CN111471844B - Treatment method for realizing superplasticity of graphitized steel - Google Patents
Treatment method for realizing superplasticity of graphitized steel Download PDFInfo
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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
- C21D1/78—Combined heat-treatments not provided for above
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/06—Methods for forging, hammering, or pressing; Special equipment or accessories therefor for performing particular operations
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/06—Methods for forging, hammering, or pressing; Special equipment or accessories therefor for performing particular operations
- B21J5/08—Upsetting
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
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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
- C22C38/002—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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- 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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Abstract
A processing method for realizing superplasticity of graphitized steel belongs to the technical field of steel material processing. The graphitized steel with good superplasticity is obtained by mainly adopting a graphitizing treatment method and an isothermal cross forging treatment method. The method comprises the following specific steps: firstly, 660 to Ac1Carrying out primary graphitization treatment on the graphitized steel within a temperature range; then carrying out isothermal cross forging at the temperature of Ac3+ 30-50 ℃; finally, carrying out a second graphitization treatment at the temperature of 620-660 ℃. The graphitized steel treated by the method has fine and uniform microstructure, and nearly spherical fine graphite particles and granular cementite are dispersed and distributed on an equiaxed ferrite matrix, so that the requirements of superplastic forming on the relevant technical requirements of the microstructure are met. Therefore, the steel has a transformation point Ac1 or lower within a temperature range of 10 to 30 ℃ and a transformation temperature of 1 to 3X 10‑3When the tensile deformation is carried out in a strain rate range/s, the strain rate sensitivity index m is not less than 0.36, the elongation is not less than 100 percent, and the good superplasticity is shown.
Description
Technical Field
The invention relates to a treatment method for realizing superplasticity of graphitized steel, belonging to the technical field of steel material processing.
Background
Graphitized steels have begun to receive increasing attention for their good machinability and cold-formed parts. The steel is developed according to the development trend of lead-free low-sulfur free-cutting steel.
In the process of machining parts using the Steel as a raw material, cold heading plastic working is a commonly used machining method, and for example, the development idea of the Steel and the process of manufacturing parts using the Steel as a raw material are generally as follows in a paper "Bar and Wire Steels for metals and Valves of Automobiles-Eco-friendly Free Cutting Steel with Lead Addition", which is published in JFE Technical Report (2004 (4):74-80.) by T.Iwamoto, T.Hoshino: steel making, casting, hot rolling, graphitization, cold heading, cutting processing, graphite redissolution (quenching and tempering) and products. Studies have shown that the steel exhibits good plastic deformation properties during cold heading plastic working.
When the applicant analyzes the cold heading plasticity processing of the steel, the applicant researches a processing method capable of realizing the superplasticity of the graphitized steel by researching the structural characteristics and the plastic deformation mechanism of the steel. At present, no literature is published on the research on the superplasticity of the steel.
Disclosure of Invention
A method for realizing superplasticity of graphitized steel mainly comprises the steps of carrying out isothermal cross forging on the graphitized steel near a phase transformation point and carrying out graphitization treatment twice before and after forging to obtain the graphitized steel with superplasticity forming performance.
The invention is realized by the following technical measures:
a treatment method for realizing superplasticity of graphitized steel is characterized by mainly comprising the following steps:
a processing method for realizing superplasticity of graphitized steel is characterized in that the main chemical components and the mass percentage content are as follows: 0.42-0.50% C; 0.80-1.60% Si; 1.00-1.80% Mn; 0.0002 to 0.0010% of B; p is less than or equal to 0.015 percent; s is less than or equal to 0.015 percent; and performing primary graphitization treatment, double cross forging and secondary graphitization treatment on the graphitized steel with the balance of Fe.
Further, the first graphitization treatment is mainly carried out at 660-Ac1The graphitization is carried out within a temperature range, the graphitization time is 10-12 min/mm, and the maximum thickness of the blank is required to be not more than 100 mm. The structure after the graphitization treatment thus obtained is mainly composed of graphite and ferrite.
Further, isothermal cross forging is carried out on the graphitized steel blank after the first graphitization treatment, namely, the graphitized steel blank after the graphitization treatment is repeatedly upset and pulled along two mutually perpendicular directions in the cross section. The isothermal cross forging temperature is Ac3+ 30-50 ℃, and the total deformation of the isothermal cross forging temperature during upsetting is 60-80%; the forging ratio during drawing is not less than 5. And after forging, controlling the cooling speed at 25-30 ℃/s to ensure that the recrystallization process of the deformed austenite is completed and avoid coarsening of recrystallized austenite grains. This ensures that fine recrystallized austenite grains are obtained and thus that fine martensite is obtained during the subsequent cooling. In this process, the graphite particles distributed on the substrate are also broken up and dispersed by the cross forging action, and the graphite particles can be refined to an average size of about 1.0 μm at this time due to the diffusion behavior of carbon atoms at high temperature, but the morphology is irregular due to deformation.
Further, carrying out secondary graphitization treatment on the forged and deformed blank, wherein the graphitization treatment temperature is 620-660 ℃, the time is 6-8 min/mm, and air cooling to room temperature after treatment.
