CN112342345A - Martensite/austenite dual-phase structure high-strength steel and preparation method thereof - Google Patents
Martensite/austenite dual-phase structure high-strength steel and preparation method thereof Download PDFInfo
- Publication number
- CN112342345A CN112342345A CN202011038146.7A CN202011038146A CN112342345A CN 112342345 A CN112342345 A CN 112342345A CN 202011038146 A CN202011038146 A CN 202011038146A CN 112342345 A CN112342345 A CN 112342345A
- Authority
- CN
- China
- Prior art keywords
- martensite
- austenite
- strength steel
- dual
- phase structure
- 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.)
- Pending
Links
Images
Classifications
-
- 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
-
- 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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D1/34—Methods of heating
- C21D1/44—Methods of heating in heat-treatment baths
- C21D1/46—Salt baths
-
- 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
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
-
- 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
- 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
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
-
- 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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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
The invention discloses martensite/austenite dual-phase structure high-strength steel and a preparation method thereof, wherein the high-strength steel comprises the following components in percentage by mass: 0.2-0.5: 4-7, comprising the elements Fe, C, Mn, the high strength steel being composed of a martensitic matrix and austenite particles dispersed in the martensitic matrix. The preparation method of the high-strength steel comprises the following steps: fe. C, Mn are weighed according to the proportion, smelted, annealed, forged, hot-rolled and cold-rolled, and then sequentially treated by austenitizing, medium-temperature annealing, austenite reverse transformation and medium-low temperature tempering to obtain the martensite matrix and austenite grain structure dispersed in the martensite matrix. The invention also provides a third generation advanced high-strength steel with a high-strength and high-toughness martensite/austenite composite structure.
Description
Technical Field
The invention relates to high-strength steel and a preparation method thereof, in particular to high-strength steel with a dual-phase structure and a preparation method thereof.
Background
Martensite is a supersaturated solid solution of carbon in ferrite, and is a structure in which austenite is transformed by a non-diffusion type phase transformation. The strength of martensite increases with increasing carbon content in the steel, while toughness generally shows a decreasing trend. In the design concept of the third-generation advanced high-strength steel which is developed rapidly at present, the mechanical property of the third-generation advanced high-strength steel is predicted by utilizing a simplified composite model based on Mileiko based on Matlock and the like, and the ideal structure of the third-generation advanced high-strength steel is a composite structure of a high-strength phase and metastable austenite, wherein the high-strength phase can be martensite, bainite or ultrafine grained ferrite. The high-strength phase in the structure is a main strength source of the whole structure, and the metastable austenite phase with weaker strength generates a transformation induced plasticity effect in the deformation process of the structure so as to increase the toughness of the whole structure.
At present, the existing steel structure mainly takes dispersed cementite particles in a ferrite matrix as a main part, but the structure can not meet the requirements of high strength and strong toughness at the same time; the partial structure is a two-phase structure consisting of austenite laths and martensite laths, and austenite reverse transformation occurs in the annealing process of the two-phase region, so that the strength of the obtained steel structure is still not ideal.
Disclosure of Invention
The purpose of the invention is as follows: the object of the present invention is to provide a high strength steel of martensite/austenite dual phase structure having austenite particles uniformly dispersed in a martensite matrix, which has both high strength and high toughness;
another object of the present invention is to provide a method for manufacturing a high strength steel having a martensite/austenite dual phase structure.
The technical scheme is as follows: the martensite/austenite dual-phase structure high-strength steel comprises the following components in percentage by mass: 0.2-0.5: 4-7, and the martensite/austenite dual-phase structure high-strength steel consists of a martensite matrix and austenite particles dispersed in the martensite matrix.
The preparation method of the martensite/austenite dual-phase structure high-strength steel comprises the following steps:
(1) weighing Fe, C and Mn according to mass percent, smelting into an ingot, annealing, forging, hot rolling and cold rolling to obtain a rolled plate sample, then carrying out austenitizing treatment, and cooling to room temperature to form martensite;
(2) annealing the sample obtained in the step (1) at 400-600 ℃, performing heat preservation treatment to obtain a dual-phase composite structure sample consisting of a ferrite matrix and a cementite phase, and then cooling to room temperature;
(3) and heating the annealed sample at 700-800 ℃ at a heating rate of 30-100 ℃/s, carrying out heat preservation treatment to reversely deform the ferrite matrix and the cementite particles into austenite, and cooling to room temperature to obtain the martensite/austenite dual-phase structure high-strength steel with the austenite particles dispersed in the martensite matrix.
