CN109837470B - High-strength nitrogen-containing economical austenitic stainless steel and manufacturing method thereof - Google Patents
High-strength nitrogen-containing economical austenitic stainless steel and manufacturing method thereof Download PDFInfo
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Abstract
The high-strength nitrogen-containing economical austenitic stainless steel comprises the following chemical components in percentage by weight: c: 0.05-0.15%, Si: 0.3-1%, Mn: 8.5-11.0%, Cr: 14.0-16.0%, Ni: 1.0-2.5%, N: 0.10 to 0.25% of P<0.08％，S<0.01%, Cu: 0.5-2.0%, Mo: 0.1-0.5%, the balance of Fe and inevitable impurities, and Md30/50Not less than 20 ℃. In the manufacturing process, the invention refines crystal grains by two times of cold rolling and flexible annealing and utilizing the generation and inversion of deformed martensite, and finally obtains the crystal grains with the size below 500nm, thereby greatly improving the strength of the material, and the specific properties are as follows: the yield strength is more than or equal to 650MPa, the tensile strength is more than or equal to 1000MPa, the elongation is more than or equal to 35 percent, and the method is suitable for preparing high-strength thin-specification precise strip steel.
Description
Technical Field
The present invention relates to a high-strength nitrogen-containing economical austenitic stainless steel and a method for manufacturing the same, and more particularly, to a high-strength nitrogen-containing economical austenitic stainless steel obtained by obtaining nano-scale grains through repeated thermal mechanical deformation and flexible annealing, and a method for manufacturing the same.
Background
With the progress of industrial technology, the requirements of various industries on metal materials are continuously increased, and low cost and high strength are the development trend of future metal materials. For example, in the fields of automobiles, aviation and the like, the requirement of light weight development requires that the material has higher strength and better plasticity, and the cost cannot be too high. In addition, in the precision electronics industry, a large number of high-strength thin strips are also needed to meet the requirement that the size of electronic products is gradually reduced.
Stainless steel is an important choice for materials in the industrial field because of having certain strength and corrosion resistance. However, the conventional austenitic stainless steels 304 and 316 have low strength and cannot well meet the requirements of high-strength materials, and the products contain high nickel content and have high cost. In addition, since the price fluctuation of Ni is large, the price fluctuation of these products is also large, which brings about a relatively large economic risk. Therefore, it is very important to develop an economical stainless steel, and to satisfy the requirement of high strength by technical means, so as to achieve the purpose of low cost and high strength.
In fact, in recent years, people use an N alloying means to obtain nickel-saving or even nickel-free austenitic stainless steel, so that the cost is greatly reduced, the strength is improved to a certain extent, and the products are widely applied to the fields of household electrical products, containers and the like. However, the N content of the currently developed nickel-saving austenitic stainless steel is usually below 0.2%, the yield strength is only about 400MPa, the tensile strength can only reach 700-800 MPa, and the strength can not completely meet the requirements of high-strength stainless steel. If the nitrogen content is increased to more than 0.4 percent, the prepared high-nitrogen stainless steel can meet the requirements of high-strength stainless steel, for example, the yield strength reaches more than 600MPa, and the tensile strength reaches more than 1000 MPa. However, the difficulty of the high-nitrogen steel in the actual industrial production process is very high, and wide high-nitrogen steel plates cannot be prepared at present. Therefore, in order to achieve high strength, temper rolling, known as hard stainless steel, is currently used, and the generation of deformed martensite is used to improve the strength of the material, with the 301 series of hard stainless steels being typical examples.
Although temper rolling is well applied to the production of high-strength stainless steel, the problems that the strength is not uniformly controlled and the strip shape of the strip steel is difficult to control are often encountered in the production of thin or extremely thin strip steel due to the difficulty in accurately controlling the temper rolling reduction, and the existence of the problems causes the difficulty in producing high-quality high-strength stainless steel thin strips.
