CN113073264B - 2000 MPa-grade ultrahigh-strength steel with high uniform elongation and preparation method thereof - Google Patents
2000 MPa-grade ultrahigh-strength steel with high uniform elongation and preparation method thereof Download PDFInfo
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Abstract
The invention discloses ultrahigh-strength steel with high uniform elongation of 2000MPa and a preparation method thereof, and solves the technical problems that the uniform elongation of the conventional 2000 MPa-grade steel is difficult to reach 10%, the preparation process is complex, and the efficiency is low. The ultrahigh-strength steel with the high uniform elongation of 2000MPa comprises the following chemical components in percentage by weight: 0.3 to 0.4 percent of C, 8 to 9 percent of Ni, 6.5 to 10.0 percent of Cr, 3.0 to 6.0 percent of Mo, 0 to 2 percent of Mn, 0 to 2 percent of Si, 0 to 2 percent of Cu, 0.05 to 0.15 percent of V, 0.05 to 0.15 percent of Nb and the balance of Fe. The invention relates to a preparation method of ultrahigh-strength steel with high uniform elongation of 2000MPa, which comprises the following steps: pretreating a steel plate, wherein the pretreatment comprises solution treatment; carrying out room temperature rolling treatment on the solid solution steel plate treated in the step 1; carrying out warm rolling treatment on the steel plate treated in the step 2; carrying out high-temperature short-time annealing treatment on the steel plate subjected to warm rolling treatment in the step 3; and (4) carrying out medium-temperature long-time aging treatment on the steel plate subjected to the high-temperature short-time annealing treatment in the step (4). The invention has the advantages of tensile strength of more than 2000MPa, uniform elongation of more than 10 percent, high preparation efficiency and the like.
Description
Technical Field
The invention relates to the technical field of advanced high-strength steel, in particular to ultrahigh-strength steel with high uniform elongation of 2000MPa and a preparation method thereof.
Background
The acquisition of high-strength and high-plasticity integrated advanced high-strength steel is a target which is always pursued in steel research. The development of high performance steels with high strength and high plasticity is driven by their wide range of structural applications in automotive, aerospace and transportation. For example, steels with high strength can offer high passenger safety, high weight savings and energy saving potential in terms of collision protection in the automotive industry. However, high strength steels also need to have good ductility. For example, cold stamping techniques used in the automotive industry to manufacture complex automotive parts require steels with good ductility.
The tensile strength of the traditional advanced high-strength steel is 1500-2000MPa, but the plasticity is often less than 10%. For example, chinese patent publication nos.: the maraging steel disclosed in CN105568151A "an aluminum-reinforced maraging steel and a preparation method thereof" has an excellent tensile strength of 2000MPa, but the uniform elongation at a high strength level is less than 5%, the total elongation is less than 10%, and the molding requirement of complex parts in the industries of automobiles and the like is difficult to meet.
In addition to the requirement of strong plasticity integration, the high-efficiency preparation process is also a crucial part in the advanced research of high-strength steel, for example, chinese patent publication no: CN109790611A dual-phase steel and its manufacturing method discloses an advanced high-strength steel with high strength and good ductility, the dual-phase steel in the patent has an ultimate tensile strength of 2300MPa and a corresponding total elongation of 16%, which meets the requirement of strong plasticity required by industrial application, but the preparation process is complex, rolling and annealing are required to be carried out alternately, the time required by the preparation process is increased, and the preparation process efficiency is low.
The bottleneck of the advanced high-strength steel research is still as follows: the steel grade with high strength and high plasticity integration and the corresponding high-efficiency preparation process are developed.
Based on the current state of the art high strength steels, there is a need for improvements to obtain high strength steels with good elongation in a more efficient way.
Disclosure of Invention
The invention provides ultrahigh-strength steel with high uniform elongation of 2000MPa and a preparation method thereof, aiming at restriction factors of the steel in the wide application of engineering and the complexity of the existing preparation process.
The technical scheme of the invention is as follows:
the ultrahigh-strength steel with the high uniform elongation rate of 2000MPa comprises the following chemical components in percentage by weight:
0.3 to 0.4 percent of C, 8 to 9 percent of Ni, 6.5 to 10.0 percent of Cr, 3.0 to 6.0 percent of Mo, 0 to 2 percent of Mn, 0 to 2 percent of Si, 0 to 2 percent of Cu, 0.05 to 0.15 percent of V, 0.05 to 0.15 percent of Nb and the balance of Fe.
