CN112011747A - High-nitrogen steel and slab continuous casting process thereof - Google Patents

High-nitrogen steel and slab continuous casting process thereof Download PDF

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Publication number
CN112011747A
CN112011747A CN201910451149.4A CN201910451149A CN112011747A CN 112011747 A CN112011747 A CN 112011747A CN 201910451149 A CN201910451149 A CN 201910451149A CN 112011747 A CN112011747 A CN 112011747A
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nitrogen
steel
continuous casting
casting process
nitrogen steel
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郭亮亮
徐荣军
徐正其
徐国栋
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • B22D11/10—Supplying or treating molten metal
    • B22D11/11—Treating the molten metal
    • 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
    • B22D11/10—Supplying or treating molten metal
    • B22D11/11—Treating the molten metal
    • B22D11/114—Treating the molten metal by using agitating or vibrating means
    • B22D11/115—Treating the molten metal by using agitating or vibrating means by using magnetic fields
    • 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
    • B22D11/16—Controlling or regulating processes or operations
    • B22D11/18—Controlling or regulating processes or operations for pouring
    • 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
    • C22C38/001—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
    • 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
    • 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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Continuous Casting (AREA)

Abstract

The invention discloses high-nitrogen steel which comprises the following chemical elements in percentage by mass: c is more than 0 and less than or equal to 0.03 percent, Si is more than 0 and less than or equal to 1.0 percent, Mn: 5.0-12.0%, N: 0.2 to 1.2%, Cr: 20-28%, Ni: 1-10%, Nb: 0.01-0.4%, Al: 0.001-0.05%, Mo: 0.1-10%, W: 0.1-0.5%; the balance being Fe and other unavoidable impurities; wherein, Mo + W: 0.2 to 10 percent. In addition, the invention also discloses a slab continuous casting process of the high-nitrogen steel, wherein a crystallizer of the continuous casting process is hermetically filled with argon for pressurization so as to ensure the top atmosphere pressure P of the crystallizermIs 0.1 to 0.5 MPa. The high-nitrogen steel can fully exert the advantages of continuous casting production, can inhibit the generation of pores and cracks of a casting blank, obviously improve the surface and center quality of the casting blank, and can realize multi-furnace continuous casting.

