CN115679089B - Forging and cooling control process for regulating and controlling microstructure of low-carbon bainite non-quenched and tempered steel for front axle - Google Patents
Forging and cooling control process for regulating and controlling microstructure of low-carbon bainite non-quenched and tempered steel for front axle Download PDFInfo
- Publication number
- CN115679089B CN115679089B CN202211328174.1A CN202211328174A CN115679089B CN 115679089 B CN115679089 B CN 115679089B CN 202211328174 A CN202211328174 A CN 202211328174A CN 115679089 B CN115679089 B CN 115679089B
- Authority
- CN
- China
- Prior art keywords
- cooling
- forging
- quenched
- tempered steel
- low
- 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
- 238000001816 cooling Methods 0.000 title claims abstract description 83
- 238000005242 forging Methods 0.000 title claims abstract description 68
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 54
- 239000010959 steel Substances 0.000 title claims abstract description 54
- 229910001563 bainite Inorganic materials 0.000 title claims abstract description 52
- 238000000034 method Methods 0.000 title claims abstract description 41
- 229910052799 carbon Inorganic materials 0.000 title claims abstract description 37
- 230000001276 controlling effect Effects 0.000 title claims abstract description 13
- 230000001105 regulatory effect Effects 0.000 title claims abstract description 11
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 18
- 238000010583 slow cooling Methods 0.000 claims abstract description 14
- 230000006698 induction Effects 0.000 claims abstract description 12
- 238000010438 heat treatment Methods 0.000 claims description 19
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 229910052720 vanadium Inorganic materials 0.000 claims description 6
- 238000004321 preservation Methods 0.000 claims description 5
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims description 4
- 229910052698 phosphorus Inorganic materials 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims 1
- 239000007769 metal material Substances 0.000 abstract description 2
- 238000010080 roll forging Methods 0.000 abstract 1
- 238000009966 trimming Methods 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 12
- 239000000463 material Substances 0.000 description 5
- 230000033228 biological regulation Effects 0.000 description 3
- 239000006185 dispersion Substances 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 238000013021 overheating Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000005452 bending Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
Classifications
-
- 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
- Y02P10/25—Process efficiency
Landscapes
- Heat Treatment Of Steel (AREA)
- Forging (AREA)
Abstract
The invention belongs to the field of metal materials, and relates to a forging and cooling control process for regulating and controlling a microstructure of low-carbon bainite non-quenched and tempered steel for a front shaft. The process comprises the following steps: the front axle with the diameter phi of 130mm is heated by a low-carbon bainite non-quenched and tempered steel bar through a blanking and medium-frequency induction furnace, is controlled and cooled by a cooling control line after roll forging, die forging and trimming, and is controlled and cooled by a sectional cooling mode of quick cooling and slow cooling. The microstructure obtained by the process is granular bainitic structure and a small amount of ferrite structure which is distributed in a tiny and dispersed way, the proportion of the bainitic structure accounts for 90-95%, the tensile strength R m is 990-1050 MPa, the yield strength R p0.2 is 650-670 MPa, the room temperature impact energy A KU is 60-63J, and meanwhile, the microstructure has proper Vickers hardness, and the hardness is controlled between 370 and 380 HV.
Description
Technical Field
The invention belongs to the field of metal materials, and relates to high-strength high-toughness low-carbon bainite non-quenched and tempered steel for a front shaft, in particular to a forging and cooling control process for regulating and controlling microstructure of the high-strength high-toughness low-carbon bainite non-quenched and tempered steel for the front shaft.
Background
The front axle is one of the most important safety parts as a key structure and safety component in the chassis of an automobile. The front axle is simultaneously subjected to alternating loads such as bending load and impact load, so that the strength and toughness of the front axle material are required to be well matched. The mechanical properties of the quenched and tempered steel front axle are stable, but a great amount of energy consumption and other consumption are generated in the heat treatment process, so that the working procedure and the production cost are increased. The non-quenched and tempered steel is called green steel, and is mainly characterized by microalloying and obtaining the proper mechanical properties of the product through a forging (rolling) and cooling control technology, so that the traditional quenching and tempering process is omitted, and more automobile parts such as automobile front axles try to adopt the non-quenched and tempered steel. The related research of non-quenched and tempered steel front axles of various factories has been developed a few years ago, but the research of control technology for precisely controlling the material organization property, especially the secondary forming process, is still lack, so the non-quenched and tempered front axles have not been widely used.
