension of the sample is smaller; on the other hand, the material after large deformation in the heating process of the two-phase region can only be heated for a short time to ensure that ultrafine grains are obtained, and if the cross section size of the material is larger, the material cannot be austenitized by short-time heating, and a two-phase structure cannot be obtained. Therefore, the preparation technology of the large-section-size ultra-fine dual-phase steel, which is simple in development process and suitable for industrial production, is a key technical problem in the technical field of the ultra-fine dual-phase steel.
Disclosure of Invention
In order to overcome the technical defects, the invention aims to provide layered superfine grain dual-phase ferrite/martensite steel and a preparation method thereof, which solve the problem of preparing high-strength and high-toughness superfine grain dual-phase steel in low-carbon Mn-Si-Cr series steel, have layered superfine grain ferrite/martensite structures, and obviously improve the impact toughness while improving the material strength and the elongation.
In order to achieve the purpose, the invention adopts the technical scheme that:
the layered superfine crystal dual-phase ferrite/martensite steel comprises the following components in percentage by weight: 0.15-0.25% of C, 0.5-2.0% of Cr, 1.5-3.0% of Mn, 0.7-2.50% of Si, P: < 0.05%, S: < 0.06%, the balance being Fe.
The layered superfine dual-phase steel structure is as follows: the ferrite and the martensite are alternately distributed in a layered mode, the ferrite is in an equiaxial mode, the average grain size is about 1 mu m, the volume fraction of the martensite is 10-50%, the thickness of the martensite strips is 0.2-2 mu m, and the distance between the martensite strips is 0.2-2 mu m.
The impact energy (A) of the layered superfine dual-phase steel is in the temperature range of-196 ℃ to 80 DEG CKV) More than 138J, abnormal toughness rise in the temperature range of-60 ℃ to 0 ℃, and the highest impact energy of more than 258J.
A preparation method of layered ultra-fine grained dual-phase ferrite/martensite steel comprises the following steps: the low-carbon Mn-Si-Cr series steel comprises the following components in percentage by weight (wt.%): 0.15-0.25% of C, 0.5-2.0% of Cr, 1.5-3.0% of Mn, 0.7-2.50% of Si, P: < 0.05%, S: < 0.06%, the balance being Fe; heating low-carbon Mn-Si-Cr series steel to 900-1200 ℃ to obtain austenite, preserving heat for 0.5-2h to homogenize austenite components and coarsen crystal grains, and then air-cooling or water-quenching to room temperature to obtain a lath martensite structure;
the lath martensite structure is reheated to A1-A3Heating the steel plate in a two-phase region at a certain temperature for 0.5 to 3 hours to obtain a ferrite/austenite structure with lath characteristics;
then, the obtained ferrite/austenite structure is rolled for multiple times within the temperature range of 550-700 ℃, the accumulated rolling reduction is 40-70%, and the rolled material is subjected to air cooling or water quenching treatment; thus obtaining the layered superfine crystal dual-phase ferrite/martensite steel.
The layered superfine dual-phase steel comprises the following components in percentage by weight: 0.15-0.25% of C, 0.5-2.0% of Cr, 1.5-3.0% of Mn, 0.7-2.50% of Si, P: < 0.05%, S: < 0.06%, the balance being Fe.
The lamellar superfine dual-phase steel structure prepared by the preparation method comprises the following steps: the ferrite and the martensite are alternately distributed in a layered mode, the ferrite is in an equiaxial mode, the average grain size is about 1 mu m, the volume fraction of the martensite is 10-50%, the thickness of the martensite strips is 0.2-2 mu m, and the distance between the martensite strips is 0.2-2 mu m.
The impact energy (A) of the prepared lamellar superfine crystal dual-phase steel is in the temperature range of-196 ℃ to 80 DEG CKV) More than 138J, abnormal toughness rise in the temperature range of-60 ℃ to 0 ℃, and the highest impact energy of more than 258J.
