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CN110760748B - Spring steel with excellent fatigue life and manufacturing method thereof - Google Patents

Spring steel with excellent fatigue life and manufacturing method thereof Download PDF

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Publication number
CN110760748B
CN110760748B CN201810842312.5A CN201810842312A CN110760748B CN 110760748 B CN110760748 B CN 110760748B CN 201810842312 A CN201810842312 A CN 201810842312A CN 110760748 B CN110760748 B CN 110760748B
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spring steel
fatigue life
percent
steel
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CN110760748A (en
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姚赞
金峰
万根节
齐彦峰
吴振平
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority to CN201810842312.5A priority Critical patent/CN110760748B/en
Priority to PCT/CN2019/096726 priority patent/WO2020020066A1/en
Priority to US17/261,457 priority patent/US20210164078A1/en
Priority to JP2021503062A priority patent/JP7110480B2/en
Priority to EP19841872.5A priority patent/EP3831970B1/en
Priority to KR1020217001643A priority patent/KR102760130B1/en
Publication of CN110760748A publication Critical patent/CN110760748A/en
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • 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
    • B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
    • B21C1/003—Drawing materials of special alloys so far as the composition of the alloy requires or permits special drawing methods or sequences
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • B22D11/1206—Accessories for subsequent treating or working cast stock in situ for plastic shaping of strands
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
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    • B22D11/20—Controlling or regulating processes or operations for removing cast stock
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/072—Treatment with gases
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/10—Handling in a vacuum
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    • 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
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/58—Oils
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    • 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
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/60—Aqueous agents
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/04—Modifying the physical properties of iron or steel by deformation by cold working of the surface
    • C21D7/06—Modifying the physical properties of iron or steel by deformation by cold working of the surface by shot-peening or the like
    • 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
    • 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
    • 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
    • C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/573—Continuous furnaces for strip or wire with cooling
    • C21D9/5735—Details
    • C21D9/5737—Rolls; Drums; Roll arrangements
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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    • 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
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    • C21—METALLURGY OF IRON
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
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Abstract

A spring steel with excellent fatigue life and a manufacturing method thereof are disclosed, wherein the spring steel comprises the following chemical components in percentage by weight: c: 0.52-0.62%; si: 1.20 to 1.45 percent; mn: 0.25-0.75%; cr: 0.30-0.80%; v: 0.01 to 0.15 percent; nb: 0.001-0.05%; n: 0.001-0.009%; o: 0.0005-0.0040%; p: less than or equal to 0.015 percent; s: less than or equal to 0.015 percent; al: less than or equal to 0.0045 percent; the balance of Fe and inevitable impurities, and simultaneously satisfies: the ratio of (2Nb + V)/(20N + C) is more than or equal to 0.02 and less than or equal to 0.40. The microstructure of the spring steel is a tempered troostite + sorbite structure, the size of a prior austenite grain is less than 80um, the size of an alloy nitrogen carbon precipitate is 5-60nm, and the maximum width of a single-particle inclusion is less than 30 um. The spring steel has the processing strength of more than 2020MPa, good plasticity and toughness (the surface shrinkage is higher than 40%), and high fatigue life of more than or equal to 80 ten thousand times, and can meet the application requirements of high-stress springs in the industries of automobiles, machinery and the like.

Description

Spring steel with excellent fatigue life and manufacturing method thereof
Technical Field
The invention relates to spring steel and a manufacturing method thereof, in particular to spring steel with excellent fatigue life and a manufacturing method thereof, which can be used for automobile springs with the processing strength of more than 2020MPa, the surface shrinkage rate of more than 35 percent, refined structure, high steel purity, low cost and excellent fatigue life.
Background
The spring as an important damping and functional part is widely applied to social production and people's life in all aspects, and is widely applied to transportation, machinery manufacturing, automobile industry, military industry and daily life. The spring is used in the elastic range and should return to its original position after unloading, and it is desirable that the smaller the plastic deformation, the better, so that the wire should have a high elastic limit, yield strength and tensile strength. The higher the yield ratio, the closer the elastic limit is to the tensile strength, so the higher the strength utilization rate can be improved, and the stronger the elastic force of the manufactured spring is. The spring absorbs impact energy by virtue of elastic deformation, so that the spring wire does not necessarily have high plasticity, but at least has plasticity capable of withstanding the spring forming and sufficient toughness capable of withstanding the impact energy. Springs are typically operated under alternating stress for extended periods of time and therefore have a high fatigue limit, as well as good creep and relaxation resistance.