As the bainite non-quenched and tempered steel has high deformation temperature and small and uneven deformation in the secondary forging process, when the forging is subjected to cooling transformation, proeutectoid ferrite is easy to be separated out in a net shape along the prior austenite grain boundary, and a coarse ferrite-bainite structure is obtained, so that the strength and toughness are both unfavorable, and the application of the bainite non-quenched and tempered steel to high-strength and high-toughness automobile parts is limited. Therefore, the bainitic non-quenched and tempered steel for the front axle has high toughness and the matching of microstructure should be regulated and controlled at the same time, so that coarse reticular distributed ferrite is changed into small blocky ferrite with fine dispersion distribution as much as possible. The matching of bainite and ferrite in the low-carbon bainite type non-quenched and tempered steel structure for the front axle is regulated and controlled in a sectional cooling mode after forging, so that the low-carbon bainite type non-quenched and tempered steel structure has good toughness.
In the patent application 'a V microalloyed high strength and toughness bainite non-quenched and tempered steel, a controlled forging and cooling process and a production process thereof', the patent application number 202010152284.1 discloses a V microalloyed high strength and toughness bainite non-quenched and tempered steel and a controlled forging and cooling process thereof, but the cooling mode is divided into three sections of controlled cooling, and the cooling system is completely different from the invention, and is applicable to V, ti composite microalloyed bainite non-quenched and tempered steel, and is not applicable to lower-carbon bainite non-quenched and tempered steel for a front shaft only with V microalloying. Furthermore, patent 202010152284.1 is focused on the regulation of mechanical properties of materials, whereas the regulation of microstructure matching is not involved.
Disclosure of Invention
The invention aims to provide a forging and cooling control process for regulating and controlling a low-carbon bainite type non-quenched and tempered steel microstructure for a front shaft, which is used for treating the low-carbon bainite type non-quenched and tempered steel microstructure for the front shaft by the process, wherein the microstructure of the low-carbon bainite type non-quenched and tempered steel for the front shaft is a granular bainite structure and a small amount of ferrite structures distributed in a fine dispersion manner, the proportion of the bainite structure is 90-95%, the tensile strength R m is 990-1050 MPa, the yield strength R p0.2 is 650-670 MPa, the room temperature impact energy A KU is 60-63J, and meanwhile, the hardness is controlled between 370 and 380 HV.
The low-carbon bainite non-quenched and tempered steel for the front axle comprises the following chemical components in percentage by mass ：0.20％～0.23％C、0.20％～0.40％Si、1.8％～1.9％Mn、0.40％～0.50％Cr、0.10％～0.15％V、0.02％～0.04％Al、0.025％～0.045％S、P≤0.025％、Ni≤0.10％、Mo≤0.05％、0.010％～0.015％N, and the balance of Fe and unavoidable impurities. Compared with the composite microalloying of the bainite non-quenched and tempered steel V, ti in the patent 202010152284.1, the material used in the invention is V microalloying low-carbon bainite non-quenched and tempered steel, and the contents of C, mn and Cr elements are lower, and the N content is higher, so that the toughness of the steel is improved.
The invention relates to a forging and cooling control process for regulating and controlling a microstructure of low-carbon bainite non-quenched and tempered steel for a front shaft, wherein the low-carbon bainite non-quenched and tempered steel comprises the following components in percentage by mass ：0.20％～0.23％C、0.20％～0.40％Si、1.8％～1.9％Mn、0.40％～0.50％Cr、0.10％～0.15％V、0.02％～0.04％Al、0.025％～0.045％S、P≤0.025％、Ni≤0.10％、Mo≤0.05％、0.010％～0.015％N, and the balance of Fe and unavoidable impurities; the main process flow is as follows: phi 130mm bar material, medium frequency induction heating, forging control and cooling control, wherein the forging control and cooling control process comprises the following steps: the front axle with the diameter of phi 130mm is fed with low-carbon bainite non-quenched and tempered steel bar, then is subjected to frequency induction heating to a certain temperature, is preserved for a certain time, is forged at a certain temperature, and is subjected to controlled cooling by adopting a sectional cooling mode of quick cooling and slow cooling after forging.