The invention has the beneficial effects that:
the invention is characterized in that the low-carbon Mn-Si-Cr series steel for preparing the lamellar superfine dual-phase steel needs to have obvious structure genetic characteristics, ferrite and austenite structures obtained after the martensite structure is heated in a two-phase region have the characteristics of martensite lath, the austenite obtained after the two-phase region is heated has enough stability, the transformation from the austenite to pearlite or ferrite does not occur in the subsequent rolling process, and the transformation into the martensite structure is carried out in the cooling process after the rolling. In addition, compared with the process for preparing the superfine dual-phase steel by large deformation and short-time heating quenching in a two-phase region, the invention has the following characteristics: a) the deformation amount of the prepared superfine crystal dual-phase steel can be obviously reduced, and the grains are refined without great deformation amount; b) the superfine crystal dual-phase steel can be prepared by one-step process without heating and quenching the two-phase region after rolling; c) can prepare the large-section-size ultrafine-crystal dual-phase steel, and solves the technical problem of preparation of the large-section-size ultrafine-crystal dual-phase steel. The mechanical properties of the layered superfine crystal dual-phase steel prepared by the method are as follows: rp0.2 is more than or equal to 750MPa, Rm is more than or equal to 1300MPa, A is more than or equal to 12 percent, and the impact energy (A) is in the temperature range of-196 ℃ to 80 DEG CKV) More than 138J, abnormal toughness rise in the temperature range of-60 ℃ to 0 ℃, and the highest impact energy of more than 258J.
Drawings
FIG. 1 is a schematic view of a layered ultra-fine grained dual-phase steel rolling process.
FIG. 2 is a layered ultra-fine dual-phase steel SEM structure.
FIG. 3 is a TEM structure of lamellar superfine dual-phase steel.
Detailed Description
The present invention will be described in further detail by way of examples.
The implementation steps of the invention are as follows: firstly, heating low-carbon Mn-Si-Cr series steel to 900-; then the martensite structure is formedReheating to A1-A3Heating the two-phase region at a certain temperature, keeping the temperature for 0.5-3h, obtaining a ferrite/austenite structure with lath characteristics by utilizing the tissue genetic phenomenon in the heating process of the two-phase region of the martensite structure, refining the structure, introducing more phase interfaces into the material, and accelerating the grain subdivision process in the subsequent rolling process; then rolling for multiple passes within the temperature range of 550-700 ℃, wherein the accumulated rolling reduction is between 40 and 70 percent, and performing air cooling or water quenching treatment after rolling to obtain the ultra-fine grain ferrite/martensite structure with the layered characteristic, wherein the process flow is shown in figure 1. In the implementation process of the invention, the proportion of ferrite and martensite phases in the prepared ultrafine grain structure can be adjusted by regulating and controlling the heating temperature of the two-phase region.
Example 1
The chemical components are selected according to the mass percentage (wt.%): 0.17C, 1.5Mn, 1.5Si, 1.0Cr, 0.02P, 0.032S, and the balance Fe. Measurement of A by differential thermal analysis (DSC)3And A1The temperatures were 820.2 ℃ and 745.4 ℃ respectively. Heating the low-carbon Mn-Si-Cr series steel of the components to 1050 ℃, preserving heat for 1.5h, and then quenching the steel to room temperature; and then heating the martensitic steel to 800 ℃, preserving the heat for 1h, then carrying out warm rolling at 650 ℃, accumulating the rolling reduction by 50%, and carrying out air cooling to room temperature after rolling to obtain a 10mm thick-layer superfine grain dual-phase steel plate, wherein the volume fraction of martensite is about 40.6%, the average grain size of ferrite is 0.98 μm, and SEM and TEM tissues are respectively shown in figures 2 and 3. The mechanical properties are as follows: rp 0.2: 836MPa, Rm: 1432MPa, A: 15.8%, impact energy at room temperature (A)KV) 139.8J, 258.7J for impact work at-20 ℃ and 138J for impact work at-196 ℃.