The invention has the beneficial effects that:
the graphitized steel treated according to the method disclosed by the application has a fine and uniform microstructure, the average size of ferrite grains is 7-9 mu m, and the form of the graphitized steel is mainly in a nearly equiaxial shape; the average size of the graphite particles is 1-3 mu m, and the graphite particles are mainly in a nearly spherical shape and are distributed in a dispersion manner; in addition, a granular cementite having an average size of 0.1 to 0.3 μm is dispersed on the ferrite matrix. The structural characteristics can ensure that the steel has good superplasticity, such as the temperature of 10-30 ℃ below the transformation point Ac1, namely Ac 1-10-30 ℃, and the temperature of 1-3 multiplied by 10-3When the stretching deformation is carried out in the strain rate range/s, the strain rate sensitive index m is not less than 0.36, and the elongation is not less than 100%. When the steel is stretched at the temperature range of 10-30 ℃ below the transformation point Ac1, the steel can effectively inhibit the decomposition of cementite due to the high content of Mn in the steel. Therefore, the dispersed and distributed micro cementite particles ensure that the ferrite has no obvious size change in the stretching deformation process, and further ensure that the steel has good superplastic forming performance from the aspect of organization structure.
Detailed Description
Embodiments of the present invention will now be described in detail.
The invention provides a treatment method for realizing superplasticity of graphitized steel, which is mainly carried out according to the following steps:
(1) the main chemical components and the mass percentage content are as follows: 0.42-0.50% C; 0.80-1.60% Si; 1.00-1.80% Mn; 0.0002 to 0.0010% of B; p is less than or equal to 0.015 percent; s is less than or equal to 0.015 percent; and carrying out primary graphitization treatment on the graphitized steel with the balance of Fe. The first graphitization treatment is mainly at 660-Ac1The graphitization is carried out within a temperature range, the graphitization time is 10-12 min/mm, and the maximum thickness of the blank is required to be not more than 100 mm;
(2) and carrying out isothermal cross forging on the graphitized steel blank subjected to the first graphitization treatment, namely repeatedly upsetting and drawing the graphitized steel blank subjected to the graphitization treatment along two mutually perpendicular directions in the cross section. The isothermal cross forging temperature is Ac3+ 30-50 ℃, and the total deformation of the isothermal cross forging temperature during upsetting is 60-80%; the forging ratio during drawing is not less than 5. And controlling the cooling speed at 25-30 ℃/s after forging.
(3) And carrying out secondary graphitization treatment on the forged and deformed blank, wherein the graphitization treatment temperature is 620-660 ℃, the time is 6-8 min/mm, and air cooling to room temperature after treatment.
The technical solution of the present invention is further described with reference to the following examples. The examples are intended to illustrate the invention only and are not intended to limit the invention in any way.
Example 1
This example prepares a graphitized steel that realizes superplasticity according to the following steps:
(1) the main chemical components and the mass percentage content are as follows: graphitized steel of 0.43% of C, 1.20% of Si, 1.1% of Mn, 0.0008% of B, 0.011% of P, 0.010% of S and the balance of Fe is subjected to primary graphitization treatment. The first graphitization treatment temperature is 680 ℃, and the graphitization time is 11 min/mm.
(2) Carrying out isothermal cross forging on the graphitized steel blank subjected to the first graphitization treatment, wherein the forging temperature is 810 ℃, and the total deformation of the graphitized steel blank during upsetting is 70%; the forging ratio at the time of drawing was 7. After forging, the cooling rate was controlled at 26 ℃/s.
(3) And carrying out secondary graphitization treatment on the forged and deformed blank, wherein the graphitization treatment temperature is 630 ℃, the time is 7min/mm, and the treatment is carried out air cooling to the room temperature.
The metallographic analysis results of the graphitized steel treated according to the method disclosed by the application show that: the microstructure is fine and uniform, the average size of ferrite grains is 7.8 mu m, and the shape of the ferrite grains is mainly near equiaxial; the average size of graphite particles is 1.9 mu m, and the graphite particles are mainly in a nearly spherical shape and are distributed in a dispersion way; in addition, a particulate cementite having an average size of 0.12 μm was dispersed and distributed on the ferrite matrix. The temperature was 710 ℃ and the strain rate was 1.2X 10-3The tensile test result at the time of/s shows that the strain rate sensitivity index m of the steel is 0.38, the elongation is 160 percent, and the steel not only shows good superplasticity, but also can be subjected to superplastic forming.
Example 2
This example prepares a graphitized steel that realizes superplasticity according to the following steps:
(1) the main chemical components and the mass percentage content are as follows: graphitized steel of 0.46% of C, 1.60% of Si, 1.5% of Mn, 0.0005% of B, 0.010% of P, 0.008% of S and the balance of Fe is subjected to a first graphitization treatment. The first graphitization treatment temperature is 680 ℃, and the graphitization time is 10 min/mm;
(2) carrying out isothermal cross forging on the graphitized steel blank subjected to the first graphitization treatment, wherein the forging temperature is 830 ℃, and the total deformation of the graphitized steel blank during upsetting is 60%; the forging ratio at the time of drawing was 6. After forging, the cooling rate was controlled at 27 ℃/s.