With the technical progress of the automobile and machinery industry, higher requirements are put forward on the strength and the fatigue life of spring parts, and the development of materials for manufacturing springs with high strength, good plasticity and high fatigue resistance reliability becomes the focus of attention of advanced steel enterprises in various countries.
At present, the conventional Cr-V series, Cr-Mn series and Si-Mn series spring steel materials can not meet the production requirement of high-strength springs, and the common Si-Cr series spring steel with higher strength and better yield ratio also reaches the limit of strength and fatigue life.
Chinese patent CN101787493B discloses high strength spring steel alloy components: 0.56 to 0.64 percent of C, 0.80 to 1.10 percent of Si, 0.80 to 1.20 percent of Mn, less than or equal to 0.035 percent of P, less than or equal to 0.03 percent of S, 0.80 to 1.20 percent of Cr, 0.60 to 1.00 percent of Mo, 0.20 to 0.30 percent of V, 0.05 to 0.12 percent of Nb, 0.01 to 0.060 percent of N, O.02 to 0.07 percent of RE and the balance of Fe. The design material has more Mn, Cr and Mo alloy elements, wherein Mo is mainly used for improving the tempering stability, the durable creep resistance, the heat resistance and the like of the steel.
The spring steel alloy disclosed in chinese patent CN100455691C comprises the following components: 0.4-0.6% of C, 1.7-2.5% of Si, 0.1-0.4% of Mn, 0.5-2.0% of Cr, 0-0.006% of N, and 0.021-0.07% of Al. The design route of the high-carbon high-silicon low-manganese alloy is adopted, the hydrogen brittleness resistance of the steel is enhanced by controlling the amount, the size and the shape of the retained austenite, the requirement on the material quenching and tempering process is high, the content of the Al alloy is high, the inclusion control difficulty in the smelting process is increased, and the fatigue life of the spring is easily shortened due to the hard and brittle aluminum oxide.
The spring steel alloy disclosed in the chinese patent CN1279204C is designed as follows: 0.30-0.50% of C, 0.80-2.0% of Si, 0.50-1.0% of Mn, 0.40-1.0% of Cr, 0.01-0.5% of W, 0.08-0.30% of V, 0.005-0.25% of rare earth elements and also 0.001-0.10% of B, and the alloy is mainly designed by low carbon, improves the content of Si element and the strength, and simultaneously adopts W element to improve the hardenability of steel, improve the deformation resistance and prevent decarburization, but the difficulties of smelting W and rare earth elements and heat treatment are higher.
Chinese patent CN1039725C discloses a low decarburization high toughness spring steel for automotive suspension springs. In this steel, the content of elemental Si is increased without reducing the content of C, 0.5-0.7% C, 1.0-3.5% Si, 0.3-1.5% Mn, 0.3-1.0% Cr, 0.05-0.5% V and or Nb, less than 0.02% P, less than 0.02% S, 0.5-5. O% Ni and other unavoidable impurities, the remainder being Fe. The material is added with more Ni elements for solving the decarburization problem and improving the toughness, and the alloy cost is high.
According to the technical scheme of the existing alloy, the strength of the material is improved mainly through adjustment of elements C, Si and Mn, the elasticity limit of the material is reduced due to too low Si content, the anti-elasticity reduction performance is poor, the plasticity of the material is poor due to too high Si content, the decarburization control difficulty is increased, and the fatigue life of the spring is influenced. Too high alloying element additions will lead to increased material costs and at the same time affect the precipitation size, leading to reduced fatigue properties of the material. The material design strength is still low while not much consideration is given to the fatigue life of the spring.
The development of light weight of automobiles and the technical progress of mechanical industry push the strength of spring materials to be continuously improved, and the commonly used Cr-V spring steel, Cr-Mn spring steel, Si-Mn spring steel and Cr-Si spring steel all reach the material limit.
Disclosure of Invention
The invention aims to provide spring steel with excellent fatigue life and a manufacturing method thereof, wherein the spring steel has the processing strength of more than 2020MPa, good plasticity and toughness (the surface shrinkage is higher than 40 percent), and high fatigue life of more than or equal to 80 ten thousand times, and can meet the application requirements of high-stress springs in the industries of automobiles, machinery and the like.