The Chinese patent CN200810042817.X ensures the stability of an austenite structure by adding higher Mn content, thereby obtaining the performance of keeping no magnetism under the cold deformation condition. The high content of N in the material can greatly increase the strength of the material under the cold deformation condition, and high strength performance is obtained. However, the high strength obtained by the patent is still formed by cold rolling, and the same as the traditional quenching and tempering, the problems that the performance difference of the same plate is large, the plate shape is difficult to control accurately and the like are faced.
Chinese patent CN201310367890.5 discloses a high nitrogen austenitic stainless steel, the N content of which is more than 1.0%. In fact, in an industrial mass production mode, products with N content higher than 1.0% cannot be stably produced at present. Therefore, the production of high nitrogen steel is also essentially in the laboratory or pilot plant stage, with size limitations.
Disclosure of Invention
The invention aims to provide high-strength nitrogen-containing economical austenitic stainless steel and a manufacturing method thereof, wherein the grain size of a metallographic structure of the steel is below 500nm, the yield strength of the steel is more than or equal to 650MPa, the tensile strength of the steel is more than or equal to 1000MPa, the elongation of the steel is more than or equal to 35%, the strength of the steel material is obviously improved, good plasticity is kept, and the steel has the advantages of small performance difference of the same steel plate and good plate shape.
In order to achieve the purpose, the technical scheme of the invention is as follows:
the high-strength nitrogen-containing economical austenitic stainless steel comprises the following chemical components in percentage by weight: c: 0.05-0.15%, Si: 0.3-1%, Mn: 8.5-11.0%, Cr: 14.0-16.0%, Ni: 1.0-2.5%, N: 0.10-0.25%, P < 0.08%, S < 0.01%, Cu: 0.5-2.0%, Mo: 0.1-0.5%, and the balance of Fe and inevitable impurities, wherein the elements simultaneously satisfy the following relations:
Md30/50≥20℃，Md30/50the calculation formula is as follows:
Md30/50＝413-462*(C％+N％)-9.2*Si％-8.1*Mn％-9.5*Ni％-3.7*Cr％-18.5*Mo％。
preferably, the high-strength nitrogen-containing economical austenitic stainless steel has a Mn: 9.5 to 10.5 percent by weight.
Preferably, the high-strength nitrogen-containing economical austenitic stainless steel has a Cr: 14-15% by weight.
Preferably, the high-strength nitrogen-containing economical austenitic stainless steel has a Ni: 1.5 to 2.0 percent by weight.
Preferably, the high-strength nitrogen-containing economical austenitic stainless steel has a nitrogen content of N: 0.10-0.20% by weight.
Preferably, the high-strength nitrogen-containing economical austenitic stainless steel has a Cu: 1.0 to 1.5 percent by weight.
Preferably, in the high-strength nitrogen-containing economical austenitic stainless steel, the ratio of Mo: 0.1 to 0.5 percent by weight.
Furthermore, the metallographic structure of the high-strength nitrogen-containing economical austenitic stainless steel is a single austenitic structure, and the grain size is less than or equal to 500 nm.
The yield strength of the high-strength nitrogen-containing economical austenitic stainless steel is more than or equal to 650MPa, the tensile strength is more than or equal to 1000MPa, and the elongation is more than or equal to 35%.
The steel of the invention has the following functions of the elements in the design of the steel components:
c: c is an element that strongly forms, stabilizes and expands the austenite region, and plays an important role in forming an austenite structure at room temperature. However, the C content is too high, which reduces the plasticity of the stainless steel and is unfavorable for the corrosion resistance of the stainless steel, so the C content is controlled to be 0.05-0.15 percent.
Mn: mn is a relatively weak austenite-forming element, but is a strong austenite structure-stabilizing element in stainless steel, and can improve the solubility of N in steel. In the low nickel type austenitic stainless steel, Mn acts in combination with elements such as C, N in the steel, and partially substitutes Ni to ensure that the stainless steel has an austenitic structure at room temperature. However, Mn has a negative influence on the corrosion resistance of the austenitic stainless steel, so that the Mn content cannot be too high, and the Mn content is controlled to be 8.5-11%, preferably, the Mn: 9.5 to 10.5 percent.
