CN113755761B - Production method of high-strength and high-toughness automobile suspension spring steel - Google Patents
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/04—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of bars or wire
- B21C37/047—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of bars or wire of fine wires
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- 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
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- 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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
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Abstract
The invention relates to the technical field of automobile suspension spring steel, in particular to high-strength and high-toughness automobile suspension spring steel and a production method thereof. The chemical components of the material by weight percentage are as follows: c: 0.5% -0.6%, Si: 1.2% -1.6%, Mn: 0.60-0.9%, Cr: 0.6% -0.9%, V: 0.01-0.3%, P is less than or equal to 0.015%, S is less than or equal to 0.015%, Ti is less than or equal to 0.0015%, and the weight ratio of all aluminum: 0.0005% -0.0050%, total oxygen: less than or equal to 0.0025 percent, less than or equal to 0.0050 percent of N, less than 0.1 percent of inevitable impurities, and the balance of iron. The invention solves the technical problems of surplus strength and insufficient ductility and toughness of 2000MPa automotive suspension spring steel wires by brand-new chemical component design with low alloy content and low cost and matching with proper converter smelting, refining, continuous casting, continuous rolling, wire rod rolling, drawing, heat treatment and other processes. The tensile strength of the invention can reach 2000MPa and 2100MPa respectively, and the surface shrinkage rate is more than or equal to 45 percent. The spring steel has the excellent high-strength and high-toughness mechanical properties, and also has the advantages of low cost, low decarburization, high surface quality, high purity and excellent fatigue property.
Description
Technical Field
The invention relates to the technical field of automobile suspension spring steel, in particular to high-strength and high-toughness automobile suspension spring steel and a production method thereof.
Background
The 55SiCr spring steel is Si-Cr spring steel, is mainly used for manufacturing automobile suspension springs, is the most extensive steel used for manufacturing the automobile suspension springs at present, and has excellent fatigue performance and anti-sag performance.
In the current industrial production process, the tensile strength of the oil quenching tempering steel wire made by drawing and heat treating the steel wire rod can reach 1800MPa (1750-1850 MPa), 1900MPa (1850-1950 MPa) and 2000MPa (1950-2050 MPa) respectively according to different production processes.
However, in the actual production process of 2000MPa oil quenching tempered suspension spring steel wire, if the center of the wire rod raw material used for manufacturing the steel wire has a certain degree of center segregation, the center of the steel wire has an insufficient tempering structure after the steel wire is drawn and heat treated, and finally the strength of the steel wire can meet the requirement, but the surface shrinkage rate does not meet the technical requirement (not less than 40%), namely the quality problem that the strength has surplus toughness and is insufficient is solved.
In order to solve the quality problem, those skilled in the art usually adopt a method of reducing the wire speed of the steel wire and/or increasing the tempering temperature to eliminate the central tempering insufficient tissue, thereby increasing the area shrinkage rate. However, the method can sacrifice the strength, and finally, the strength of the steel wire is reduced, so that the technical standard requirement of the steel wire of 2000MPa class can not be met.
Disclosure of Invention
In order to overcome the defects of the prior art, the invention provides the high-strength high-toughness automobile suspension spring steel and the production method thereof, and the high-strength high-toughness automobile suspension spring steel not only has excellent high-strength high-toughness mechanical properties, but also has low cost, low decarburization, high surface quality, high purity and excellent fatigue performance.
In order to achieve the purpose, the invention adopts the following technical scheme:
the high-strength and high-toughness automobile suspension spring steel comprises the following chemical components in percentage by weight:
c: 0.5% -0.6%, Si: 1.2% -1.6%, Mn: 0.60-0.9%, Cr: 0.6% -0.9%, V: 0.01-0.3%, P is less than or equal to 0.015%, S is less than or equal to 0.015%, Ti is less than or equal to 0.0015%, and the weight ratio of all aluminum: 0.0005% -0.0050%, total oxygen: less than or equal to 0.0025 percent, less than or equal to 0.0050 percent of N, less than 0.1 percent of inevitable impurities, and the balance of iron.