Description

High-nitrogen steel and slab continuous casting process thereof
Technical Field
The invention relates to a steel grade and a manufacturing process thereof, in particular to high-nitrogen steel and a continuous casting process thereof.
Background
High nitrogen steel refers to a nitrogen-containing steel in which the nitrogen content in the steel exceeds the solubility limit of atmospheric pressure nitrogen, and a steel in which the nitrogen content in an austenitic matrix exceeds 0.4 wt% or the nitrogen content in a ferritic matrix exceeds 0.08 wt% is generally defined as a high nitrogen steel. The nitrogen is used as a gap element in the steel, and can improve various performances of the steel, such as strength, toughness, creep deformation, corrosion resistance, wear resistance and the like, through the synergistic effect of the nitrogen and other alloy elements, and the nitrogen is widely applied to industries of buildings, automobiles, energy sources, chemical engineering and the like. The common preparation process of high-nitrogen steel mainly comprises induction melting in high-pressure nitrogen atmosphere, electroslag remelting in high-pressure nitrogen atmosphere, high-pressure arc furnace melting, high-pressure nitrogen plasma melting, electroslag heating in steel ladle-high-pressure nitriding and the like, counter-pressure casting, diffusion and solid solution of nitrogen into solid steel, AOD and VOD refining furnace production and the like.
Although the method can produce high-nitrogen steel with higher nitrogen content, the product is scrapped due to the air holes caused by the segregation and precipitation of nitrogen in the solidification process.
Based on the above, it is desirable to obtain a high-nitrogen steel which has good quality of the surface and the center of a continuous casting billet in the production process, is not easy to generate nitrogen segregation and precipitation, and has high production efficiency and high product quality.
Disclosure of Invention
One of the purposes of the invention is to provide high-nitrogen steel which can overcome the defects of the prior art, is not easy to generate segregation and precipitation phenomena of nitrogen, and ensures that the surface and the center of a continuous casting billet are good in quality in the production process.
In order to achieve the purpose, the invention provides high-nitrogen steel which comprises the following chemical elements in percentage by mass:
c is more than 0 and less than or equal to 0.03 percent, Si is more than 0 and less than or equal to 1.0 percent, Mn: 5.0-12.0%, N: 0.2-1.2%, Cr: 20-28%, Ni: 1-10%, Nb: 0.01-0.4%, Al: 0.001-0.05%, Mo: 0.1-10%, W: 0.1-0.5%; the balance being Fe and other unavoidable impurities; wherein, Mo + W: 0.2 to 10 percent.
In the high nitrogen steel of the present invention, the design principle of each chemical element is as follows:
c: carbon is an element for enlarging an austenite region, but because the solubility of carbon in the nickel-rich alloy is very low, carbide is easily formed, and the alloy performance is influenced, the lower the carbon content is, the better the carbon content is, and therefore, the mass percent of C in the high-nitrogen steel can be controlled to be more than 0 and less than or equal to 0.03 percent.
Si: silicon is a strong ferrite forming element, has influence on the corrosion resistance of steel in certain specific corrosion mediums, is not too high in content and needs to be strictly controlled, so that the mass percent of Si in the high-nitrogen steel can be controlled to be more than 0 and less than or equal to 1.0 percent.
Mn: in the technical scheme of the invention, manganese has the function of strongly stabilizing austenite, can replace nickel in stainless steel, and can also increase the solubility of nitrogen, thereby saving nickel and improving strength. However, too high mass percent of manganese accelerates the precipitation of sigma phase and significantly reduces the toughness of the steel, so that the mass percent of Mn in the high-nitrogen steel can be controlled to be 5.0-12.0%.
N: in the high-nitrogen steel of the invention, nitrogen is an element which forms austenite very strongly and enlarges an austenite phase region, about 30 times of nickel, and besides the nickel-saving effect, the solid solution strengthening of nitrogen can obviously improve the strength of the steel without obviously damaging the plasticity and the toughness of the steel. In order to take account of the nitrogen alloying effect and the production difficulty, the mass percent of N is controlled to be 0.2-1.2% in the technical scheme of the invention.
Cr: in the technical scheme of the invention, Cr is one of the most important alloy elements with pitting corrosion resistance in high-nitrogen steel, and can improve the acid resistance, salt resistance and oxidation resistance of the alloy. Moreover, when the chromium content reaches a certain amount, the corrosion resistance of the steel is mutated. Therefore, in the technical scheme of the invention, the mass percent of Cr is controlled to be 20-28%.
Ni: in the solution according to the invention, the main role of nickel is to form an austenitic crystal structure, thereby improving properties of the steel such as plasticity, weldability and toughness. On the other hand, in the high nitrogen steel of the present invention, since it is a dual phase steel in which Cr is 20 to 28% by mass, if the mass percentage of Ni is too low, the ferrite phase in the steel increases, and the ductility and toughness of the steel are reduced. And when the mass fraction of nickel reaches 10%, the tensile strength reaches the highest value. Therefore, in the high-nitrogen steel, the mass percent of Ni is controlled to be 1-10%.
Nb: in the high-nitrogen steel, niobium is a ferrite forming element, and can preferentially form carbon and nitride when added into the steel, so that the harm caused by carbon and nitrogen is reduced; however, too high mass percent of niobium will deteriorate the steel production process, causing a large amount of surface defects, increasing the amount of grinding, decreasing the yield and increasing the cost. Based on this, the mass percent of Nb is controlled to be 0.01-0.4% in the technical scheme of the invention.
Al: in the technical scheme, aluminum is a ferrite forming element, and the ferrite forming capacity is 2.5-3.0 times of that of chromium. Its functions are ageing strengthening, improving tempering stability and increasing secondary hardening effect. Because the aluminum-containing inclusion can increase the susceptibility of the high-nitrogen steel to pitting corrosion, the mass percent of Al is not too high, so that the mass percent of Al in the high-nitrogen steel is controlled to be 0.001-0.05%