Cr: cr is the most important alloy element in stainless steel and is a guarantee for obtaining stainless steel rust resistance and corrosion resistance. The reason why the Cr content of the steel is controlled to be 14-16% and cannot be too high is to obtain a single austenite structure at room temperature. The preferable range of the Cr content in the invention is 14-15%.
Mo: mo is also an important element for improving the corrosion resistance of the stainless steel, Mo microalloying is carried out for improving the corrosion resistance, and researches show that the coordination of the Mo and the N has an obvious effect on improving the corrosion resistance of the stainless steel. However, since Mo is a noble metal element, the content of Mo added to the steel of the present invention is controlled to be 0.1 to 0.5%, and preferably, Mo: 0.1 to 0.5 percent.
Ni: ni is the most important element for forming and stabilizing an austenite phase, and can also enhance the capability of stainless steel in resisting reducing acid and improve the processing performance, but in order to reduce the cost, the content of Ni is greatly reduced and is controlled to be 1-2.5%, preferably, the ratio of Ni: 1.5 to 2.0 percent.
N: n is an element that forms, stabilizes, and expands the austenite region very strongly in stainless steel. Besides replacing precious resources such as Ni, N in the stainless steel can also obviously improve the strength of the material on the premise of not obviously reducing the plasticity and toughness of the material, and can also improve the stainless steel in rust resistance and corrosion resistance, delay the precipitation of carbide and the like. However, due to the limited solubility of N in stainless steel, in order to avoid the steel from forming subcutaneous bubbles during solidification, the amount of N must be determined in coordination with other alloying elements to ensure that N is present in a solid solution state and in combination with other alloying elements to ensure that the stainless steel has a single phase austenitic structure at room temperature. Therefore, the content of N is controlled to be 0.10-0.25%, and preferably, the content of N: 0.10 to 0.20 percent.
Cu: the Cu can improve the cold processing performance of the stainless steel, and the cold work hardening index of the stainless steel is obviously reduced along with the increase of the Cu content, so that the Cu content of the steel is kept at a high content, specifically controlled at 0.5-2.0%, and preferably, the Cu: 1.0 to 1.5 percent.
Si: si is added as a deoxidizer in the smelting process of low-nickel austenitic stainless steel, and therefore, in order to control the low total [ O ] content in the steel, the steel must have a certain reduced Si content. However, Si is a ferrite-forming element in stainless steel, and the Si content must be limited in order to ensure that the stainless steel has a single-phase austenitic structure at room temperature. The invention controls the content of Si to be 0.3-1.0%.
P: p is considered as a harmful element in stainless steel, and the lower the amount should be controlled, the better.
S: considering that the steel of the present invention has a high Mn content and easily forms MnS inclusions, affecting corrosion resistance, it is required to control the S content at a low level.
The invention relates to a method for manufacturing a high-strength nitrogen-containing economical austenitic stainless steel, which comprises the following steps:
1) smelting and casting
Smelting the chemical components in an electric furnace, smelting in a converter, refining outside the furnace, and continuously casting into a blank;
2) hot rolling + hot rolling annealing pickling
3) One-time cold rolling and one-time flexible annealing
The primary cold rolling reduction is 50-80%; the primary flexible annealing temperature is 800-950 ℃, and the annealing heat preservation time is 1-3 min;
4) secondary cold rolling and secondary flexible annealing
The secondary cold rolling reduction is 50-80%; the secondary flexible annealing temperature is 800-950 ℃, and the annealing heat preservation time is 1-3 min.
Further, in the step 1), Si deoxidation is adopted in the converter smelting process, and the content of reduced Si is controlled to be 0.3-1.0%.
In the step 1), in the external refining process, the refining time is more than or equal to 40 minutes, the argon gas soft stirring time is more than or equal to 10 minutes, and Ca treatment is carried out.
And the metallographic structure of the high-strength nitrogen-containing economical austenitic stainless steel is a single austenitic structure, and the grain size is less than or equal to 500 nm.