Further, the invention mainly comprises the following steps:
(1) The medium frequency induction heating process comprises the following steps: heating a bainite non-quenched and tempered steel bar with the diameter of phi 130mm to be fully austenitized by medium frequency induction, wherein the austenitizing heating temperature is 1100-1200 ℃, the heat preservation time is 1-2 min, and forging;
(2) The forging and cooling control process comprises the following steps: the austenitized bainite non-quenched and tempered steel bar is forged, the final forging temperature is 950-1000 ℃, cooling is performed on a cooling line after the forging is finished, cooling is performed in a controlled manner by a sectional cooling mode of quick cooling firstly and then slow cooling, the steel bar is immediately and quickly cooled to 500-550 ℃ after forging, then slowly cooled to room temperature, the quick cooling speed is 3-5 ℃/s, and the slow cooling speed is 0.5-1 ℃/s.
In the technical scheme, the induction heating temperature is 1100-1200 ℃. Too low a heating temperature may deteriorate the forgings forgeability; and the excessive heating temperature is easy to cause overheating and overburning of the forging, and coarse grains, which is unfavorable for obtaining target tissues and performances.
The heat preservation time is 1-2 min. Too short heating time, insufficient austenitization, too long austenitization leads to coarsening of austenite grains, which is also unfavorable for obtaining target structure and performance, and reduces production efficiency.
The final forging temperature is 950-1000 ℃. Too high forging temperature can cause coarse microstructure and reduced toughness; the forging temperature is too low, the forging is easy to crack, the equipment is also not forged, and the equipment capacity is not allowed.
The controlled cooling process is a sectional cooling mode of quick cooling firstly and then slow cooling, wherein the quick cooling is firstly carried out to 500-550 ℃, and then the slow cooling is carried out so as to quickly avoid a ferrite transformation zone and obtain more granular bainitic structures.
The reason for adopting the forging and cooling control process is as follows: the coarse reticular ferrite structure is effectively controlled, and the granular bainite and a small amount of fine dispersed ferrite structure are obtained, so that the hardness is proper and the toughness is good. Compared with patent 202010152284.1, the invention is a forging and cooling control process suitable for regulating and controlling the microstructure of the high-strength high-toughness low-carbon bainite type non-quenched and tempered steel for the front axle, which is independently added with microalloy elements V, can effectively regulate and control the structure and performance of steel, has great difference in the aspects of process flow and parameter setting, and is concretely as follows:
(1) The medium frequency induction heating process comprises the following steps: in the invention, the rolled bar with the diameter of 130mm is heated to 1100-1200 ℃ by adopting an intermediate frequency induction heating mode, and the heat preservation time is 1-2 min. The heating temperature in patent 202010152284.1 is 1220-1270 deg.C, and no mention is made of the holding time. The heating temperature and the heat preservation time are set to fully austenitize the bar and improve the forgeability of the forging, so that the problems of overheating, overburning and the like of the forging are prevented.
(2) The cold control process after forging: in the invention, after the forging is finished, the cooling line is subjected to controlled cooling, the sectional cooling mode of quick cooling and slow cooling is performed, the temperature is immediately and quickly cooled to 500-550 ℃ after the forging, then the temperature is slowly cooled to room temperature, the cooling speed of the quick cooling is 3-5 ℃/s, the cooling speed of the slow cooling is 0.5-1 ℃/s, and the process can quickly avoid a ferrite transformation area to obtain more granular bainitic structures. In patent 202010152284.1, natural cooling is adopted on a cooling control line after forging is finished, strong air cooling is started when the surface temperature of the part reaches 800+/-10 ℃, and slow cooling is started when the surface temperature of the part reaches 400+/-10 ℃. The cooling rate of the strong wind cooling is 0.8 ℃/s to 2.4 ℃/s.
The high-strength high-toughness low-carbon bainite non-quenched and tempered steel for the front axle is subjected to V microalloying, so that the content of C, mn and Cr elements is reduced and the content of N is increased, and the matching of microstructure regulation and toughness is realized through a controlled forging and cooling process for regulating and controlling the microstructure of the high-strength high-toughness low-carbon bainite non-quenched and tempered steel for the front axle.