Mo and W: in the high-nitrogen steel, molybdenum is used for improving pitting corrosion resistance and crevice corrosion resistance of the high-nitrogen steel, and tungsten acts like molybdenum and mainly improves local corrosion resistance such as pitting corrosion resistance and crevice corrosion resistance of the alloy. However, when the mass percentages of molybdenum and tungsten are too high, both hot and cold working are difficult, and scale peeling or peracid is more observed in the case of pickling the scale. Therefore, in the technical scheme of the invention, the mass percent of Mo is controlled to be 0.1-10%, the mass percent of W is controlled to be 0.1-10%, and the total mass percent of Mo and W is controlled to be Mo + W: 0.2 to 10 percent.
Furthermore, the high-nitrogen steel also contains Cu which is more than 0% and less than or equal to 2.0%.
In the scheme, the addition of Cu in the high-nitrogen steel can improve the performance of the steel, such as corrosion resistance, mechanical property, cold forming and cutting processability; however, if the mass percent of Cu is too high, the resulting Cu-rich phase deteriorates the hot workability of the steel, and therefore, in the embodiment of the present invention, the mass percent of Cu is controlled to be 0 < Cu < 2.0%.
Further, in the high nitrogen steel of the present invention, P is 0.04% or less and/or S is 0.01% or less among other inevitable impurities.
In the above solutions, P, S is an element harmful to the alloy, and the low melting point brittle material produced by it causes hot embrittlement, so in order to improve the performance of the high nitrogen steel of the present invention, P, S is controlled as follows: p is less than or equal to 0.04% and/or S is less than or equal to 0.01%.
Further, in the high nitrogen steel of the present invention, Cr equivalent CreqWith Ni equivalent of NieqThe ratio of the ratio is 1.5 to 2.5; wherein Nieq＝Ni％+30(C+N)％+0.5Mn％+0.3Cu％；Creq＝Cr％+1.5Mo％+1.5Si％+0.75％W+1.75Nb％+3.0Al％。
Accordingly, another object of the present invention is to provide a slab continuous casting process for high nitrogen steel, which can overcome the disadvantages of the prior art, so that the segregation and precipitation of nitrogen is not easily generated when the high nitrogen steel is produced, the production efficiency is improved, and the quality of the obtained product is optimized.
In order to achieve the aim, the invention also provides the slab continuous casting process of the high-nitrogen steel, wherein the crystallizer of the continuous casting process is hermetically filled with argon for pressurization so as to ensure the top atmosphere pressure P of the crystallizermIs 0.1 to 0.5 MPa.
Due to the factors that influence the solubility of nitrogen in steel, mainly temperature and pressure, for high nitrogen steels of certain composition. In the solidification process, the phase change process from liquid to ferrite to austenite of the high-nitrogen steel causes the nitrogen solubility to change suddenly, and the nitrogen solubility in the steel is changed due to the change of the metal structure. Generally, the solubility of nitrogen in liquid phase is higher than that in solid phase, and the solubility of nitrogen in austenite is higher than that in ferrite.
Therefore, the technical scheme provided by the invention emphasizes on solving the nitrogen precipitation behavior in the continuous casting and solidification process of the high-nitrogen steel. The inventor discovers through a large amount of experimental researches that high-nitrogen steel firstly separates out high-temperature ferrite along with temperature reduction in the solidification process, the solubility of nitrogen in the high-temperature ferrite is very low, the nitrogen content or nitrogen activity of a residual liquid phase of a dendritic arm of the high-temperature ferrite is higher and higher along with the temperature reduction, and nitrogen overflows from the high-temperature steel to form nitrogen bubbles when the nitrogen content or nitrogen activity is higher than the saturated solubility of the nitrogen in the steel; in the later stage of solidification, after austenite begins to be separated out, the nitrogen content in the molten steel is gradually reduced until the molten steel is completely solidified. In order to inhibit the nitrogen bubbles from being separated out, the continuous casting solidification process needs to meet the following requirements: ps+Pc+Pm>PN2Wherein P issThe static pressure generated by the molten steel at the position of the air hole is shown, and the dimension is MPa; pcDenotes the capillary pressure required for bubble formation, and has a dimension of MPa, PmThe atmospheric pressure at the top of the crystallizer is expressed, and the dimension of the atmospheric pressure is MPa; pN2Represents the nitrogen bubble deposition pressure in MPa. At PsAnd PcUnder the condition of no change, the top atmosphere pressure P of the crystallizer is increasedmThe sum of the three can be higher than PN2Thereby inhibiting the precipitation of nitrogen in the solidification process of the high-nitrogen molten steel.
Based on the above, in the slab continuous casting process of the invention, the crystallizer of the continuous casting process can be closely filled with argon for pressurization so as to ensure the top atmosphere pressure P of the crystallizermIs 0.1 to 0.5 MPa.
Further, in the slab continuous casting process of high nitrogen steel according to the present invention, the mold top atmosphere pressure PmIs 0.15 to 0.4 MPa.
Further, in the slab continuous casting process, the superheat degree of molten steel in the tundish is controlled to be 5-40 ℃.
In the scheme, the problems that when the superheat degree of the molten steel in the tundish is lower than 5 ℃, the molten steel has poor fluidity, so that a crystallizer water port is easy to freeze steel, and the pouring is forced to be interrupted are solved; however, if the molten steel in the tundish is higher than 40 ℃, the continuous casting solidification time is long, the nitrogen separation crystallization is sufficient, and the casting blank segregation and the porosity are aggravated. Based on this, the superheat degree of the molten steel in the tundish can be preferably controlled to be 5-40 ℃.
Furthermore, in the slab continuous casting process, the superheat degree of molten steel in the tundish is controlled to be 15-35 ℃.
Further, in the slab continuous casting process according to the present invention, the continuous casting process parameter is controlled to satisfy at least one of the following:
the blank drawing speed is 0.6-1.6 m/min;
the water amount of the wide surface of the crystallizer is 3500-4000L/min;
the current intensity of the electromagnetic stirring is 1200-2000A.