The yield strength of the high-strength nitrogen-containing economic austenitic stainless steel is more than or equal to 650MPa, the tensile strength is more than or equal to 1000MPa, and the elongation is more than or equal to 35%.
In the manufacturing process of the invention:
in the smelting process of the converter, Si is adopted for deoxidation, and the content of reduced Si is controlled to be 0.3-1.0%. The maintenance of the reduced Si content in the steel is an effective measure for reducing the total [ O ] content in the steel, and the lower the total [ O ] content in the steel, the lower the inclusion content, thereby improving the polishing properties. When the content of reduced Si is more than 0.3%, the total [ O ] content in the molten steel can be reduced to below 50ppm, and the purity of the molten steel can be well ensured.
In the external refining process, the invention ensures that the refining time is not less than 40 minutes, the argon soft stirring time is not less than 10 minutes, and the Ca treatment is carried out. The refining and argon soft stirring time with enough time is ensured, so that impurities in the molten steel can be promoted to float sufficiently, and the purity of the molten steel is improved. For the possible presence of high melting point Al in the steel2O3The inclusion is modified through Ca treatment, so that the influence of high-melting-point inclusion on subsequent processing performance can be reduced, the surface quality of a finished product is improved, and the corrosion resistance is favorably improved.
The method adopts a mode of cold rolling and flexible annealing twice to refine crystal grains, wherein the rolling reduction of each cold rolling is 50-80%, the flexible annealing temperature is 800-950 ℃, and the annealing heat preservation time is 1-3 min. In the invention, the metastable austenite forms a large amount of deformed martensite through cold rolling, and then is annealed to refine grains.
The invention adopts a cold rolling and flexible annealing process to obtain nano-scale grains, improves the strength of the material and keeps higher plasticity, and the main principle is as follows: the structure of the material is transformed from austenite to deformed martensite by cold rolling deformation, due to the Md of the invention30/50Maintaining a higher temperature (Md)30/50Not less than 20 ℃), the austenite structure is unstable in the cold rolling deformation process and is easy to be transformed into martensite, the deformation martensite amount (volume fraction) can reach more than 80% after the cold rolling is finished, and the original austenite structure is fully crushed. And then carrying out flexible annealing, and recrystallizing the fully-crushed structure, wherein for the steel component system, the recrystallization temperature can be reached within the temperature range of 800-950 ℃, and compared with the existing annealing temperature (more than or equal to 1100 ℃), the annealing temperature is lower, and the structure is not easy to grow, so that the effect of refining grains is achieved. The nano-scale crystal grains are finally obtained through the crystal grain crushing and recrystallization twice, and the strength of the material can be greatly improved according to a Hall-Petch formula.
According to the invention, through scientific alloy design, on the premise of greatly reducing the cost of raw materials, excellent corrosion resistance and mechanical properties are obtained. In addition, through a reasonable flexible annealing process, the material obtains the grain size of a nanometer level, so that the strength of the material is greatly improved, and meanwhile, the material has good plasticity. And moreover, the processing mode of repeated mechanical deformation (cold rolling) and flexible annealing is adopted to obtain crystal grains with the size of below 500nm, the tensile strength of the material is ensured to be above 1000MPa, the advantages of small difference between the performances of the strip steel and the plate and good plate shape are achieved, and the difficulty that the plate shape is difficult to control in the traditional high-strength thin-specification steel preparation process is overcome. Therefore, the invention is very suitable for preparing high-strength thin-specification precise strip steel.
The invention has the beneficial effects that:
on the premise of greatly reducing the use of noble metal Ni, the austenitic stainless steel disclosed by the invention is added with a certain amount of Mn, N, Cu and other elements, so that a single austenitic structure at room temperature is obtained, and the austenitic stainless steel has excellent cold processing performance. In addition, the steel grade of the invention contains higher Cr content, and a small amount of Mo element is added, so that the product has good corrosion resistance.