After the treatment by the process method, the microstructure of the low-carbon bainite non-quenched and tempered steel for the front axle is a granular bainitic structure and a small amount of ferrite structures which are distributed in a tiny and dispersed way, the proportion of the bainitic structure is 90-95%, the tensile strength R m is 990-1050 MPa, the yield strength R p0.2 is 650-670 MPa, the room-temperature impact energy A KU is 60-63J, and meanwhile, the low-carbon bainite non-quenched and tempered steel has proper Vickers hardness, and the hardness is controlled between 370-380 HV.
Drawings
FIG. 1 is a microstructure view of the bainitic non-quenched and tempered steel in example 1;
FIG. 2 is a microstructure map of the bainitic non-quenched and tempered steel in example 2;
FIG. 3 is a structural morphology diagram of the bainitic non-quenched and tempered steel of comparative example 1;
FIG. 4 is a microstructure chart of the bainitic non-quenched and tempered steel of comparative example 2.
Detailed Description
The low-carbon bainite non-quenched and tempered steel for the front axle comprises the following chemical components in percentage by mass: 0.22% C, 0.34% Si, 1.86% Mn, 0.02% P, 0.034% S, 0.46% Cr, 0.03% Ni, 0.01% Mo, 0.11% V, 0.022% Al, 0.0126% N, and the balance being Fe.
The parameters of the forging and cooling control process adopted in the embodiment are shown in table 1, the microstructure photo of the forging is shown in fig. 1, and the microstructure proportion and the mechanical property are shown in table 2. It can be seen that after controlled cooling by the sectional cooling method of rapid cooling followed by slow cooling, the microstructures of examples 1 and 2 are basically composed of granular bainite, and a small amount of fine dispersed ferrite structure is present. In example 1, after controlled forging and cooling, the bainitic structure content is 85%, the tensile strength is 999MPa, the yield strength is 658MPa, the room temperature impact energy A KU is 62.4J, and the Vickers hardness is 373HV; example 2 after controlled forging and cooling, the bainitic structure content was 90%, the tensile strength was 1049MPa, the yield strength was 671MPa, the impact energy a KU was 61.6J, and the vickers hardness was 379HV. After the forging and cooling control process, the microstructure of the low-carbon bainite non-quenched and tempered steel for the front axle is a ferrite structure with granular bainite and a small amount of fine dispersion distribution, the content of the bainite structure is 85-90%, the tensile strength R m is 990-1050 MPa, the yield strength R p0.2 is 650-670 MPa, the room temperature impact energy A KU is 60-63J, and the Vickers hardness is 370-380 HV.
The process parameters for controlling forging and cooling used in comparative example 1 are shown in table 1. The microstructure photograph of the forging piece after the forging and cooling control is shown in fig. 2, and the microstructure proportion and the mechanical property are shown in table 2. It can be seen that the microstructure of comparative example 1 after controlled forging and cooling consisted essentially of granular bainite + coarse reticulated ferrite. Comparative example 1 had a tensile strength of 948MPa, a yield strength of 607MPa, a room temperature impact energy A KU of 66.5J and a Vickers hardness of 320HV after controlled forging and cooling. Therefore, after the forging and cooling control process is adopted, the ferrite content in the forging structure is more and the forging structure is distributed in a net shape, the impact energy is higher, the strength is too low, and the hardness is also lower.
The process parameters for controlling forging and cooling used in comparative example 2 are shown in table 1. The microstructure photograph of the forging piece after the forging and cooling control is shown in fig. 2, and the microstructure proportion and the mechanical property are shown in table 2. It can be seen that the microstructure of comparative example 2 consisted of granular bainite + lath bainite + reticulated ferrite + a small amount of martensite after controlled forging and cooling. Comparative example 2 had a tensile strength of 1117MPa, a yield strength of 679MPa, a room temperature impact energy A KU of 33.5J, and a Vickers hardness of 392HV after controlled forging and cooling. It can be seen that after the forging and cooling control process, two granular and lath-shaped bainitic structures and a small amount of martensite appear in the forge piece structure, ferrite is distributed in a net shape, the strength is higher, the impact work is lower, and the hardness is higher.