The invention discloses a preferable ultrahigh-strength steel with high uniform elongation of 2000MPa, which comprises the following chemical components:
0.4% of C, 8.0% of Ni, 8.0% of Cr, 4.0% of Mo, 1.0% of Mn, 1.0% of Si, 2% of Cu, 0.1% of V, 0.1% of Nb and the balance of Fe.
The ultrahigh-strength steel with the high uniform elongation of 2000MPa preferably has the advantages that the thickness of a superfine lamella in the ultrahigh-strength steel is 10-200 nm, the tissue structure of the steel plate is a martensite tissue and an austenite tissue, the martensite content is 60-90%, and the austenite content is 10-40%.
The optimal ultrahigh-strength steel with high uniform elongation of 2000MPa has the thickness of the superfine lamella of 20-50 nm, the volume fraction of martensite of 70-80 percent and the austenite content of 20-30 percent.
The invention obtains a martensite and austenite dual-phase structure through component improvement, and the structure contains a superfine lamellar structure, wherein the martensite is beneficial to improving the strength of steel, the austenite provides contribution for high uniform elongation of the steel, and the thickness of the superfine lamellar structure is smaller, so that the strength is further improved.
A preparation method of ultrahigh-strength steel with high uniform elongation of 2000MPa comprises the following steps:
step 1: pretreating a steel plate, wherein the pretreatment step comprises solid solution treatment to obtain a solid solution steel plate;
step 2: carrying out room temperature rolling treatment on the solid solution steel plate pretreated in the step 1;
and step 3: carrying out warm rolling treatment on the steel plate subjected to the room temperature rolling treatment in the step 2;
and 4, step 4: carrying out high-temperature short-time annealing treatment on the steel plate subjected to warm rolling treatment in the step 3;
and 5: and (4) carrying out medium-temperature long-time aging treatment on the steel plate subjected to the high-temperature short-time annealing treatment in the step (4).
According to the preparation method of the ultrahigh-strength steel with the high uniform elongation of 2000MPa, the solution treatment in the step 1 is carried out, wherein the solution temperature range is 900-1200 ℃, the solution time range is 1-6 h, and the cooling mode is water cooling.
According to the preparation method of the preferred ultrahigh-strength steel with the high uniform elongation of 2000MPa, the rolling temperature in the step 2 is room temperature, the rolling quantity is 55-70%, and the rolling quantity in each pass is less than 5%.
According to the preparation method of the preferred ultrahigh-strength steel with the high uniform elongation of 2000MPa, the rolling temperature in the step 3 is 500-700 ℃, the cooling mode is air cooling, the rolling quantity is 50-70%, and the rolling quantity in each pass is less than 5%.
According to the preparation method of the preferred ultrahigh-strength steel with the high uniform elongation of 2000MPa, in the step 4, the annealing temperature range is 600-800 ℃, the heat preservation time range is 10-600 s, and the cooling mode is air cooling.
According to the preparation method of the ultrahigh-strength steel with the high uniform elongation of 2000MPa, the temperature range of the aging treatment in the step 5 is 300-500 ℃, the heat preservation time range is 2-5 h, and the cooling mode is air cooling.
The ultrahigh-strength steel with the high uniform elongation rate of 2000MPa level prepared by the invention is mechanically characterized in that the tensile yield strength range is 1800 MPa-2000 MPa, the ultimate tensile strength range is 2000 MPa-2200 MPa, and the tensile uniform elongation rate range is 10% -16%.