Example 2
The chemical components are selected according to the mass percentage (wt.%): 0.23C, 2.0Mn, 1.5Si, 0.5Cr, 0.023P, 0.046S and the balance Fe. Measurement of A by differential thermal analysis (DSC)3And A1The temperatures were 813.4 ℃ and 716.7 ℃ respectively. Heating the low-carbon Mn-Si-Cr series steel of the components to 1150 ℃, preserving the heat for 2 hours, and then cooling the steel to room temperature in air; heating the martensitic steel to 760 ℃, preserving heat for 2h, warm rolling at 700 ℃, accumulating the rolling amount by 50 percent, and water quenching after rollingAnd cooling to room temperature to obtain a 20mm thick-layer superfine grain dual-phase steel plate, wherein the volume fraction of martensite is about 30 percent, and the average grain size of ferrite is 1.12 mu m. The mechanical properties are as follows: rp 0.2: 873MPa, Rm: 1538MPa, A: 14.1%, impact energy at room temperature (A)KV) 159.3J, and 271.4J of impact energy at-20 ℃,
example 3
The chemical components are selected according to the mass percentage (wt.%): 0.15C, 2.5Mn, 1.0Si, 1.0Cr, 0.036P, 0.051S, and the balance Fe. Measurement of A by differential thermal analysis (DSC)3And A1The temperatures were 803.7 ℃ and 701.7 ℃ respectively. Heating the low-carbon Mn-Si-Cr series steel of the components to 1200 ℃, preserving heat for 0.5h, and then air-cooling to room temperature; and then heating the martensitic steel to 760 ℃, preserving the heat for 2.5h, carrying out warm rolling at 700 ℃, accumulating the rolling quantity by 70%, and carrying out air cooling to room temperature after rolling to obtain a 3mm thick-layer superfine-grained dual-phase steel plate, wherein the volume fraction of martensite is about 35%, and the average grain size of ferrite is 0.86 μm. The mechanical properties are as follows: rp 0.2: 763MPa, Rm: 1362MPa, A: 18.7%, impact energy at room temperature (A)KV) 203.8J, and the impact energy at-20 ℃ is 351.2J,
example 4
The chemical components are selected according to the mass percentage (wt.%): 0.25C, 2.5Mn, 1.5Si, 1.0Cr, 0.037P, 0.031S, and the balance Fe. Measurement of A by differential thermal analysis (DSC)3And A1The temperatures were 790.6 ℃ and 733.3 ℃ respectively. Heating the low-carbon Mn-Si-Cr series steel of the components to 950 ℃, preserving the heat for 2 hours, and then cooling the steel to room temperature in air; and then heating the martensitic steel to 750 ℃, preserving the heat for 2.5h, then carrying out warm rolling at 700 ℃, accumulating the rolling amount by 70%, and carrying out air cooling to room temperature after rolling to obtain a 3mm thick-layer superfine-grained dual-phase steel plate, wherein the volume fraction of martensite is about 20%, and the average grain size of ferrite is 0.81 mu m.
The invention utilizes the tissue genetic phenomenon in the heating process of the initial martensite two-phase region, ferrite and austenite tissues with lath characteristics are obtained after the two-phase region is heated, the tissues are refined, and simultaneously, more phase interfaces are introduced into the material, thereby accelerating the grain subdivision process in the rolling process, promoting the grain refinement, obviously reducing the rolling deformation amount in the preparation process of the superfine dual-phase steel, and simultaneously solving the preparation problem of the superfine dual-phase steel with large section size. The ultra-fine grained ferrite/martensite structure with lamellar characteristics is obtained, and the impact toughness is obviously improved while the material strength and the elongation are improved.
Claims (6)
1. The layered ultra-fine grain dual-phase ferrite/martensite steel is characterized by comprising the following components in percentage by weight (wt.%): 0.15-0.25% of C, 0.5-2.0% of Cr, 1.5-3.0% of Mn, 0.7-2.50% of Si, P: < 0.05%, S: < 0.06%, the balance being Fe;
the layered superfine dual-phase steel structure is as follows: the ferrite and the martensite are alternately distributed in a layered mode, the ferrite is in an equiaxial mode, the average grain size is 1 mu m, the volume fraction of the martensite is 10-50%, the thickness of martensite strips is 0.2-2 mu m, and the distance between the martensite strips is 0.2-2 mu m.
2. The layered ultra fine grained dual phase ferrite/martensite steel as claimed in claim 1, wherein the layered ultra fine grained dual phase steel has an impact energy (A) in a temperature range of-196 ℃ to 80 ℃KV) More than 138J, abnormal toughness rise in the temperature range of-60 ℃ to 0 ℃, and the highest impact energy of more than 258J.
3. A preparation method of layered ultra-fine grained dual-phase ferrite/martensite steel is characterized by comprising the following steps: the low-carbon Mn-Si-Cr series steel comprises the following components in percentage by weight (wt.%): 0.15-0.25% of C, 0.5-2.0% of Cr, 1.5-3.0% of Mn, 0.7-2.50% of Si, P: < 0.05%, S: < 0.06%, the balance being Fe; heating low-carbon Mn-Si-Cr series steel to 900-1200 ℃ to obtain austenite, preserving heat for 0.5-2h to homogenize austenite components and coarsen crystal grains, and then air-cooling or water-quenching to room temperature to obtain a lath martensite structure;
the lath martensite structure is reheated to A1-A3Heating the steel plate in a two-phase region at a certain temperature for 0.5 to 3 hours to obtain a ferrite/austenite structure with lath characteristics;
then, the obtained ferrite/austenite structure is rolled for multiple times within the temperature range of 550-700 ℃, the accumulated rolling reduction is 40-70%, and the rolled material is subjected to air cooling or water quenching treatment; thus obtaining the layered superfine crystal dual-phase ferrite/martensite steel.