According to the scheme, the blank drawing speed is higher than 1.60m/min, the primary blank shell is thin, the casting blank is cooled unevenly, longitudinal cracks are easy to generate, and even steel leakage occurs, but if the blank drawing speed is lower than 0.60m/min, the solidification time in the crystallizer is too long, nitrogen solidification separation crystallization is sufficient, separation is easy, and the excessively low blank drawing speed influences the overall production capacity of the continuous casting machine, so that the blank drawing speed can be controlled to be 0.6-1.6 m/min in the technical scheme of the invention.
In addition, different from the prior art that the water amount of the wide surface of the crystallizer is controlled to be below 3000L/min, in some preferred embodiments, in order to increase the cooling strength, shorten the solidification time of high-nitrogen steel and inhibit the nitrogen separation crystallization time, a strong cooling measure is adopted, and the water amount of the wide surface of the crystallizer can be controlled to be 3500-4000L/min.
In addition, in order to improve segregation and loosening caused by nitrogen solidification for continuous casting, a secondary cooling zone electromagnetic stirring process can be added, and because the electromagnetic stirring current intensity is lower than 1200A, the secondary cooling zone electromagnetic stirring process has no effect on improving fusing (or breaking) dendritic crystals enriched in nitrogen, and because the electromagnetic stirring current intensity is higher than 2000A, the liquid level fluctuation of a crystallizer is large, and negative segregation is easy to occur to a casting blank. Therefore, the current intensity of the electromagnetic stirring can be preferably controlled to 1200 to 2000A.
Further, in the slab continuous casting process according to the present invention, the continuous casting process parameter is controlled to satisfy at least one of:
the blank drawing speed is 0.6-1.2 m/min;
the water amount of the wide surface of the crystallizer is 3600-3800L/min;
the current intensity of the electromagnetic stirring is 1400-2000A.
Compared with the prior art, the high-nitrogen steel and the slab continuous casting process thereof have the following advantages and beneficial effects:
the high-nitrogen steel is not easy to generate the segregation and precipitation phenomena of nitrogen, so that the surface and center quality of the continuous casting billet is good in the production process of the high-nitrogen steel, and the method is extremely effective in improving the continuous casting production efficiency of the high-nitrogen steel slab and the product quality.
In addition, the slab continuous casting process of the present invention also has the advantages and benefits described above.
Detailed Description
The high nitrogen steel and the slab continuous casting process thereof according to the present invention will be further explained and illustrated with reference to specific examples, which, however, should not be construed to unduly limit the technical scope of the present invention.
Examples 1 to 6
The high nitrogen steels of examples 1-6 above were prepared using the following procedure:
smelting and casting were carried out according to the chemical composition shown in Table 1, wherein the mold for the continuous casting process was hermetically filled with argon and pressurized so that the top atmosphere pressure P of the mold was increasedmThe superheat degree of the molten steel in the tundish is controlled to be 5-40 ℃, the blank drawing speed is 0.6-1.6 m/min, the water quantity of the wide surface of the crystallizer is 3500-4000L/min, and the current intensity of electromagnetic stirring is 1200-2000A.
It should be noted that in some preferred embodiments, the pressure P of the atmosphere at the top of the crystallizer may be adjustedmIs 0.15 to 0Under the pressure of 4MPa, the superheat degree of the molten steel in the tundish is controlled to be 15-35 ℃, the throwing speed is 0.6-1.2 m/min, the water amount of the wide surface of the crystallizer is 3600-3800L/min, and the current intensity of electromagnetic stirring is 1400-2000A.
Table 1 shows the mass percentages of the chemical elements of the high nitrogen steel of examples 1 to 6.
TABLE 1 (wt%, balance Fe and unavoidable impurity elements other than P and S)
Figure BDA0002075186250000061
Table 2 lists the specific process parameters involved in the manufacture of the high nitrogen steels of examples 1-6.
Table 2.
Figure BDA0002075186250000062
Table 3 shows the slab quality of examples 1 to 6 in this case
Table 3.
Examples Quality of casting blank
1 No air holes, central porosity and segregation of 0.5 grade
2 No air holes, center loose and segregation grade 1.5
3 No air holes, central porosity and segregation of 0.5 grade
4 No air holes, center loose and segregation of 1.0 grade
5 No air holes, center loose and segregation of 1.0 grade
6 No air holes, center loose and segregation grade 1.5
As can be seen from Table 3, the high-nitrogen steel finally obtained by adopting the slab continuous casting process can well overcome the defects of the prior art, no air holes are generated in each embodiment, and the surface and center quality of the casting blank is effectively improved.
Therefore, the high-nitrogen steel and the slab continuous casting process thereof can fully exert the advantages of continuous casting production, can inhibit the generation of pores and cracks of a casting blank, obviously improve the surface and center quality of the casting blank, and can realize multi-furnace continuous casting.
It should be noted that the prior art in the protection scope of the present invention is not limited to the examples given in the present application, and all the prior art which is not inconsistent with the technical scheme of the present invention, including but not limited to the prior patent documents, the prior publications and the like, can be included in the protection scope of the present invention.
In addition, the combination of the features in the present application is not limited to the combination described in the claims of the present application or the combination described in the embodiments, and all the features described in the present application may be freely combined or combined in any manner unless contradictory to each other.
It should also be noted that the above-mentioned embodiments are only specific examples of the present invention, and it is obvious that the present invention is not limited to the above-mentioned embodiments, and many similar variations are possible. All modifications which would occur to one skilled in the art and which are, therefore, directly derived or suggested from the disclosure herein are deemed to be within the scope of the present invention.