The reason for the ultrahigh strength and the excellent uniform elongation of the preparation method of the ultrahigh strength steel with the high uniform elongation of 2000MPa is that: compared with the solid solution treatment steel, the preparation method of the ultrahigh strength steel with the high uniform elongation of 2000MPa obtains a large amount of lamellar martensite structures after rolling at room temperature in the step 2, and then obtains a superfine lamellar dual-phase structure through dual-phase region warm rolling treatment, so that the steel plate obtains high strength. And further, by high-temperature short-time annealing treatment, the superfine lamellar structure is ensured, and part of martensite after rolling treatment is returned to an austenite structure, so that the plasticity of the steel plate is improved. Then carrying out medium-temperature long-term aging treatment to obtain a precipitated phase M6C carbide, wherein the size of the precipitated phase is 200 nm-600 nm, and the strength of the steel plate is further improved. The steel plate finally obtained by the multistage rolling and the multistage heat treatment has high strength and excellent uniform elongation. The invention effectively solves the engineering application bottleneck that the uniform elongation of the existing 2000 MPa-grade ultrahigh-strength steel is less than 10 percent, and the 2000 MPa-grade ultrahigh-strength steel with high uniform elongation is obtained through a simple and effective preparation method.
Compared with the prior art, the invention has the following advantages:
1. the 2000 MPa-grade ultrahigh-strength steel with the uniform elongation of more than 10% is prepared by improving the component improvement and matching process.
2. The preparation process is simple and efficient, and the ultrahigh-strength steel with high strength and high uniform elongation can be realized only by two-step rolling.
Drawings
The accompanying drawings, which are included to provide a further understanding of the embodiments of the invention and are incorporated in and constitute a part of this application, illustrate embodiment(s) of the invention and together with the description serve to explain the principles of the invention. In the drawings:
fig. 1 is a tensile engineering stress-strain graph of the ultra-high strength steels prepared in examples 1-2.
Fig. 2 is a Transmission Electron Microscope (TEM) bright field photograph of the ultra-high strength steel prepared in example 2.
Fig. 3 is a tensile engineering stress-strain graph of the ultra-high strength steels prepared in examples 3-5.
Fig. 4 is a Transmission Electron Microscope (TEM) bright field photograph of the ultra-high strength steel prepared in example 4.
FIG. 5 is a Transmission Electron Microscope (TEM) bright field photograph of the ultra-high strength steel containing precipitated phases prepared in example 5.
Detailed Description
The present invention will be described in further detail below with reference to examples and the accompanying drawings. These examples are only for explaining the objects, technical solutions and advantageous effects of the present invention, and do not limit the scope of the present invention in any way.
The chemical element components and the weight of the embodiment of the invention are shown in the following table 1:
table 1 chemical composition of the steel of the examples
| Numbering | C | Ni | Cr | Mo | Mn | Si | Cu | V | Nb |
| Example 1 | 0.3 | 8 | 8 | 4 | 2 | 1 | 0 | 0.1 | 0.1 |
| Example 2 | 0.3 | 9 | 8 | 4 | 1 | 2 | 0 | 0.1 | 0.1 |
| Example 3 | 0.4 | 8 | 8 | 4 | 1 | 1 | 1 | 0.1 | 0.1 |
| Example 4 | 0.4 | 9 | 8 | 4 | 2 | 2 | 2 | 0.1 | 0.1 |
| Example 5 | 0.4 | 9 | 8 | 4 | 0 | 0 | 2 | 0.1 | 0.1 |
Examples 1 and 2
The preparation method of the ultrahigh-strength steel with high uniform elongation of 2000MPa comprises the following specific preparation steps:
step 1: carrying out solution treatment on the steel plate;
an initial steel plate with the thickness of 10mm is selected for solution treatment, the solution temperature is 1100 ℃, the heat preservation time is 2 hours, and the cooling mode is water cooling.
Step 2: carrying out room temperature rolling treatment on the solution treatment steel plate obtained in the step 1;
and (3) rolling the steel plate obtained in the step (1) at room temperature to obtain a steel plate with the thickness of 3mm, wherein the rolling reduction per pass is less than 5%, and the total accumulated rolling reduction is about 70%.
And step 3: carrying out secondary warm rolling on the room-temperature rolled steel plate obtained in the step 2;
and (3) carrying out warm rolling on the room-temperature rolled steel plate obtained in the step (2), wherein the warm rolling temperature is 600 ℃, the cooling mode is air cooling, the steel plate with the thickness of 1mm is obtained, the rolling quantity in each pass is less than 5%, and the total accumulated rolling quantity is about 67%.
And 4, step 4: carrying out high-temperature short-time annealing treatment on the steel plate obtained in the step 3;
and (4) carrying out high-temperature short-time annealing on the steel plate with the thickness of 1mm obtained in the step (3) in a box type furnace, wherein the annealing temperature is 650 ℃, the annealing time is 300s, and then air-cooling to room temperature.