A production method of high-strength and high-toughness automobile suspension spring steel specifically comprises the following steps:
1) the blast furnace molten iron is pretreated for desulfurization, the S content in the desulfurized molten iron is less than or equal to 0.002 percent, the Ti content is less than or equal to 0.030 percent, and the temperature of the molten iron is more than or equal to 1320 ℃;
2) the converter adopts high-carbon steel tapping, the carbon content at the smelting end point of the converter is more than 0.3 percent, and the temperature at the end point of the converter is controlled to be more than 1600 ℃;
3) the converter adopts a double-slag method for smelting, and the content of P at the end point of the converter is less than or equal to 0.007 percent;
4) after tapping of the converter, a rinsing tank of aluminum-free deoxidized steel or a special tank for cord steel is adopted to prevent Al in molten steel;
5) slagging off after tapping of the converter, wherein the thickness of a slag layer after slagging off is less than 80mm, and adding 200-400 kg/tank (or 2-4 kg/t) of pre-melted wollastonite after slagging off;
6) when tapping from the converter, carrying out deoxidation alloying by adopting special ferrosilicon L, medium-carbon ferromanganese and low-carbon ferrochrome;
7) only adding premelted wollastonite for slagging in the LF refining process, wherein the adding amount is not less than 800 kg/tank (or 8 kg/t); refining time is 30-70 minutes after the slag is manufactured, and the temperature in the refining process is controlled to be 1520-1620 ℃; controlling the oxygen content of the molten steel at the refining end point to be 0.0010-0.0040 percent, and controlling the acid-soluble Al content of the molten steel to be 0.0005-0.0020 percent;
8) VD vacuum degassing and pressure maintaining time is more than 15min, and weak argon blowing and stirring are carried out for more than 20min after the air is broken;
9) continuous casting by adopting a bloom, protecting and pouring in the whole process, wherein the superheat degree of molten steel is less than 25 ℃, and the drawing speed is 0.5-0.7 m/min;
10) the heating temperature of the continuous casting billet in the heating furnace is controlled to be more than 1200 ℃ before the 280mm multiplied by 380mm continuous casting bloom is continuously rolled and cogging into 160mm multiplied by 160mm continuous rolling billets; carrying out secondary full grinding, surface defect flaw detection and internal ultrasonic flaw detection on the surface of the continuously rolled blank;
11) the temperature of the continuously rolled blank in a soaking section of a heating furnace is 1030-1120 ℃, and the heating and heat preservation time is 90-120 min; removing phosphorus from the continuous rolling blank by high-pressure water after the continuous rolling blank is discharged from the furnace, wherein the phosphorus removal pressure is more than 22MPa, and removing iron scale on the surface;
12) the diameter of a wire rod is 12-18 mm, the temperature of a double module is 900-910 ℃, the spinning temperature is 890-900 ℃, the cooling speed before phase change after spinning is 3-7 ℃/s, the phase change temperature of pearlite is 650-710 ℃, and the initial roller speed is 0.4-0.6 m/s;
13) drawing process: the diameter of the steel wire is 11-16 mm, the drawing speed is 30-50 m/min, the drawing passes are 1-2 passes, and the surface reduction rate of each pass is 15-30%; carrying out online eddy current inspection and online coping on surface defects with the sensitivity of below 50 microns before drawing the steel wire;
14) the heat treatment process comprises the following steps: electromagnetic induction heating is adopted, the steel wire speed is 10-25 m/min, the quenching temperature is 880-1000 ℃, the quenching medium is water, the tempering temperature is 350-500 ℃, and the water is cooled;
15) and carrying out online surface defect flaw detection and paint spraying marking on the finished steel wire.
Compared with the prior art, the invention has the beneficial effects that:
the invention solves the technical problems of residual strength and insufficient ductility and toughness of 2000 MPa-level automobile suspension spring steel wires due to central segregation (insufficient tempering) of the core of the coil stock by brand-new chemical component design with low alloy content and low cost and matching with proper converter smelting, refining, continuous casting, continuous rolling, coil rolling, drawing, heat treatment and other processes.
The tensile strength of the invention can reach 2000MPa (1950 MPa-2050 MPa) and 2100MPa (2050 MPa-2150 MPa) respectively, and the surface shrinkage is more than or equal to 45 percent. The spring steel has the excellent high-strength and high-toughness mechanical properties, and also has the advantages of low cost, low decarburization, high surface quality, high purity and excellent fatigue property.
Detailed Description
The invention discloses high-strength and high-toughness automobile suspension spring steel and a production method thereof. Those skilled in the art can modify the process parameters appropriately to achieve the desired results with reference to the disclosure herein. It is expressly intended that all such similar substitutes and modifications which would be obvious to one skilled in the art are deemed to be included in the invention. While the methods and applications of this invention have been described in terms of preferred embodiments, it will be apparent to those of skill in the art that variations and modifications, or appropriate variations and combinations of the methods and applications described herein may be made to implement and use the techniques of this invention without departing from the spirit and scope of the invention.