4. The method of claim 3, wherein the layered ultra-fine grained dual-phase ferrite/martensite steel comprises the following components by weight percent: 0.15-0.25% of C, 0.5-2.0% of Cr, 1.5-3.0% of Mn, 0.7-2.50% of Si, P: < 0.05%, S: < 0.06%, the balance being Fe.
5. The method of claim 3, wherein the layered ultra-fine grained dual-phase ferrite/martensite steel has a structure of: the ferrite and the martensite are alternately distributed in a layered mode, the ferrite is in an equiaxial mode, the average grain size is about 1 mu m, the volume fraction of the martensite is 10-50%, the thickness of the martensite strips is 0.2-2 mu m, and the distance between the martensite strips is 0.2-2 mu m.
6. The method as claimed in claim 3, wherein the impact energy (A) of the lamellar ultra-fine grained dual-phase ferrite/martensite steel is in the temperature range of-196 ℃ to 80 ℃KV) More than 138J, abnormal toughness rise in the temperature range of-60 ℃ to 0 ℃, and the highest impact energy of more than 258J.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201711217801.3A CN108018503B (en) | 2017-11-28 | 2017-11-28 | Layered superfine crystal dual-phase ferrite/martensite steel and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201711217801.3A CN108018503B (en) | 2017-11-28 | 2017-11-28 | Layered superfine crystal dual-phase ferrite/martensite steel and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN108018503A CN108018503A (en) | 2018-05-11 |
| CN108018503B true CN108018503B (en) | 2020-03-31 |
Family
ID=62077241
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201711217801.3A Active CN108018503B (en) | 2017-11-28 | 2017-11-28 | Layered superfine crystal dual-phase ferrite/martensite steel and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN108018503B (en) |
Families Citing this family (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109355549B (en) * | 2018-12-11 | 2020-10-02 | 东北大学 | Steel plate with high strength and excellent low-temperature toughness and manufacturing method thereof |
| CN111485083B (en) * | 2019-01-25 | 2021-09-10 | 南京理工大学 | Preparation method of ultrahigh-strength nano heterogeneous low-carbon steel |
| CN109735698B (en) * | 2019-01-31 | 2019-11-19 | 东北大学 | Manganese TRIP steel and its method of low temperature process forming in a kind of high-performance |
| CN109680223B (en) * | 2019-03-08 | 2020-10-16 | 东北大学 | Preparation method of free-cutting high-strength complex-phase non-quenched and tempered steel |
| CN110396583A (en) * | 2019-09-06 | 2019-11-01 | 西京学院 | A kind of high strength martensitic/ferrite dual phase steel strength-toughening treatment process and dual phase steel |
| CN113801984B (en) * | 2020-06-15 | 2023-03-21 | 中国科学院金属研究所 | Plastic deformation processing technology for synchronously improving strength and plasticity of low-carbon steel |
| CN112342345A (en) * | 2020-09-28 | 2021-02-09 | 东南大学 | Martensite/austenite dual-phase structure high-strength steel and preparation method thereof |
| CN113151648B (en) * | 2021-04-02 | 2022-05-24 | 南京理工大学 | Preparation method of ultrahigh-strength dual-phase isomeric stainless steel |
| CN115725896B (en) * | 2021-09-01 | 2023-11-28 | 中国科学院金属研究所 | Ultra-high-strength steel with lamellar structure and preparation method thereof |
| CN114214573B (en) * | 2021-12-17 | 2022-12-02 | 西安交通大学 | Ferrite-martensite dual-phase steel and preparation method thereof |
| CN114908226A (en) * | 2022-04-01 | 2022-08-16 | 南京钢铁有限公司 | Manufacturing method of hot forging forming composite quenching structure refined high-strength bolt |
| CN115074637B (en) * | 2022-06-25 | 2023-04-28 | 上海交通大学 | Ultra-high-strength high-toughness ultra-fine tissue low-carbon low-alloy steel and preparation method thereof |
| CN115927959B (en) * | 2022-11-15 | 2023-07-18 | 北京科技大学 | 2.2 GPa-grade low-cost low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel and preparation method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001207236A (en) * | 2000-01-26 | 2001-07-31 | Kawasaki Steel Corp | High tensile strength hot dip galvanized steel plate and producing method therefor |