The dashed line in fig. 1 is the engineering stress-strain curve of example 1 in the rolling direction, and its mechanical characteristics are: the yield strength is 1800MPa, the tensile strength is 2030MPa, and the uniform elongation is 10.5 percent.
The solid line in fig. 1 is the engineering stress-strain curve of example 2 in the rolling direction, and its mechanical characteristics are: the yield strength is 1788MPa, the tensile strength is 2120MPa, and the uniform elongation is 12.1%.
FIG. 2 is a TEM bright field image of the side surface of the plate obtained after the high-temperature short-time annealing of step 4 is completed in example 2, and a remarkable austenite and martensite structure is observed, the existence of austenite provides guarantee for the ductility of the material, and meanwhile, a large number of ultra-fine lamellar structure structures with the lamellar thickness of about 23nm can be found.
Example 3 and example 4
Step 1: carrying out solution treatment on the steel plate;
an initial steel plate with the thickness of 5mm is selected for solution treatment, the solution temperature is 1100 ℃, the heat preservation time is 2 hours, and the cooling mode is water cooling.
Step 2: carrying out room temperature rolling treatment on the solution treatment steel plate obtained in the step 1;
and (3) rolling the steel plate obtained in the step (1) at room temperature to obtain a steel plate with the thickness of 2mm, wherein the rolling reduction per pass is less than 5%, and the total accumulated rolling reduction is about 60%.
And step 3: carrying out secondary warm rolling on the room-temperature rolled steel plate obtained in the step 2;
and (3) carrying out warm rolling on the room-temperature rolled steel plate obtained in the step (2), wherein the warm rolling temperature is 650 ℃, the cooling mode is air cooling, the steel plate with the thickness of 1mm is obtained, the rolling quantity in each pass is less than 5%, and the total accumulated rolling quantity is about 50%.
And 4, step 4: carrying out high-temperature short-time annealing treatment on the steel plate obtained in the step 3;
and (4) carrying out high-temperature short-time annealing on the steel plate with the thickness of 1mm obtained in the step (3) in a box type furnace, wherein the annealing temperature is 600 ℃, the annealing time is 300s, and then air-cooling to room temperature.
The dotted line in fig. 3 is the engineering stress-strain curve of example 3 in the rolling direction, and its mechanical characteristics are: the yield strength is 1814MPa, the tensile strength is 2017MPa, and the uniform elongation is 12.1%.
The solid line in fig. 3 is the engineering stress-strain curve of example 4 in the rolling direction, and its mechanical characteristics are: the yield strength is 1710MPa, the tensile strength is 2023MPa, and the uniform elongation is 15.2%.
FIG. 4 is a TEM bright field image of the side of the plate obtained after step 4 high temperature short time annealing of example 4, and also a distinct ultrafine lamellar austenite and martensite structure can be observed, with a lamellar thickness of about 20 nm.
Example 5
This example differs from example 4 in that the aging treatment was carried out on the basis of the completion of example 4 to obtain an aged phase. The aging treatment of example 4 was carried out in a box furnace at an aging temperature of 450 ℃ for 2.5 hours, and then air-cooled to room temperature.
The dashed line in fig. 3 is the engineering stress-strain curve in the rolling direction after the aging of the present embodiment is completed, and the mechanical characteristics are as follows: the yield strength is 1812MPa, the tensile strength is 2169MPa, and the uniform elongation is 11.6%.
FIG. 5 is the side of the sheet obtained after the aging of the present embodiment is completedTEM bright field image of the surface, it is observed that the martensite and austenite and ultrafine lamellar microstructure remain intact compared to those before aging in FIG. 4, while a distinct second phase M is present6C carbide.
The results of the performance tests of the above examples are summarized in table 2 below.
TABLE 2 mechanical property test results of different examples
By observing the microstructure structure of the figures 2 and 4, the invention discovers that martensite and austenite coexist in the material through high-temperature short-time annealing treatment after secondary rolling, and the whole structure presents an obvious superfine lamellar structure, so that the invention has excellent plasticity while ensuring high strength. Comparing fig. 4 and 5, it is evident that a precipitated phase exists after the aging treatment, further improving the strength of the material.