(3) And performing secondary graphitization treatment on the forged and deformed blank, wherein the graphitization treatment temperature is 630 ℃, the time is 6min/mm, and the blank is air-cooled to room temperature.
The metallographic analysis results of the graphitized steel treated according to the method disclosed by the application show that: the microstructure is fine and uniform, the average size of ferrite grains is 8.6 mu m, and the shape of the ferrite grains is mainly near equiaxial; the average size of graphite particles is 2.3 mu m, and the graphite particles are mainly in a nearly spherical shape and are distributed in a dispersion way; in addition, in ferriteThe matrix is also dispersed with a particulate cementite having an average size of 0.22 μm. At a temperature of 700 ℃ and a strain rate of 2.3X 10-3The tensile test result at the time of/s shows that the strain rate sensitivity index m of the steel is 0.32, the elongation is 136 percent, and the steel not only shows good superplasticity, but also can be subjected to superplastic forming.
The embodiment shows that the treatment method for realizing superplasticity of the graphitized steel provided by the invention can obtain a fine and uniform microstructure, thereby showing good superplasticity and being capable of carrying out superplastic forming on the graphitized steel. The treatment method is beneficial to popularization and application of the graphitization technology in steel.
Claims (5)
1. A processing method for realizing superplasticity of graphitized steel is characterized in that the main chemical components and the mass percentage content are as follows: 0.42-0.50% C; 0.80-1.60% Si; 1.00-1.80% Mn; 0.0002 to 0.0010% of B; p is less than or equal to 0.015 percent; s is less than or equal to 0.015 percent; sequentially carrying out first graphitization treatment, isothermal cross forging and second graphitization treatment on the graphitized steel with the balance of Fe;
wherein, the first graphitization treatment is mainly set for graphitizing steel to obtain graphite and ferrite tissues; the isothermal cross forging is mainly set for refining martensite structure and crushing graphite particles; the second graphitization treatment is mainly arranged for obtaining a micro ferrite structure and enabling the graphite particle shape to be approximately spheroidized;
the graphitized steel treated by the method has a fine and uniform microstructure, the average size of ferrite grains is 7-9 mu m, and the form of the graphitized steel is mainly in an approximately equiaxial shape; the average size of the graphite particles is 1-3 mu m, and the graphite particles are mainly in a nearly spherical shape and are distributed in a dispersion manner; in addition, a granular cementite having an average size of 0.1 to 0.3 μm is dispersed on the ferrite matrix.
2. The treatment method for realizing superplasticity of graphitized steel according to claim 1, wherein the first graphitization treatment is mainly at 660 ℃ to Ac ℃1The graphitization is carried out within a temperature range, the graphitization time is 10-12 min/mm, wherein the maximum thickness of the blank is requiredNot greater than 100 mm; the structure after the graphitization treatment thus obtained is mainly composed of graphite and ferrite.
3. The method for achieving superplasticity of graphitized steel according to claim 1, wherein said isothermal cross forging is isothermal forging plastic deformation of the graphitized steel blank after the first graphitization treatment, that is, repeatedly upsetting and drawing the graphitized steel blank after graphitization treatment along two mutually perpendicular directions in the cross section; the isothermal cross forging temperature is Ac3+ 30-50 ℃, and the total deformation of the isothermal cross forging temperature during upsetting is 60-80%; the forging ratio during drawing is not less than 5; after forging, controlling the cooling speed according to 25-30 ℃/s to ensure that the recrystallization process of the deformed austenite is completed and avoid coarsening of recrystallized austenite grains; this ensures that fine recrystallized austenite grains are obtained and thus fine martensite is obtained in the subsequent cooling process; in this process, the graphite particles distributed on the substrate are also broken up and dispersed by the cross forging action, and the graphite particles can be refined to an average size of about 1.0 μm at this time due to the diffusion behavior of carbon atoms at high temperature, but the morphology is irregular due to deformation.
4. The method for realizing superplasticity of graphitized steel according to claim 1, wherein the second graphitization treatment is performed on the forged and deformed blank, the graphitization treatment temperature is 620-660 ℃, the time is 6-8 min/mm, and the blank is air-cooled to room temperature after the graphitization treatment.
5. The method for superplasticizing a graphitized steel as claimed in any one of claims 1 to 4, wherein the temperature is 10 to 30 ℃ below the transformation point Ac1, i.e. Ac1-10 to 30 ℃, and 1 to 3 x 10-3When the stretching deformation is carried out within the strain rate range/s, the strain rate sensitivity index m is not less than 0.36, and the elongation is not less than 100%; when the steel is stretched at the temperature range of 10-30 ℃ below the transformation point Ac1, the steel can effectively inhibit the decomposition of cementite due to the high content of Mn in the steel; thus, finely divided cementite particles are dispersedThe ferrite has no obvious size change in the stretching deformation process, and the steel is further ensured to have good superplastic forming performance from the structural angle.
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