In order to achieve the purpose, the technical scheme of the invention is as follows:
a spring steel with excellent fatigue life comprises the following chemical components in percentage by weight:
C：0.52-0.62％；
Si：1.20-1.45％；
Mn：0.25-0.75％；
Cr：0.30-0.80％；
V：0.01-0.15％；
Nb：0.001-0.05％；
N：0.001-0.009％；
O：0.0005-0.0040％；
P：≤0.015％；
S：≤0.015％；
Al：≤0.0045％；
the balance of Fe and inevitable impurities, and simultaneously satisfies: the ratio of (2Nb + V)/(20N + C) is more than or equal to 0.02 and less than or equal to 0.40.
The microstructure of the spring steel is a tempered troostite + sorbite structure, the size of a prior austenite grain is less than 80um, the size of an alloy nitrogen carbon precipitate is 5-60nm, and the maximum width of a single-particle inclusion is less than 30 um.
In the spring steel composition design of the invention:
c is a component necessary for ensuring the room temperature strength and the hardenability of the spring steel, and is also an element for ensuring the spring steel to reach high elastic limit and good anti-ballistic performance, when the content of C is lower than 0.52%, the strength of the alloy spring steel cannot be ensured to reach more than 2020MPa, and simultaneously, the precipitation of micro-alloy element carbonitride is not facilitated, but the excessively high content of C causes the carbide to be oversize in the tempering process, the plasticity of the material is deteriorated, the material is not facilitated to keep good plastic toughness under high strength, and the fatigue life of the material is influenced, so the content of C is required to be lower than 0.62%.
Si is a non-carbide forming element and is mainly dissolved in a ferrite phase in a solid mode to play a role in strengthening, the improvement of the content of alloy silicon is beneficial to the improvement of the elastic limit and the anti-elasticity-reducing property of a material and the optimization of the performance of a spring, but too high content of Si can cause the plasticity of the material to be deteriorated and is not beneficial to the forming of the spring and influences the service life of a finished spring, meanwhile, the content of Si is high, so that the decarburization tendency is increased in the production and heat treatment processes of the material, the processing cost is increased, and the control range of the content of Si in the material is comprehensively considered to.
Mn is a commonly used additive element in steel, can effectively improve hardenability and strength, has little influence on the plasticity of the steel, and can not be lower than 0.25 percent in order to ensure the alloy strength and the hardenability. When the Mn content is excessively high, segregation is serious, and crystal grain growth is caused, so that the Mn content in the steel needs to be controlled, and the allowable range is 0.25-0.75%.
Cr has the functions of improving the hardenability of spring steel, simultaneously precipitating alloy cementite in the tempering process, improving the material strength, and refining the structure of Cr, so the solid solution strengthening and precipitation strengthening functions of Cr are exerted in the design of the material, and the content of the Cr is controlled to be 0.30-0.80 percent when the material structure is improved.
V, Nb elements are often used as microalloy elements to be added into steel, and the two elements have strong forming tendency of nitride and carbide, improve the precipitation nucleation rate of carbonitride in the tempering process and refine the structure. V, Nb, the carbonitride is precipitated in the process of rolling the wire rod, which is beneficial to reducing the austenite grain size of the material and improving the strength and the plasticity of the material. The nanoscale precipitate is beneficial to improving the strength, the plasticity and the fatigue life of the material, the size of the precipitate is increased when the V, Nb content in the alloy is excessively added, the mutual influence between two elements is considered, and through multiple rounds of verification, the addition amount of V is controlled to be 0.01-0.15%, the content of Nb is controlled to be 0.001-0.05%, and a better effect can be achieved. The brittleness of the material is enhanced due to the increase of the content of N, the effect of N on the precipitation of alloy elements is considered, and the content of N in steel needs to be controlled: 0.001-0.009%, and (2Nb + V)/(20N + C) in the steel is controlled within the range of 0.02-0.40 for the purpose of refining the precipitates. In order to achieve high strength, good plasticity and long fatigue life of the finished spring, the original austenite grain size of the material after quenching and tempering is less than 80um, and the size control range of the educt in the steel is 5-60 nm.