The above-mentioned embodiments are intended to illustrate the objects, technical solutions and advantages of the present invention in further detail, and it should be understood that the above-mentioned embodiments are merely exemplary embodiments of the present invention, and are not intended to limit the scope of the present invention, and any modifications, equivalent substitutions, improvements and the like made within the spirit and principle of the present invention should be included in the scope of the present invention.
Claims (4)
1. A preparation method of ultrahigh-strength steel with high uniform elongation of 2000MPa grade,
the preparation method of the ultrahigh-strength steel comprises the following steps:
step 1: pretreating a steel plate, wherein the pretreatment step comprises solid solution treatment to obtain a solid solution steel plate; in the solid solution treatment, the solid solution temperature range is 900-1200 ℃, the solid solution time range is 1-6 h, and the cooling mode is water cooling;
step 2: carrying out room temperature rolling treatment on the solid solution steel plate pretreated in the step 1; the rolling temperature is room temperature, the rolling quantity is 55-70%, and the rolling quantity in each pass is less than 5%;
and step 3: carrying out warm rolling treatment on the steel plate subjected to the room temperature rolling treatment in the step 2; the rolling temperature is 500-700 ℃, the cooling mode is air cooling, the rolling quantity is 50-70 percent, and the rolling quantity in each pass is less than 5 percent;
and 4, step 4: carrying out high-temperature short-time annealing treatment on the steel plate subjected to warm rolling treatment in the step 3; the annealing temperature range is 600-800 ℃, the heat preservation time range is 10-600 s, and the cooling mode is air cooling;
and 5: carrying out medium-temperature long-time aging treatment on the steel plate subjected to the high-temperature short-time annealing treatment in the step 4; the temperature range of the aging treatment is 300-500 ℃, the heat preservation time range is 2-5 h, and the cooling mode is air cooling;
the chemical components of the prepared ultrahigh-strength steel in percentage by weight are as follows:
0.3 to 0.4 percent of C, 8 to 9 percent of Ni, 6.5 to 10.0 percent of Cr, 3.0 to 6.0 percent of Mo, 0 to 2 percent of Mn, 0 to 2 percent of Si, 0 to 2 percent of Cu, 0.05 to 0.15 percent of V, 0.05 to 0.15 percent of Nb and the balance of Fe.
2. The method for preparing the ultra-high strength steel with high uniform elongation rate of 2000MPa according to claim 1, wherein the chemical components of the ultra-high strength steel are as follows:
0.4% of C, 8.0% of Ni, 8.0% of Cr, 4.0% of Mo, 1.0% of Mn, 1.0% of Si, 2% of Cu, 0.1% of V, 0.1% of Nb and the balance of Fe.
3. The method for preparing the ultra-high strength steel with high uniform elongation rate of 2000MPa according to claim 1 or 2, wherein the thickness of the ultra-fine lamellar layer in the ultra-high strength steel is 10nm to 200nm, the structure of the steel plate is a martensite structure and an austenite structure, the martensite content is 60% to 90%, and the austenite content is 10% to 40%.
4. The method for preparing the ultrahigh-strength steel with the high uniform elongation of 2000MPa according to claim 3, wherein the thickness of the superfine sheet layer is 20-50 nm, the volume fraction of martensite is 70-80%, and the austenite content is 20-30%.
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| PCT/CN2021/131842 WO2022199079A1 (en) | 2021-03-24 | 2021-11-19 | 2000 mpa-grade ultrahigh-strength steel with high uniform elongation, and preparation method therefor |
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| CN114480977B (en) * | 2021-12-13 | 2023-04-07 | 四川大学 | Low-temperature 2500 MPa-grade ultrahigh-strength high-toughness steel and preparation method thereof |
| CN114686774B (en) * | 2022-03-08 | 2022-12-02 | 四川大学 | High-strength high-toughness nano precipitation-strengthened ultrafine-grained martensite austenite dual-phase steel and preparation method thereof |
| CN114717485B (en) * | 2022-03-08 | 2023-01-24 | 四川大学 | Nano precipitation strengthening ultrahigh-strength high-alloy steel and preparation method thereof |
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| JP3348187B2 (en) * | 1994-02-10 | 2002-11-20 | 新日本製鐵株式会社 | High-strength PC steel rod and method of manufacturing the same |
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