Preferably, the dual-phase structure high-strength steel obtained in the step (3) is subjected to a tempering treatment for eliminating the brittleness of martensite.
Preferably, the time for heat preservation in the step (2) is 1-35 h.
Preferably, the time for heat preservation in the step (3) is 30s-2 min.
Preferably, the specific method of the austenitizing treatment in the step (1) is as follows: heating the sample at 800-900 ℃ in an inert atmosphere, and preserving the heat for 10min-1 h.
Preferably, the tempering treatment step is: and (3) preserving the temperature of the sample in an oil bath furnace at 200-250 ℃ for 0.5-2h, and then cooling to room temperature.
Preferably, the tempering treatment step is: and (3) preserving the temperature of the sample in a salt bath furnace at 250-400 ℃ for 30s-1h, and then cooling to room temperature.
The annealed structure of martensite is a dual-phase composite structure consisting of a ferrite matrix with lower strength (manganese-poor zone) and a cementite phase with higher brittleness (manganese-rich zone). After the organization is subjected to the transient austenite reverse transformation treatment, because the diffusion rate of carbon atoms is far higher than that of manganese atoms, in the process of rapidly heating to the austenite reverse transformation temperature and temporarily preserving heat, ferrite and carburized phases are both reversely transformed into austenite due to rapid diffusion of the carbon atoms, and the distribution of the manganese elements is kept unchanged. During subsequent rapid cooling, the carburized phase (manganese-rich zone) austenite particles remain to room temperature due to their higher stability than the manganese-poor zone, while the ferritic matrix (manganese-poor zone) austenite transforms into a martensitic matrix, eventually forming a composite structure with uniformly dispersed austenite particles in the martensitic matrix. The martensite matrix has higher strength but poorer toughness, but because the austenite particles which can generate phase transformation induced plasticity are embedded in the martensite matrix, the toughness of the martensite is greatly improved, thereby forming the third generation advanced high-strength steel with a martensite/austenite composite structure with high strength and high toughness.
Has the advantages that: compared with the prior art, the invention has the following remarkable effects: 1. under the composition of low-carbon and medium-carbon steel, the structure formed by a martensite matrix and austenite particles dispersed in the martensite matrix has high strength and better toughness. 2. The annealed martensite structure is used as a matrix, the enrichment effect of carbon and manganese elements in cementite particles is utilized, the ferrite matrix and the ferrite matrix are inverted into austenite through a rapid temperature rise condition, and the dispersed austenite particle structure in the martensite matrix formed after air cooling has high strength and high toughness. 3. Compared with the reverse transformation of partial austenite in the annealing process of the critical zone, the reverse transformation of the austenite is carried out in the austenitizing process after annealing, the martensite content in the final structure is higher, and therefore the strength is higher.
Drawings
FIG. 1 is a scanning electron micrograph of a dual-phase high-strength steel in example 1;
FIG. 2 is a tensile curve after annealing and subsequent austenite reverse transformation for example 1;
FIG. 3 is a schematic flow chart of a preparation method of the dual-phase structure high-strength steel of the present invention.
Detailed Description
The invention is described in further detail below with reference to the drawings.
Example 1
The martensite/austenite dual-phase composite high-strength steel comprises the following components in percentage by mass: c: 0.2, Mn: 5 and the balance of Fe. The preparation method of the martensite/austenite dual-phase composite high-strength steel comprises the following steps:
(1) austenitizing treatment: weighing Fe, C and Mn according to mass percent, smelting into an ingot, annealing, forging, hot rolling and cold rolling to obtain a cold-rolled sheet sample, sampling from the middle part of the cold-rolled sheet sample, carrying out austenitizing treatment on the sample at 850 ℃ in a tubular furnace filled with industrial argon atmosphere, preserving heat for 10min, and then air-cooling to room temperature to form martensite; wherein the air cooling is cooling under the air condition;
(2) annealing treatment: putting the martensite sample into a 550 ℃ salt bath furnace for annealing, preserving heat for 3 hours to form cementite particles in a ferrite matrix, and air-cooling to room temperature;
(3) austenite reverse transformation treatment: placing the annealed sample into a salt bath furnace, heating to 730 ℃ at the heating rate of 30 ℃/second, preserving heat for 2min to ensure that cementite particles are reversed to become austenite particles, a ferrite matrix is reversed to become an austenite matrix, the manganese content in the austenite matrix is reserved, air cooling to room temperature is carried out, the austenite matrix is reversed to become a martensite matrix, and the austenite particles still stably exist to form a dual-phase structure of the austenite particles dispersed and the martensite matrix;
(4) tempering treatment: and then keeping the temperature of the sample in an oil bath furnace at 200 ℃ for 30min to eliminate the brittleness of martensite, and air-cooling the sample to room temperature.