In the manufacturing process, the invention refines crystal grains by two times of cold rolling and flexible annealing and utilizing the generation and inversion of deformed martensite, and finally obtains the crystal grains with the size below 500nm, thereby greatly improving the strength of the material, ensuring that the yield strength of the steel is more than or equal to 650MPa, the tensile strength is more than or equal to 1000MPa, and simultaneously having the elongation of more than 35 percent.
The steel material has high strength and high plasticity, and can well replace the stainless steel hard steel obtained by cold rolling and tempering at present. Meanwhile, compared with the traditional quenching and tempering rolling, the flexible annealing method adopted by the invention has the advantages of good plate shape and stable and uniform performance in the preparation of extremely thin products, and is a novel method for producing high-strength stainless steel precise strip steel.
Drawings
FIG. 1 is a photograph of a metallographic structure of a steel after thermal annealing and pickling in example 1 of the present invention.
FIG. 2 is a photograph showing the results of the intergranular corrosion test of the steel of example 2 of the present invention.
FIG. 3 is a photograph of the metallographic structure of steel according to example 3 of the present invention.
Detailed Description
The invention is further illustrated by the following examples and figures.
Example 1
The steel components are shown in table 1, and the two-step smelting of an electric furnace and AOD is adopted, the content of reduced Si in molten steel is controlled to be more than 0.3% in the smelting process, and the actual field analysis is 0.45%. And the LF station refining time is not less than 40min, and is actually 45 min. The argon blowing soft stirring time is not less than 10min, actually 12 min. And performing Ca treatment and B microalloying at the end point of the LF station. And continuously casting the molten steel to obtain a plate blank, and carrying out hot rolling, hot annealing and pickling, primary cold rolling, primary flexible annealing and pickling, secondary cold rolling and secondary flexible annealing and pickling on the plate blank and flattening to produce the strip steel with the 2B surface state. Wherein the primary cold rolling reduction is 55%, the primary flexible annealing temperature is 850 ℃, the primary flexible annealing time is 2min, the secondary cold rolling reduction is 55%, the secondary flexible annealing temperature is 850 ℃, and the secondary flexible annealing heat preservation time is 3 min. Component detection shows that: the total oxygen content [ O ] of the strip is less than 50ppm, and actually 38 ppm. The grade of inclusions in steel was evaluated by the metallographic method according to GB/T10561-2005, and the results are shown in Table 2. The metallographic structure of the steel of this example is shown in FIG. 1.
As is clear from Table 2, the number of inclusions in the steel of the present invention was small. Therefore, the manufacturing process of the invention can obtain high-purity molten steel, and is beneficial to improving the corrosion resistance of the material.
The results of the mechanical property tests of this example are shown in Table 3.
FIG. 1 shows the metallographic structure after thermal annealing and pickling. As can be seen from FIG. 1, the metallographic structure of the steel of the present invention is a single austenitic structure, and it can be seen that the present invention obtains a single austenitic structure at room temperature by adding reasonable elements such as Mn, N, etc. on the premise of reducing the content of the noble metal Ni element.
Example 2
The steel components are shown in table 1, the two-step smelting method of an electric furnace and AOD is adopted, the control requirement of the smelting process is the same as that of the embodiment 1, and the actual values of all main control points are as follows: the LF refining time is 40min, and the argon blowing soft stirring time is 15 min. The molten steel is subjected to continuous casting, hot rolling annealing and pickling, primary cold rolling, primary flexible annealing and pickling, secondary cold rolling, secondary flexible annealing and pickling and leveling to produce the 2B surface state high-strength nickel-saving austenitic stainless steel thin strip, wherein the primary cold rolling reduction is 60%, the primary flexible annealing temperature is 800 ℃, the primary flexible annealing time is 3min, the secondary cold rolling reduction is 50%, the secondary flexible annealing temperature is 900 ℃, and the secondary flexible annealing heat preservation time is 3 min. The results of the mechanical property tests of this example are shown in Table 3.