| CN105568145A (en) * | 2015-12-24 | 2016-05-11 | 北京科技大学 | Cold-rolled ultrahigh-strength biphase steel plate for vehicle with corrosion resistance and preparation method thereof |
| CN106957995A (en) * | 2016-12-09 | 2017-07-18 | 燕山大学 | Fine ferrite grain/low temperature bainite two-phase mild steel and preparation method thereof |
-
2017
- 2017-11-28 CN CN201711217801.3A patent/CN108018503B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001207236A (en) * | 2000-01-26 | 2001-07-31 | Kawasaki Steel Corp | High tensile strength hot dip galvanized steel plate and producing method therefor |
| CN105568145A (en) * | 2015-12-24 | 2016-05-11 | 北京科技大学 | Cold-rolled ultrahigh-strength biphase steel plate for vehicle with corrosion resistance and preparation method thereof |
| CN106957995A (en) * | 2016-12-09 | 2017-07-18 | 燕山大学 | Fine ferrite grain/low temperature bainite two-phase mild steel and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN108018503A (en) | 2018-05-11 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN108018503B (en) | Layered superfine crystal dual-phase ferrite/martensite steel and preparation method thereof | |
| CN108018484B (en) | Cold-rolled high-strength steel having tensile strength of 1500MPa or more and excellent formability, and method for producing same | |
| CN107619993B (en) | Cold-rolled martensite steel plate with yield strength of 750MPa and manufacturing method thereof | |
| CN101613828B (en) | Super-thick steel plate for low yield ratio buildings with 460 MPa grade yield strength and manufacturing method | |
| CN103343281B (en) | A kind of lamellar two-phase high-strength and high-toughness steel and preparation method thereof | |
| CN102080192B (en) | Low-yield ratio, high-plasticity, ultrafine-grain and high-strength steel and manufacturing method thereof | |
| CN103215516A (en) | 700MPa high strength hot rolling Q&P steel and manufacturing method thereof | |
| CN101638749A (en) | Automobile steel with low cost and high strength ductility balance and preparation method thereof | |
| CN104498821B (en) | Medium-manganese high-strength steel for automobiles and production method thereof | |
| WO1999013123A1 (en) | Hot rolled steel plate to be processed having hyper fine particles, method of manufacturing the same, and method of manufacturing cold rolled steel plate | |
| CN102943169A (en) | Quenching and annealing preparation method of ultrahigh-strength thin steel plate for automobiles | |
| CN105274432A (en) | 600 MPa grade high-yield-ratio high-plasticity cold-rolled steel plate and manufacturing method thereof | |
| CN102965568B (en) | Phase toughness Low Alloy Steel Plate and preparation method thereof | |
| CN110453146A (en) | A kind of Cr alloying steel of no yield point elongation and preparation method thereof | |
| CN103233161A (en) | Low-yield-ratio high-strength hot-rolled Q&P steel and manufacturing method thereof | |
| CN108998741A (en) | Manganese phase change induction plasticity steel and preparation method thereof in ultra-high strength and toughness | |
| CN106868398A (en) | 1300MPa grades of ultra-fine grained ferrite/low temperature bainite dual-phase steel and preparation method thereof | |
| CN110484834A (en) | A kind of Cr, Mn alloying TRIP steel and preparation method thereof | |
| CN102400038A (en) | Hot-rolled dual-phase steel and production method thereof | |
| CN101906519A (en) | Manufacture method of low yield ratio surface layer ultra fine grain low-carbon steel thick plate | |
| CN110343960B (en) | Automobile steel with high cold bending property and manufacturing method thereof | |
| CN110343970B (en) | Hot-rolled high-strength-ductility medium manganese steel with lower Mn content and preparation method thereof | |
| CN110551878A (en) | Ultrahigh-strength ultrahigh-toughness low-density dual-phase layered steel plate and preparation method thereof | |
| CN103103438A (en) | High-strength and high-plasticity medium manganese cold-roll steel sheet and manufacturing method thereof | |
| CN110408861A (en) | A kind of cold rolling high strength and ductility medium managese steel and preparation method thereof having lower Mn content |
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 |