The scanning electron micrograph of the dual-phase structure high-strength steel of the present example is shown in fig. 1, in which the black fine regions eroded away by the corrosive liquid are austenite particles, and the remaining gray regions are a martensite matrix. The engineering stress-strain tensile curve of the dual-phase composite high-strength steel of the embodiment is shown in fig. 2, wherein the solid line represents annealed martensite, the dotted line represents the mechanical property of the structure after the austenite reverse phase transformation, and the strength of the two-phase structure generated after the austenite reverse phase transformation is greatly improved compared with that before the austenite reverse phase transformation. A schematic of the thermal processing scheme for preparing the biphasic structure is shown in FIG. 3.
Example 2
The dual-phase composite high-strength steel comprises the following components in percentage by mass: c: 0.4, Mn: 5, balance Fe. The basic steps of the preparation method of the dual-phase composite high-strength steel are the same as those of the embodiment 1, except that:
in the step (1), the austenitizing treatment temperature is 800 ℃, and the temperature is kept for 1 h;
in the step (2), the martensite sample is put into a salt bath furnace at 500 ℃ for annealing, and the temperature is kept for 24 hours;
in the step (3), the temperature rise rate is 100 ℃/s, the temperature is raised to 800 ℃, and the temperature is kept for 20 s;
in the step (4), the sample is kept warm for 30s in a salt bath furnace at 400 ℃.
Example 3
The dual-phase composite high-strength steel comprises the following components in percentage by mass: c: 0.2, Mn: 7, balance Fe. The basic steps of the preparation method of the dual-phase composite high-strength steel are the same as those of the embodiment 1, except that:
in the step (1), the temperature of austenitizing treatment is 850 ℃, and the temperature is kept for 30 min;
in the step (2), the martensite sample is put into a salt bath furnace at 520 ℃ for annealing, and the temperature is kept for 22 h;
in the step (3), the temperature rise rate is 50 ℃/s, the temperature is raised to 760 ℃, and the temperature is kept for 1 min;
in step (4), the sample is held in an oil bath at 250 ℃ for 30 seconds.
Example 4
The dual-phase composite high-strength steel comprises the following components in percentage by mass: c: 0.1, Mn: 7, balance Fe. The basic steps of the preparation method of the dual-phase composite high-strength steel are the same as those of the embodiment 1, except that:
in the step (1), the temperature of austenitizing treatment is 900 ℃, and the temperature is kept for 5 min;
in the step (2), the martensite sample is put into a 600 ℃ salt bath furnace for annealing, and the temperature is kept for 1 h;
in the step (3), the temperature rise rate is 70 ℃/s, the temperature is raised to 780 ℃, and the temperature is kept for 20 s;
in the step (4), the sample is kept in an oil bath furnace at 200 ℃ for 1 h.
Example 5
The dual-phase composite high-strength steel comprises the following components in percentage by mass: c: 0.5, Mn: 6, balance Fe. The basic steps of the preparation method of the dual-phase composite high-strength steel are the same as those of the embodiment 1, except that:
in the step (1), the temperature of austenitizing treatment is 820 ℃, and the temperature is kept for 10 min;
in the step (2), the martensite sample is put into a 560 ℃ salt bath furnace for annealing, and the temperature is kept for 10 hours;
in the step (2), the temperature is increased to 740 ℃ for 50s at the heating rate of 100 ℃/s;
in the step (4), the annealed sample is placed into an oil bath furnace at 450 ℃ and is kept warm for 20 s.