Table 1 the controlled forging and cooling process parameters used in the examples and comparative examples
| Numbering device | Intermediate frequency induction heating temperature | Holding time | Final forging temperature | Cold control mode after forging | Post-forging cooling rate |
| Example 1 | 1200℃ | 1min | 1000℃ | Segmented cooling | 3℃/s→1℃/s |
| Example 2 | 1200℃ | 1min | 1000℃ | Segmented cooling | 5℃/s→1℃/s |
| Comparative example 1 | 1200℃ | 1min | 1000℃ | Direct slow cooling | 1℃ |
| Comparative example 2 | 1200℃ | 1min | 1000℃ | Direct quick cooling | 3℃ |
TABLE 2 Bainite content and mechanical Properties after treatment of examples and comparative examples
Claims (2)
1. A forging and cooling control process for regulating and controlling a microstructure of low-carbon bainite non-quenched and tempered steel for a front shaft is characterized in that the low-carbon bainite non-quenched and tempered steel comprises ：0.20％～0.23％C、0.20％～0.40％Si、1.8％～1.9％Mn、0.40％～0.50％Cr、0.10％～0.15％V、0.02％～0.04％Al、0.025％～0.045％S、P≤0.025％、Ni≤0.10％、Mo≤0.05％、0.010％～0.015％N, mass percent of Fe and unavoidable impurities as the rest; the forging and cooling control process comprises the following steps of: the front axle with the diameter of phi 130mm is fed by a low-carbon bainite non-quenched and tempered steel bar, then is subjected to frequency induction heating to a certain temperature, is preserved for a certain time, is forged at a certain temperature, and is subjected to controlled cooling by adopting a sectional cooling mode of quick cooling and slow cooling after forging;
After the treatment by the process method, the microstructure of the low-carbon bainite non-quenched and tempered steel for the front axle is a granular bainitic structure and a small amount of ferrite structures which are distributed in a tiny and dispersed way, the proportion of the bainitic structure is 90-95%, the tensile strength R m is 990-1050 MPa, the yield strength R p0.2 is 650-670 MPa, the room-temperature impact energy A KU is 60-63J, and meanwhile, the low-carbon bainite non-quenched and tempered steel has proper Vickers hardness, and the hardness is controlled between 370-380 HV.
2. The forging and cooling control process for controlling a microstructure of low-carbon bainite non-quenched and tempered steel for a front axle according to claim 1, is characterized by comprising the following steps:
(1) The medium frequency induction heating process comprises the following steps: heating a bainite non-quenched and tempered steel bar with the diameter of phi 130mm to be fully austenitized by medium frequency induction, wherein the austenitizing heating temperature is 1100-1200 ℃, the heat preservation time is 1-2 min, and forging;
(2) The forging and cooling control process comprises the following steps: the austenitized bainite non-quenched and tempered steel bar is forged, the final forging temperature is 950-1000 ℃, cooling is performed on a cooling line after the forging is finished, cooling is performed in a controlled manner by a sectional cooling mode of quick cooling firstly and then slow cooling, the steel bar is immediately and quickly cooled to 500-550 ℃ after forging, then slowly cooled to room temperature, the quick cooling speed is 3-5 ℃/s, and the slow cooling speed is 0.5-1 ℃/s.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211328174.1A CN115679089B (en) | 2022-10-27 | 2022-10-27 | Forging and cooling control process for regulating and controlling microstructure of low-carbon bainite non-quenched and tempered steel for front axle |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211328174.1A CN115679089B (en) | 2022-10-27 | 2022-10-27 | Forging and cooling control process for regulating and controlling microstructure of low-carbon bainite non-quenched and tempered steel for front axle |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN115679089A CN115679089A (en) | 2023-02-03 |
| CN115679089B true CN115679089B (en) | 2024-09-06 |
Family
ID=85100204
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202211328174.1A Active CN115679089B (en) | 2022-10-27 | 2022-10-27 | Forging and cooling control process for regulating and controlling microstructure of low-carbon bainite non-quenched and tempered steel for front axle |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115679089B (en) |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109295391A (en) * | 2018-11-22 | 2019-02-01 | 钢铁研究总院 | A kind of high-strength tenacity non-hardened and tempered steel and preparation method thereof |