The material is subjected to the pitting corrosion performance test by GB/T17897-1999, and the test result is as follows: the weight loss ratio (g/m 2 h) of the material is 7.89, so that the steel has better pitting corrosion resistance.
FIG. 2 shows the results of the intergranular corrosion test of this example. As can be seen from FIG. 2, the adoption of the two cold rolling and two flexible annealing processes can completely dissolve the carbide in the finished product, and no intergranular corrosion occurs.
Example 3
The steel components are shown in table 1, the two-step smelting method of an electric furnace and AOD is adopted, the control requirement of the smelting process is the same as that of the embodiment 1, and the actual values of all main control points are as follows: the LF refining time is 40min, and the argon blowing soft stirring time is 15 min. The molten steel is subjected to continuous casting, hot rolling, hot annealing and pickling, primary cold rolling, primary flexible annealing and pickling, secondary cold rolling, secondary flexible annealing and pickling and leveling to produce the 2B surface state high-strength nickel-saving austenitic stainless steel thin strip. The primary cold rolling reduction is 60%, the primary flexible annealing temperature is 850 ℃, the primary flexible annealing time is 3min, the secondary cold rolling reduction is 50%, the secondary flexible annealing temperature is 900 ℃, and the secondary flexible annealing time is 1.5 min. The results of the mechanical property tests of this example are shown in Table 3.
The metallographic structure of this example is shown in fig. 3. As can be seen from FIG. 3, the grain size in the metallographic structure was about 500 nm. Therefore, the metastable austenite forms a large amount of deformed martensite through cold rolling, and then is annealed to refine grains. In addition, the invention controls the grain size of the material at the nanometer level through two times of cold rolling and flexible annealing, greatly improves the strength of the material and can keep good plasticity.
Example 4
The steel components are shown in table 1, the two-step smelting of an electric furnace and AOD is adopted, the control requirement of the smelting process is the same as that of the embodiment 1, and the actual values of all main control points are as follows: the LF refining time is 40min, and the argon blowing soft stirring time is 15 min. The molten steel is subjected to continuous casting, hot rolling, hot annealing and pickling, primary cold rolling, primary flexible annealing and pickling, secondary cold rolling, secondary flexible annealing and pickling and leveling to produce the 2B surface state high-strength nickel-saving austenitic stainless steel thin strip. The primary cold rolling reduction is 60%, the primary flexible annealing temperature is 850 ℃, the primary flexible annealing time is 1min, the secondary cold rolling reduction is 60%, the secondary flexible annealing temperature is 900 ℃, and the secondary flexible annealing time is 1 min. The results of the mechanical property tests of this example are shown in Table 3.
As can be seen from Table 3, the yield strength of the steel of the invention is more than or equal to 650MPa, the tensile strength is more than or equal to 1000MPa, and the elongation is more than or equal to 35 percent.
Table 1 units: wt.%
| C | Si | S | P | Cr | Mn | Ni | N | Cu | Mo | |
| Example 1 | 0.080 | 0.45 | 0.001 | 0.02 | 14.0 | 8.9 | 1.25 | 0.11 | 1.00 | 0.50 |
| Example 2 | 0.065 | 0.63 | 0.002 | 0.03 | 16.0 | 8.5 | 1.08 | 0.20 | 0.70 | 0.35 |
| Example 3 | 0.030 | 1.00 | 0.002 | 0.03 | 14.8 | 11.0 | 2.40 | 0.22 | 1.58 | 0.10 |
| Example 4 | 0.050 | 0.67 | 0.003 | 0.02 | 15.3 | 10.2 | 1.9 | 0.15 | 1.85 | 0.15 |
TABLE 2
TABLE 3
| Yield strengthDegree (MPa) | Tensile strength (MPa) | Elongation (%) | |
| Example 1 | 702 | 1105 | 36.9 |
| Example 2 | 680 | 1058 | 39.01 |
| Example 3 | 712 | 1103 | 35.80 |
| Example 4 | 691 | 1005 | 38.47 |
Claims (11)