Claims (8)
1. The martensite/austenite dual-phase structure high-strength steel is characterized by comprising the following components in percentage by mass: 0.2-0.5: 4-7, and the martensite/austenite dual-phase structure high-strength steel consists of a martensite matrix and austenite particles dispersed in the martensite matrix.
2. A method for manufacturing a high-strength steel having a martensite/austenite dual phase structure according to claim 1, comprising the steps of:
(1) weighing Fe, C and Mn according to mass percent, smelting into an ingot, annealing, forging, hot rolling and cold rolling to obtain a rolled plate sample, then carrying out austenitizing treatment, and cooling to room temperature to form martensite;
(2) annealing the sample obtained in the step (1) at 400-650 ℃, performing heat preservation treatment to obtain a dual-phase composite structure sample consisting of a ferrite matrix and a cementite phase, and then cooling to room temperature;
(3) and heating the annealed sample at 700-800 ℃ at a heating rate of 30-100 ℃/s, carrying out heat preservation treatment to reversely deform the ferrite matrix and the cementite particles into austenite, and cooling to room temperature to obtain the martensite/austenite dual-phase structure high-strength steel with the austenite particles dispersed in the martensite matrix.
3. The method for producing a high-strength steel having a martensite/austenite dual-phase structure according to claim 2, wherein the high-strength steel having a martensite/austenite dual-phase structure obtained in the step (3) is subjected to a tempering treatment for eliminating brittleness of martensite.
4. The method for preparing the high-strength steel having the martensite/austenite dual-phase structure according to claim 2, wherein the holding time in the step (2) is 1 to 35 hours.
5. The method for preparing the high-strength steel with the martensite/austenite dual-phase structure according to claim 2, wherein the holding time in the step (3) is 30s-2 min.
6. The method for preparing the martensite/austenite dual-phase structure high-strength steel according to claim 2, wherein the specific method of the austenitizing treatment in the step (1) is as follows: heating the sample at 800-900 ℃ in an inert atmosphere, and preserving the heat for 10min-1 h.
7. The method for producing the high-strength steel having the martensite/austenite dual-phase structure according to claim 2, wherein the tempering step comprises: and (3) preserving the temperature of the sample in an oil bath furnace at 200-250 ℃ for 30s-2h, and then cooling to room temperature.
8. The method for producing the high-strength steel having the martensite/austenite dual-phase structure according to claim 2, wherein the tempering step comprises: and (3) preserving the temperature of the sample in a salt bath furnace at 250-400 ℃ for 30s-1h, and then cooling to room temperature.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011038146.7A CN112342345A (en) | 2020-09-28 | 2020-09-28 | Martensite/austenite dual-phase structure high-strength steel and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011038146.7A CN112342345A (en) | 2020-09-28 | 2020-09-28 | Martensite/austenite dual-phase structure high-strength steel and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN112342345A true CN112342345A (en) | 2021-02-09 |
Family
ID=74361086
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202011038146.7A Pending CN112342345A (en) | 2020-09-28 | 2020-09-28 | Martensite/austenite dual-phase structure high-strength steel and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112342345A (en) |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103243275A (en) * | 2013-04-03 | 2013-08-14 | 北京交通大学 | Preparation method of bainite/martensite/austenite composite high-strength steel |
| CN103695618A (en) * | 2013-12-16 | 2014-04-02 | 北京科技大学 | Thermomechanical treatment method for preparing submicron complex phase steel |
| CN108018503A (en) * | 2017-11-28 | 2018-05-11 | 西安交通大学 | A kind of stratiform Ultra-fine Grained dual phase ferritic/martensite steel and preparation method thereof |
| CN108251759A (en) * | 2018-02-01 | 2018-07-06 | 南京理工大学 | The martensitic stain less steel and its manufacturing method of reversed austenite toughening |
| CN110468263A (en) * | 2019-09-12 | 2019-11-19 | 北京理工大学 | A kind for the treatment of process obtaining the advanced high-strength steel of high-strength and high ductility |