Family Cites Families (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0762204B2 (en) * | 1989-12-13 | 1995-07-05 | 新日本製鐵株式会社 | Manufacturing method of high-toughness non-heat treated steel for hot forging and its steel bars and parts |
| JP2888135B2 (en) * | 1994-05-26 | 1999-05-10 | 住友金属工業株式会社 | High durability high strength non-heat treated steel and its manufacturing method |
| CN102877001A (en) * | 2012-10-29 | 2013-01-16 | 北京科技大学 | Low-carbon tempering-free all-bainite structure plastic mould steel and preparation method thereof |
| CN104651753A (en) * | 2014-11-28 | 2015-05-27 | 南京钢铁股份有限公司 | Non-quenched and tempered steel for heavy truck balance shaft and manufacturing method thereof |
| WO2016151345A1 (en) * | 2015-03-23 | 2016-09-29 | Arcelormittal | Parts with a bainitic structure having high strength properties and manufacturing process |
| CN111020147B (en) * | 2019-12-12 | 2021-11-16 | 舞阳钢铁有限责任公司 | Rolling production method of electric slag finished steel plate for nuclear power flywheel |
| CN114892079A (en) * | 2022-04-26 | 2022-08-12 | 湖南华菱湘潭钢铁有限公司 | Production method of low-carbon bainite non-quenched and tempered hot-rolled round steel |
-
2022
- 2022-10-27 CN CN202211328174.1A patent/CN115679089B/en active Active
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109295391A (en) * | 2018-11-22 | 2019-02-01 | 钢铁研究总院 | A kind of high-strength tenacity non-hardened and tempered steel and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN115679089A (en) | 2023-02-03 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109023036B (en) | Ultrahigh-strength hot-rolled complex-phase steel plate and production method thereof | |
| JP7300451B2 (en) | Wire rod for cold heading, processed product using the same, and manufacturing method thereof | |
| US6551419B2 (en) | Hot-rolled steel wire and rod for machine structural use and a method for producing the same | |
| CN118166286B (en) | 10.9-Grade non-adjustable cold heading steel hot rolled wire rod and manufacturing method thereof | |
| CN118166191B (en) | Manufacturing method of 9.8-grade non-cold-heading steel high-strength hot-rolled wire rod | |
| CN118166190B (en) | Hot-rolled wire rod for 12.9-grade low-chromium fire-reducing bolt and manufacturing method thereof | |
| CN118186310B (en) | 12.9-Grade quenching-free high-hardenability hot-rolled multiphase cold heading steel wire rod and manufacturing method thereof | |
| KR100428581B1 (en) | A non qt steel having superior strength and toughness and a method for manufacturing wire rod by using it | |
| CN113846266A (en) | Production method of high-ductility and toughness quenched and tempered steel plate with yield strength of 1300MPa | |
| CN118207405B (en) | 10.9-Grade high Cr annealing-free cold heading steel hot rolled wire rod and manufacturing method thereof | |
| EP2722113A1 (en) | High-strength steel wire having improved mold life for cold forming and method for manufacturing same | |
| KR101262462B1 (en) | Non heat treatment cold drawn wire rod having excellent impact property and method for manufacturing the same | |
| CN115679089B (en) | Forging and cooling control process for regulating and controlling microstructure of low-carbon bainite non-quenched and tempered steel for front axle | |
| CN115491605B (en) | Bainite steel for hot forging, process, device and system for manufacturing hot forged parts | |
| CN113528947B (en) | Steel for high-plasticity-toughness automobile structural part with tensile strength of 1500MPa produced by CSP and production method | |
| CN115725893B (en) | Ultra-high strength steel for 1300MPa engineering machinery and production method thereof | |
| CN105821348A (en) | Ball stud steel of automobile steering system and manufacturing method thereof | |
| JP2007513259A (en) | Steel wire for cold heading having excellent low temperature impact characteristics and method for producing the same | |
| CN111893384B (en) | Bainite girder steel with high crack arrest performance and preparation method thereof | |
| CN118744314A (en) | Production method of commercial wheel side half shaft based on forging and cooling control process | |
| CN114686776B (en) | 460 MPa-grade high-toughness extra-thick plate and manufacturing method thereof | |
| CN1206048C (en) | Rolling process of H-shaped niobium-containing steel | |
| CN108611572A (en) | High-plasticity hypereutectoid spring steel plate and production method thereof | |
| CN115261581B (en) | Non-quenched and tempered high-strength steel plate and production method thereof | |
| KR102065265B1 (en) | Wire rod for chq capable of reducing softening treatment time, and method for manufaturing the same |
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 |