A production method of high-strength and high-toughness automobile suspension spring steel specifically comprises the following steps:
1) the molten iron production process comprises the following steps: blast furnace ironmaking, molten iron pretreatment desulphurization, the S content in the desulfurized molten steel is less than or equal to 0.002 percent, the Ti content is less than or equal to 0.030 percent, and the molten iron temperature is more than or equal to 1320 ℃.
2) Smelting in a converter: the converter adopts high-carbon steel tapping, the carbon content at the smelting end point of the converter is more than 0.3 percent, and the end point temperature of the converter is 1600-1650 ℃; the converter adopts a double-slag method for smelting, and the content of P at the end point of the converter is less than or equal to 0.007 percent; after tapping of the converter, a rinsing tank of aluminum-free deoxidized steel or a special tank for cord steel is adopted to prevent Al in molten steel; slagging off after tapping of the converter, wherein the thickness of a slag layer after slagging off is less than 80mm, and adding 200-400 kg/tank of pre-melted wollastonite after slagging off; when the converter taps steel, special ferro-silicon L, medium carbon ferromanganese and low carbon ferrochromium are adopted for deoxidation alloying.
3) LF refining: only adding premelted wollastonite in the LF refining process for slagging, wherein the adding amount is not less than 800 kg/tank. Refining time is 30-70 minutes after the slag is manufactured, and the temperature in the refining process is controlled to be 1520-1620 ℃; the oxygen content of the molten steel at the refining end is 0.0010-0.0040%, and the acid-soluble Al content of the molten steel is 0.0005-0.0020%.
4) VD treatment process: and VD vacuum degassing and pressure maintaining time is more than 15min, and weak argon blowing and stirring are carried out for more than 20min after the air is broken.
5) Continuous casting: continuous casting of a bloom is adopted, the whole process is protected, the superheat degree of molten steel is less than 25 ℃, and the drawing speed is 0.5-0.7 m/min.
6) Continuous rolling: the heating temperature of the continuous casting billet in the heating furnace is controlled to be more than 1200 ℃ before the 280mm multiplied by 380mm continuous casting bloom is continuously rolled and cogging into 160mm multiplied by 160mm continuous rolling billets; and carrying out secondary full grinding, surface defect flaw detection and internal ultrasonic flaw detection on the surface of the continuously rolled blank.
7) Rolling the wire rods: the temperature of the continuously rolled blank in a soaking section of a heating furnace is 1030-1120 ℃, and the heating and heat preservation time is 90-120 min; removing the surface iron scale by high-pressure water dephosphorization (the dephosphorization pressure is more than 22MPa) after the continuous rolling billet is discharged from the furnace; diameter of the wire rod: 12-18 mm, the temperature of the double modules is 900-910 ℃, the spinning temperature is 890-910 ℃, the cooling speed before phase change after spinning is 3-7 ℃/s, the phase change temperature of pearlite is 650-710 ℃, and the initial roller speed is 0.4-0.6 m/s.
8) The steel wire production process comprises the following steps:
a) drawing process: the diameter of the steel wire: 11 mm-16 mm, drawing speed: 30-50 m/min, 1-2 drawing passes, and the surface reduction rate of each pass is 15-30%; before drawing, the steel wire is subjected to online eddy current inspection (the sensitivity is below 50 microns) and online polishing of surface defects.
b) The heat treatment process comprises the following steps: electromagnetic induction heating is adopted, the steel wire speed is 10-25 m/min, the quenching temperature is 880-1000 ℃, the quenching medium is water, the tempering temperature is 350-500 ℃, and the water is cooled; and (5) carrying out online surface defect flaw detection and paint spraying marking on the finished steel wire.
[ examples ] A method for producing a compound
The following are the chemical components and the corresponding production processes of the examples and comparative examples of the present invention. Wherein, table 1 shows the specific component design of the comparative example and the high strength and toughness automobile suspension spring steel embodiment of the invention, table 2 shows the production process of the comparative example and the high strength and toughness automobile suspension spring steel of the invention, and table 3 shows the mechanical property test results of the comparative example and the high strength and toughness automobile suspension spring steel embodiment of the invention.