Al plays a role in deoxidation in steel, but alumina formed by Al deoxidation is a hard brittle phase and has a large influence on the fatigue life of the spring, and large-particle brittle inclusions are one of main factors causing abnormal fracture of the spring. In order to effectively control alumina inclusions in steel, Al in the steel is less than or equal to 0.0045 percent, and the control range of oxygen content is 0.0005 to 0.0040 percent; in order to improve the fatigue life of the spring under high strength, the width of the single-particle inclusion in the steel needs to be controlled below 30 um.
In order to ensure the toughness of the material and prevent the defects of hot brittleness, cold brittleness and the like in the production process, the content of harmful P, S element in the steel is respectively controlled below 0.015 percent and 0.015 percent, and the purity of the steel is improved.
The method for producing spring steel having excellent fatigue life according to the present invention comprises: smelting, continuous casting, rough rolling, high-speed wire rolling, stelmor controlled cooling, wire rod drawing and quenching and tempering; wherein,
the smelting adopts an electric furnace or a converter, the external refining is carried out after the smelting, the external refining adopts an LF furnace and VD or RH degassing treatment, the composition and alkalinity of synthetic slag are adjusted in the LF refining process, the P, S element content in steel is controlled to be lower than 0.015 percent and 0.015 percent, argon stirring is carried out, the refined slag and inclusions in molten steel are fully reacted, the denaturation and removal of the inclusions are realized, the VD or RH vacuum degassing time needs to be longer than 30 minutes, the gas is fully removed, the end point O content is controlled to be 0.0005-0.0040 percent, the N content is controlled to be 0.0010-0.0090 percent, and the H content is lower than 2 ppm; the steel ladle sedation time is more than 15min after refining, which is beneficial to floating of large-particle inclusion and controlling the inclusion in the molten steel to be less than 30 um.
In the high-speed wire rod rolling, the heating of the heating furnace is controlled at 920-1150 ℃, and the heat preservation time is 1.0-3.0 h; controlling the rolling speed to be 15-115m/s in the rolling process of the high-speed wire rod; the online temperature control preferred scheme is as follows: the inlet temperature of the finishing mill unit is 880-1050 ℃, the inlet temperature of the reducing sizing mill unit is 840-970 ℃, and the spinning temperature is 800-950 ℃.
Preferably, a continuous casting machine is adopted to cast a round billet or a square billet, the size of the round billet or the square billet is 320-500mm, and the aim of controlling the carbon segregation in the center of the billet to be lower than 1.08 is achieved by adjusting the drawing speed range to be 0.5-0.8m/min and the cooling and tail end light pressure amount to be more than 10mm in the continuous casting process; prevent the secondary oxidation in the process of molten steel casting, and is beneficial to the floating removal of inclusions larger than 30 um.
Preferably, the rough rolling adopts a two-fire material forming process, the initial rolling and cogging of the casting blank is 115-170mm square and round blank at 1050-1270 ℃, and the total rolling reduction is higher than 40%.
Preferably, the drawing speed of the wire rod is not higher than 3.5 m/min.
Preferably, in the quenching and tempering treatment, the heating temperature is controlled within the range of 850-1100 ℃ before the quenching and tempering treatment of the drawn steel wire, the quenching medium adopts oil or water, the temperature is controlled within the range of 15-40 ℃, the tempering temperature is controlled within the range of 370-550 ℃, and the size range of the nitrogen-carbon precipitate in the finished steel wire is controlled within the range of 5-60 nm.
Preferably, in the stelmor cooling control, the air volume adjusting range of 14 fans on the stelmor line is as follows: the air volume of the F1-F7 fan is 10-100%, the air volume of the F8-F12 fan is 0-50%, and the air volume of the F13-F14 fan is 0-50%.
In the spring steel manufacturing method of the present invention:
the smelting adopts an electric furnace or a converter, the external refining is carried out after the smelting, the external refining adopts a degassing treatment process of adding VD or RH into an LF furnace, slag is prevented from entering a steel ladle when the electric furnace or the converter taps steel, the composition and alkalinity of synthetic slag are adjusted in the LF refining process, the content of P, S element in steel is controlled to be lower than 0.015 percent and 0.015 percent, argon stirring is carried out, the refined slag and inclusion in molten steel are fully reacted, the denaturation and removal of the inclusion are realized, the VD or RH vacuum degassing time needs more than 30 minutes, the gas is fully removed, the O content at the end point is controlled to be 0.0005-0.0040 percent, the N content is controlled to be 0.0010-0.0090 percent, and the H content is controlled. The steel ladle sedation time is more than 15min after refining, which is beneficial to floating of large-particle inclusion and controlling the inclusion in the molten steel to be less than 30 um.