-
2020
- 2020-09-28 CN CN202011038146.7A patent/CN112342345A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103243275A (en) * | 2013-04-03 | 2013-08-14 | 北京交通大学 | Preparation method of bainite/martensite/austenite composite high-strength steel |
| CN103695618A (en) * | 2013-12-16 | 2014-04-02 | 北京科技大学 | Thermomechanical treatment method for preparing submicron complex phase steel |
| CN108018503A (en) * | 2017-11-28 | 2018-05-11 | 西安交通大学 | A kind of stratiform Ultra-fine Grained dual phase ferritic/martensite steel and preparation method thereof |
| CN108251759A (en) * | 2018-02-01 | 2018-07-06 | 南京理工大学 | The martensitic stain less steel and its manufacturing method of reversed austenite toughening |
| CN110468263A (en) * | 2019-09-12 | 2019-11-19 | 北京理工大学 | A kind for the treatment of process obtaining the advanced high-strength steel of high-strength and high ductility |
Non-Patent Citations (2)
| Title |
|---|
| 李爱农，刘钰如主编: "《工程材料及应用》", 31 January 2019, 武汉：华中科技大学出版社 * |
| 河北工学院王健安: "《高等学校试用教材 金属学与热处理 热加工专业用 下》", 31 July 1980, 北京：机械工业出版社 * |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| Srivastava et al. | Microstructural and mechanical characterization of C–Mn–Al–Si cold-rolled TRIP-aided steel | |
| CN105648317B (en) | Manganese Q&P steel cold rolled annealed plate and its preparation process in a kind of high-strength and high-plasticity | |
| CN103215516B (en) | A kind of 700MPa grade high-strength hot-rolled Q & P steel and manufacture method thereof | |
| CN107127212B (en) | The method that super rapid heating technique produces manganese cold-rolled steel sheet in high strength and ductility | |
| Zhang et al. | Enhanced strain hardening and microstructural characterization in a low carbon quenching and partitioning steel with partial austenization | |
| CN108431279A (en) | Automotive part with high intensity and excellent durability and its manufacturing method | |
| CN111455146B (en) | Strengthening and toughening treatment method for low-alloy martensitic steel and martensitic steel | |
| CN107988550A (en) | A kind of pressurized-water reactor nuclear power plant pressure vessel supporting steel and its manufacture method | |
| CN103103438B (en) | High-strength and high-plasticity medium manganese cold-roll steel sheet and manufacturing method thereof | |
| Huang et al. | Combining a novel cyclic pre-quenching and two-stage heat treatment in a low-alloyed TRIP-aided steel to significantly enhance mechanical properties through microstructural refinement | |
| CN112063931B (en) | Low-carbon medium-manganese high-residual-austenite high-toughness steel and heat treatment method thereof | |
| CN114032459B (en) | Preparation method of high-strength-toughness low-yield-ratio medium-thickness steel plate with yield strength of 690MPa | |
| CN109694997B (en) | Heat treatment process for improving mechanical property of Fe-Mn-Al-C dual-phase steel by utilizing gamma → alpha isomerous transformation | |
| CN107012398A (en) | A kind of Nb-microalloying TRIP steel and preparation method thereof | |
| CN110055465B (en) | Medium-manganese ultrahigh-strength steel and preparation method thereof | |
| CN108950150A (en) | Manganese Q&P steel heat treatment process in superhigh intensity cold rolling based on complete austenitizing | |
| JP5614329B2 (en) | Steel sheet for soft nitriding treatment and method for producing the same | |
| CN108866443B (en) | Normalizing type low-yield-ratio high-strength steel plate and preparation method thereof | |
| CN116555672A (en) | High-strength and high-toughness medium manganese steel plate and preparation method thereof | |
| CN112342345A (en) | Martensite/austenite dual-phase structure high-strength steel and preparation method thereof | |
| CN104988295A (en) | Heat treatment method for improving medium-carbon non-quenched and tempered steel connecting rod cracking performance | |
| CN106929756B (en) | Bearing steel and preparation method thereof | |
| CN111733366B (en) | Aluminum-containing cold-rolled ultrahigh-strength steel and preparation method and application thereof | |
| CN114717393A (en) | Rapid isothermal spheroidizing annealing method for 42CrMoA steel bar | |
| CN113832408A (en) | Fe-15Mn-8Al-0.3C ferrite-austenite dual-phase low-density steel and heat treatment 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 | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20210209 |
|
| RJ01 | Rejection of invention patent application after publication |