TABLE 1 specific chemical composition (% by weight)
| Examples | C，％ | Si，％ | Mn，％ | Cr，％ | V，％ | P，％ | S，％ | Ti，％ |
| 1 | 0.54 | 1.42 | 0.68 | 0.71 | 0.032 | 0.012 | 0.008 | 0.0008 |
| 2 | 0.56 | 1.45 | 0.65 | 0.68 | 0.028 | 0.013 | 0.006 | 0.0010 |
| Comparative example | 0.53 | 1.47 | 0.66 | 0.72 | - | 0.013 | 0.005 | 0.0011 |
TABLE 2 production Process conditions
TABLE 3 mechanical Property test results
| Examples | Tensile strength of steel wire, MPa | Reduction of steel wire face, percent | Fatigue life of suspension spring ten thousand times |
| 1 | 1998 | 49 | 50 |
| 2 | 2067 | 50 | 50 |
| Comparative example | 1996 | 32 | 50 |
The invention solves the technical problems of residual strength and insufficient ductility and toughness of 2000 MPa-level automobile suspension spring steel wires due to central segregation (insufficient tempering) of the core of the coil stock by brand-new chemical component design with low alloy content and low cost and matching with proper converter smelting, refining, continuous casting, continuous rolling, coil rolling, drawing, heat treatment and other processes.
The tensile strength of the invention can reach 2000MPa (1950 MPa-2050 MPa) and 2100MPa (2050 MPa-2150 MPa) respectively, and the surface shrinkage is more than or equal to 45 percent. The spring steel has the excellent high-strength and high-toughness mechanical properties, and also has the advantages of low cost, low decarburization, high surface quality, high purity and excellent fatigue property.
The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art should be considered to be within the technical scope of the present invention, and the technical solutions and the inventive concepts thereof according to the present invention should be equivalent or changed within the scope of the present invention.
Claims (5)
1. The production method of the high-strength and high-toughness automobile suspension spring steel is characterized by comprising the following chemical components in percentage by weight:
c: 0.5% -0.6%, Si: 1.2% -1.6%, Mn: 0.60-0.9%, Cr: 0.6% -0.9%, V: 0.01-0.3%, P is less than or equal to 0.015%, S is less than or equal to 0.015%, Ti is less than or equal to 0.0015%, and the weight ratio of all aluminum: 0.0005% -0.0050%, total oxygen: less than or equal to 0.0025 percent, less than or equal to 0.0050 percent of N, less than 0.1 percent of inevitable impurities, and the balance of iron;
the tensile strength of the high-strength and high-toughness automobile suspension spring steel reaches 2000MPa, the tensile strength of 2000MPa is 1950 MPa-2050 MPa, and the surface shrinkage is more than or equal to 45%;
the method specifically comprises the following steps:
1) the blast furnace molten iron is pretreated for desulfurization, and the S content and the Ti content in the desulfurized molten steel are respectively less than or equal to 0.002% and less than or equal to 0.030%;
2) the converter adopts high-carbon steel tapping, the carbon content at the smelting end point of the converter is more than 0.3 percent, and the temperature at the end point of the converter is controlled to be more than 1600 ℃;
3) the converter adopts a double-slag method for smelting, and the content of P at the end point of the converter is less than or equal to 0.007 percent;
4) after tapping of the converter, rinsing the tank by using aluminum-free deoxidized steel or using a special tank for cord steel;
5) slagging off after tapping of the converter;
6) when tapping from the converter, carrying out deoxidation alloying by adopting special ferrosilicon L, medium-carbon ferromanganese and low-carbon ferrochrome;
7) only adding premelted wollastonite for slagging in the LF refining process, wherein the adding amount is not less than 800 kg/tank; refining 30-70 minutes after the slag is manufactured, and controlling the temperature in the refining process to be 1520-1620 ℃; controlling the oxygen content of the molten steel at the refining end point to be 0.0010-0.0040 percent, and controlling the acid-soluble Al content of the molten steel to be 0.0005-0.0020 percent;
8) VD vacuum degassing and pressure maintaining time is more than 15min, and weak argon blowing and stirring are carried out for more than 20min after the air is broken;
9) continuous casting by adopting a bloom, protecting and pouring in the whole process, wherein the superheat degree of molten steel is less than 25 ℃, and the drawing speed is 0.5-0.7 m/min;