And (3) adopting a continuous casting machine to cast the smelting alloy, wherein a round billet or a square billet can be cast, the size of the round billet or the square billet is 320-500mm, and the aim of controlling the carbon segregation at the center of the billet to be lower than 1.08 is achieved by adjusting the parameters of drawing speed, cooling and terminal soft reduction in the continuous casting process. Prevent the secondary oxidation in the process of molten steel casting, and is beneficial to the floating removal of inclusions larger than 30 um. The two-fire material forming process is adopted, the primary rolling and cogging of the continuous casting billet is 115-plus 170mm square and round billet at the temperature of 1050-plus-material 1270 ℃, the total rolling reduction is required to be higher than 40%, and the structure is refined.
Heating in a heating furnace, wherein the heating is controlled at 920-1150 ℃, and the heat preservation time is 1.0-3.0 h. And controlling the rolling speed to be 15-115m/s in the high-speed wire rod rolling process. The online temperature control preferred scheme is as follows: the inlet temperature of the finishing mill unit is 880-1050 ℃, the inlet temperature of the reducing sizing mill unit is 840-970 ℃, and the spinning temperature is 800-950 ℃. The original austenite grain of the material is refined to be less than 80um by adjusting the temperature of the rolling process and the spinning temperature, and the size range of the precipitate is controlled to be 5-60 nm.
The dimension specification of the rolled wire rod is phi 5-28mm, and the wire rod structure transformation is controlled by adjusting the components of the Steyr friction line fan after the wire rod is rolled. The air quantity adjusting range of 14 fans on the stelmor line is as follows: the air volume of the F1-F7 fan is 10-100%, the air volume of the F8-F12 fan is 0-50%, and the air volume of the F13-F14 fan is 0-50%.
Before heat treatment, the wire rod needs to be drawn, and the drawing speed is controlled not to be higher than 3.5m/min during drawing. The heating temperature is controlled within the range of 850-1100 ℃ before the quenching and tempering treatment of the drawn steel wire, the quenching medium can adopt oil or water, the temperature is controlled within the range of 15-40 ℃, the tempering temperature is controlled within the range of 370-550 ℃, and the size range of the precipitate in the finished steel wire is controlled within the range of 5-60 nm.
The invention has the beneficial effects that:
the spring steel produced by adopting the steel components and the manufacturing method has the strength of more than 2020MPa, the alloy has low cost, and the spring steel has good plasticity and toughness and good spring forming performance by the nanometer precipitate reinforcing material, prevents the generation of processing cracks, ensures that the finished spring has high fatigue life by tissue refinement and inclusion composition and size control, can meet the use requirements of high strength and long service life in the automobile lightweight and mechanical industries, is beneficial to the promotion of the technical level of the industry, and has good economic benefit.
Detailed Description
The chemical compositions of inventive examples A1-10# and three comparative steel grades B1-3# are shown in Table 1 below, and the specific manufacturing methods are as follows:
the alloy of the embodiment A1-5#, the alloy of the comparative steel B1 and the alloy of the comparative steel B2 are smelted by an electric furnace, the alloy of the embodiment A6-10#, the alloy of the comparative steel B3 are smelted by a converter, and then are refined outside the furnace, wherein the alloy of the embodiment A1-3#, the alloy A6-8#, and the alloy B1 are refined by an LF furnace and VD, while the alloy of the embodiment A4-5#, the alloy A9-10#, the alloy B2 and the alloy B3 are treated by LF and RH, the structure and alkalinity of the synthetic slag are optimized, the vacuum degassing time of the A1-6#, the vacuum degassing time of the B1 are 30 minutes, the vacuum degassing time of the A7-10#, the B2 and the vacuum degassing time of the B3 are 35 minutes, the end: 0.001-0.009%, and H content is less than 2 ppm.