1. The high-strength nitrogen-containing economical austenitic stainless steel comprises the following chemical components in percentage by weight: c: 0.05-0.15%, Si: 0.3-1%, Mn: 8.5-11.0%, Cr: 14.0-16.0%, Ni: 1.0-2.5%, N: 0.10-0.25%, P < 0.08%, S < 0.01%, Cu: 0.5-2.0%, Mo: 0.1-0.5%, and the balance of Fe and inevitable impurities, wherein the elements simultaneously satisfy the following relations:
md30/50 is more than or equal to 20 ℃, and the calculation formula of Md30/50 is as follows:
Md30/50＝413-462*(C％+N％)-9 .2*Si％-8 .1*Mn％-9 .5*Ni％-3 .7*Cr％-18 .5*Mo％；
the preparation method of the high-strength nitrogen-containing economical austenitic stainless steel comprises the following steps:
1) smelting and casting
According to the chemical components of the high-strength nitrogen-containing economic austenitic stainless steel, continuously casting the high-strength nitrogen-containing economic austenitic stainless steel into a blank through electric furnace smelting, converter smelting and external refining;
2) hot rolling and hot rolling annealing pickling;
3) one-time cold rolling and one-time flexible annealing
The primary cold rolling reduction is 50-60%, the primary flexible annealing temperature is 800-900 ℃, and the annealing heat preservation time is 1-3 min;
4) secondary cold rolling and secondary flexible annealing
The secondary cold rolling reduction is 50-60%, the secondary flexible annealing temperature is 800-900 ℃, and the annealing heat preservation time is 1-3 min.
2. The high strength nitrogen-containing economical austenitic stainless steel according to claim 1, wherein the chemical composition of the high strength nitrogen-containing economical austenitic stainless steel is characterized in that the ratio of Mn: 9.5 to 10.5 percent by weight.
3. The high strength nitrogen-containing economical austenitic stainless steel of claim 1 or 2, wherein the chemical composition of the high strength nitrogen-containing economical austenitic stainless steel is Cr: 14-15% by weight.
4. The high strength nitrogen-containing economical austenitic stainless steel of any of claims 1-3, wherein the chemical composition of the high strength nitrogen-containing economical austenitic stainless steel is Ni: 1.5 to 2.0 percent by weight.
5. The high strength nitrogen-containing economical austenitic stainless steel of any of claims 1-4, wherein the chemical composition of the high strength nitrogen-containing economical austenitic stainless steel is N: 0.10-0.20% by weight.
6. The high strength nitrogen-containing economical austenitic stainless steel of any of claims 1-5, wherein the chemical composition of the high strength nitrogen-containing economical austenitic stainless steel is Cu: 1.0 to 1.5 percent by weight.
7. The high strength nitrogen-containing economical austenitic stainless steel of any of claims 1-6, wherein the chemical composition of the high strength nitrogen-containing economical austenitic stainless steel is Mo: 0.1 to 0.5 percent by weight.
8. The high strength nitrogen-containing economical austenitic stainless steel according to any one of claims 1 to 7, wherein the metallographic structure of the high strength nitrogen-containing economical austenitic stainless steel is a single austenitic structure, and the grain size is 500nm or less.
9. The high strength nitrogen-containing economical austenitic stainless steel of any of claims 1-8, wherein the high strength nitrogen-containing economical austenitic stainless steel is provided
The yield strength of the high-strength nitrogen-containing economical austenitic stainless steel is more than or equal to 650MPa, the tensile strength is more than or equal to 1000MPa, and the elongation is more than or equal to 35%.
10. The high-strength economical austenitic stainless steel containing nitrogen according to claim 1, wherein in the step 1), Si deoxidation is adopted in a converter smelting process, and the Si content is controlled to be 0.3-1.0%.
11. The high-strength economical austenitic stainless steel containing nitrogen according to claim 1, wherein in the step 1), in the refining process outside the furnace, the refining time is not less than 40 minutes, the argon gas soft stirring time is not less than 10 minutes, and the Ca treatment is performed.
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