10) before a 280mm multiplied by 380mm continuous casting bloom is continuously rolled and cogging into a 160mm multiplied by 160mm continuous rolling billet, the heating temperature of the continuous casting billet in a heating furnace is controlled to be more than 1200 ℃; carrying out secondary full grinding, surface defect flaw detection and internal ultrasonic flaw detection on the surface of the continuously rolled blank;
11) the temperature of the continuous rolling blank in a soaking section of a heating furnace is 1030-1120 ℃, and high-pressure water dephosphorization is carried out after the continuous rolling blank is taken out of the furnace to remove surface iron oxide scales;
12) the diameter of the wire rod is 12-18 mm, the temperature of the wire rod entering the double modules is 900-910 ℃, and the spinning temperature is 890-900 ℃; cooling speed after spinning before phase change is 3-7 ℃/s, pearlite phase change temperature is 650-710 ℃, and initial roller speed is 0.4-0.6 m/s;
13) drawing process: the diameter of the steel wire is 11-16 mm, the drawing speed is 30-50 m/min, the drawing passes are 1-2 passes, and the surface reduction rate of each pass is 15-30%;
14) the heat treatment process comprises the following steps: electromagnetic induction heating is adopted, the steel wire speed is 10-25 m/min, the quenching temperature is 880-1000 ℃, the quenching medium is water, the tempering temperature is 350-500 ℃, and the water is cooled;
15) and carrying out online surface defect flaw detection and paint spraying marking on the finished steel wire.
2. The production method of the high-strength high-toughness automobile suspension spring steel according to claim 1, wherein the temperature of blast furnace molten iron in the step 1) is more than or equal to 1320 ℃.
3. The production method of the high-strength high-toughness automobile suspension spring steel according to claim 1, wherein the thickness of the slag layer after slag skimming in the step 5) is less than 80mm, and 200-400 kg/tank of pre-melted wollastonite is added after slag skimming.
4. The production method of the high-strength high-toughness automobile suspension spring steel according to claim 1, wherein the heating and heat preservation time in the step 11) is 90-120 min, and the dephosphorization pressure is greater than 22 MPa.
5. The production method of the high-strength high-toughness automobile suspension spring steel according to claim 1, wherein in the step 13), surface defects are subjected to online eddy current testing and online coping before the steel wire is drawn, and the sensitivity of the online eddy current testing of the surface defects is less than 50 microns.
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| CN114752743B (en) * | 2022-03-15 | 2023-10-24 | 建龙北满特殊钢有限责任公司 | Preparation method of 55SiCrA wire rod for automobile suspension spring |
| CN114959448B (en) * | 2022-04-21 | 2023-03-10 | 中天钢铁集团有限公司 | Efficient production method of 1900 MPa-grade steel for suspension spring |
| CN114807728B (en) * | 2022-06-30 | 2022-11-18 | 江苏省沙钢钢铁研究院有限公司 | 2100MPa grade spring steel wire and production method thereof |
| CN115094335B (en) * | 2022-07-22 | 2023-04-07 | 李家华 | Automobile tail door spring steel wire and preparation method thereof |
| CN117127122B (en) * | 2023-10-27 | 2024-01-23 | 张家港荣盛特钢有限公司 | Fatigue-resistant spring steel wire, wire rod and production method of wire rod |
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| JPS5925024B2 (en) * | 1980-06-26 | 1984-06-13 | 株式会社神戸製鋼所 | steel for suspension springs |
| CN103510020B (en) * | 2012-06-20 | 2015-10-07 | 鞍钢股份有限公司 | A kind of spring steel wire rod and inclusion control method thereof |
| KR102020385B1 (en) * | 2017-09-29 | 2019-11-04 | 주식회사 포스코 | Steel wire rod and steel wire for spring having corrosion fatigue resistance and method of manufacturing thereof |
| CN107587079B (en) * | 2017-10-26 | 2019-05-14 | 山东汽车弹簧厂淄博有限公司 | Nitrogenous microalloying spring steel and preparation method thereof |
| JP6816738B2 (en) * | 2018-03-30 | 2021-01-20 | Ｊｆｅスチール株式会社 | Steel wire manufacturing method |
| CN109457187B (en) * | 2018-12-20 | 2019-12-06 | 东北大学 | high-strength spring steel and production method thereof |
| CN109811266A (en) * | 2019-03-19 | 2019-05-28 | 马鞍山钢铁股份有限公司 | A kind of anti-corrosion spring steel and its production method of tensile strength >=2000MPa |
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