After smelting, round billets are cast into 300mm round billets A1-4# and B1, round billets A5-6# are cast into 450mm round billets, square billets A7-9# and B2 are cast into 320 x 420mm square billets, square billets A10# and B3 are cast into 500 square billets, and tundish covering agents and crystallizer protection slag with good sealing performance are adopted in the casting process. The blooming temperature of the A1-5# and B1 continuous casting billets is 1050 ℃, and the end surface size of the rolled small square billet is 115 mm. The heating temperature of the square billets A6-7# and B2 is 1270 ℃, and the size of the rolled billets is 125 mm. The heating temperature of the square billets A8-10# and B3 is 1100 ℃, and the size of the rolled billets is 170 mm.
The furnace temperature of A1-4# and B1 heating furnaces is controlled at 920 ℃, the heat preservation time is 1.0h, the furnace temperature of A5-10#, B2 and B3 heating furnaces is controlled at 1150 ℃, and the heat preservation time is 3.0 h. And controlling the rolling speed to be 15-115m/s in the high-speed wire rod rolling process. The online temperature control scheme is as follows: wherein the inlet temperature of the A1-6# and B1 alloy finishing mill set is 880-950 ℃, the inlet temperature of the reducing sizing mill set is 840-950 ℃, and the spinning temperature is 800-890 ℃. The inlet temperature of A7-10#, B2 and B3 alloy finishing mill units is 950-.
The rolling specifications of the alloy rolled wire rods A1-5#, B1 and B2 are phi 5-15mm respectively, and the rolling specifications of the alloy rolled wire rods A6-10# and B3 are phi 16-28mm respectively. The stelmor cooling process after rolling the A1-5# and B1 alloy wire rods comprises the following steps: the air volume of the F1-F4 fan is 40%, the air volume of the F5-F7 fan is 10%, the air volume of the F8-F12 fan is 5%, and the air volume of the F13-F14 fan is 40%. The stelmor cooling process after rolling the alloy wire rods A6-10#, B2 and B3 comprises the following steps: the air volume of the F1-F4 fan is 50%, the air volume of the F5-F7 fan is 20%, the air volume of the F8-F12 fan is 15%, and the air volume of the F13-F14 fan is 35%. The wire rod structure is a sorbite with a little ferrite after stelmor cooling.
Before heat treatment, the wire rod is subjected to drawing treatment, and the quenching and tempering temperature of drawn steel wires is divided into three groups, wherein the heating temperature of A1-2# and B1 is 850 ℃, the tempering temperature is 550 ℃, the heating temperature of A3-7# and B2 is 980 ℃, the tempering temperature is 470 ℃, the heating temperature of A8-10#, the heating temperature of B3 is 1100 ℃, and the tempering temperature is 370 ℃.
The mechanical properties of the high strength springs of examples A1-A10 and comparative steel grades B1-B3 are shown in Table 2 below. It can be seen from the table that the alloy strength reaches more than 2020MPa, which is higher than the samples of comparative examples B1-B3, and the material surface shrinkage can still reach more than 35%, and the alloy has good plasticity and toughness matching. The high-strength spring steel is made into the same type of spiral spring with the comparison alloy for fatigue life detection, and the fatigue life of the high-strength spring steel is superior to that of the comparison steel under the same condition.
Figure BDA0001745858870000091
Figure BDA0001745858870000101
Figure BDA0001745858870000111

Claims (7)

1. A spring steel with excellent fatigue life comprises the following chemical components in percentage by weight:
C：0.52-0.62％；
Si：1.20-1.45％；
Mn：0.25-0.75％；
Cr：0.30-0.80％；
V：0.01-0.15％；
Nb：0.001-0.05％；
N：0.001-0.009％；
O：0.0005-0.0040％；
P：≤0.015％；
S：≤0.015％；
Al：≤0.0045％；
the balance of Fe and inevitable impurities, and simultaneously satisfies: (2Nb + V)/(20N + C) is more than or equal to 0.02 and less than or equal to 0.40;
the microstructure of the spring steel is a tempered troostite + sorbite structure, the size of a prior austenite grain is less than 80um, the size of an alloy nitrogen carbon precipitate is 5-60nm, and the maximum width of a single-particle inclusion is less than 30 um;
the processing strength of the spring steel reaches more than 2020MPa, the surface shrinkage is higher than 40%, and the high fatigue life is more than or equal to 80 ten thousand times.
2. The method for manufacturing a spring steel excellent in fatigue life according to claim 1, comprising: smelting, continuous casting, rough rolling, high-speed wire rolling, stelmor controlled cooling, wire rod drawing and quenching and tempering; it is characterized in that, among them,
the smelting adopts an electric furnace or a converter, the external refining is carried out after the smelting, the external refining adopts an LF furnace and VD or RH degassing treatment, the composition and alkalinity of synthetic slag are adjusted in the LF refining process, the P, S element content in steel is controlled to be lower than 0.015 percent and 0.015 percent, argon stirring is carried out, the refined slag and inclusions in molten steel are fully reacted, the denaturation and removal of the inclusions are realized, the VD or RH vacuum degassing time needs to be longer than 30 minutes, the gas is fully removed, the end point O content is controlled to be 0.0005-0.0040 percent, the N content is controlled to be 0.0010-0.0090 percent, and the H content is lower than 2 ppm; the steel ladle calming time is longer than 15min after refining, large-particle inclusions can float upwards, and the inclusions in the molten steel are controlled to be smaller than 30 um;
in the high-speed wire rod rolling, the heating of the heating furnace is controlled at 920-1150 ℃, and the heat preservation time is 1.0-3.0 h; controlling the rolling speed to be 15-115m/s in the rolling process of the high-speed wire rod; the online temperature control preferred scheme is as follows: the inlet temperature of the finishing mill unit is 880-1050 ℃, the inlet temperature of the reducing sizing mill unit is 840-970 ℃, and the spinning temperature is 800-950 ℃.
3. The method for manufacturing spring steel with excellent fatigue life as claimed in claim 2, wherein a continuous casting machine is used to cast a round billet or a square billet with the dimensions of 320-500mm, and the core carbon segregation of the billet is controlled to be less than 1.08 by adjusting the casting speed range of 0.5-0.8m/min and the cooling and terminal light pressing amount to be more than 10mm during the continuous casting process; prevent the secondary oxidation in the process of molten steel casting, and is beneficial to the floating removal of inclusions larger than 30 um.
4. The method for manufacturing spring steel with excellent fatigue life as claimed in claim 2, wherein the rough rolling is performed by a two-fire rolling process, the billet is initially rolled into a 115-170mm square round billet at 1050-1270 ℃, and the total rolling reduction is higher than 40%.
5. The method of manufacturing a spring steel excellent in fatigue life according to claim 2, wherein a drawing speed at the time of drawing the wire rod is not higher than 3.5 m/min.
6. The method for manufacturing a spring steel excellent in fatigue life as claimed in claim 2, wherein in said quenching and tempering, the heating temperature before the quenching and tempering of the drawn wire is controlled within the range of 850-1100 ℃, the quenching medium is oil or water, the temperature is controlled within the range of 15-40 ℃, the tempering temperature is controlled within the range of 370-550 ℃, and the size of the carbonitride precipitates in the finished wire is controlled within the range of 5-60 nm.
7. The method for manufacturing a spring steel excellent in fatigue life according to claim 2, wherein in the stelmor cooling, the range of adjusting the air volume of 14 fans on the stelmor line is: the air volume of the F1-F7 fan is 10-100%, the air volume of the F8-F12 fan is 0-50%, and the air volume of the F13-F14 fan is 0-50%.
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CN101675176A (en) * 2007-05-25 2010-03-17 株式会社神户制钢所 Steel for high-cleanliness springs excellent in fatigue characteristics and high-cleanliness springs
CN101397629A (en) * 2007-09-26 2009-04-01 南京依维柯汽车有限公司 High intensity variable section spring piece under high stress and method for producing the same
CN101717893A (en) * 2009-12-15 2010-06-02 南京钢铁股份有限公司 55Si2MnVNbN spring steel and production process thereof
CN101717894A (en) * 2009-12-15 2010-06-02 南京钢铁股份有限公司 40Si2MnCrNiMoVNbN spring steel and production process thereof
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CN103045935A (en) * 2012-12-14 2013-04-17 天津钢铁集团有限公司 Control method for surface decarburization and ferrite distribution of steel disc bar of spring
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CN103484781A (en) * 2013-09-26 2014-01-01 宝山钢铁股份有限公司 High-strength and high-toughness spring steel and manufacturing method thereof
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