Claims (10)

1. The high-nitrogen steel is characterized by comprising the following chemical elements in percentage by mass:
c is more than 0 and less than or equal to 0.03 percent, Si is more than 0 and less than or equal to 1.0 percent, Mn: 5.0-12.0%, N: 0.2-1.2%, Cr: 20-28%, Ni: 1-10%, Nb: 0.01-0.4%, Al: 0.001-0.05%, Mo: 0.1-10%, W: 0.1-0.5%; the balance being Fe and other unavoidable impurities; wherein, Mo + W: 0.2 to 10 percent.
2. The high nitrogen steel as claimed in claim 1, further comprising 0 < Cu.ltoreq.2.0%.
3. The high nitrogen steel according to claim 1, wherein P.ltoreq.0.04% and/or S.ltoreq.0.01% among other unavoidable impurities.
4. High nitrogen steel according to any of claims 1-3, characterized in that the Cr equivalent CreqWith Ni equivalent of NieqThe ratio of the ratio is 1.5 to 2.5; wherein Nieq＝Ni％+30(C+N)％+0.5Mn％+0.3Cu％；Creq＝Cr％+1.5Mo％+1.5Si％+0.75％W+1.75Nb％+3.0Al％。
5. The continuous slab casting process of high nitrogen steel as claimed in any one of claims 1 to 4, characterized in that the crystallizer of the continuous casting process is closely filled with argon and pressurized to make the top atmosphere pressure P of the crystallizermIs 0.1 to 0.5 MPa.
6. Process for the continuous slab casting of high nitrogen steel according to claim 5, characterized in that the top atmosphere pressure P of the crystallizermIs 0.15 to 0.4 MPa.
7. The slab continuous casting process according to claim 5, wherein the superheat degree of the molten steel in the tundish is controlled to be 5-40 ℃.
8. The slab continuous casting process according to claim 7, wherein the degree of superheat of the molten steel in the tundish is controlled to be 15 to 35 ℃.
9. The slab casting process as claimed in claim 5, wherein the continuous casting process parameters are controlled to meet at least one of:
the blank drawing speed is 0.6-1.6 m/min;
the water amount of the wide surface of the crystallizer is 3500-4000L/min;
the current intensity of the electromagnetic stirring is 1200-2000A.
10. The slab casting process as claimed in claim 9, wherein the continuous casting process parameters are controlled to meet at least one of:
the blank drawing speed is 0.6-1.2 m/min;
the water amount of the wide surface of the crystallizer is 3600-3800L/min;
the current intensity of the electromagnetic stirring is 1400-2000A.
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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114619007A (en) * 2022-02-14 2022-06-14 包头钢铁（集团）有限责任公司 Production method of low-alloy high-nitrogen steel continuous casting billet

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CN101876024A (en) * 2009-04-30 2010-11-03 宝山钢铁股份有限公司 Production method for high-chrome continuous cast billet containing N duplex stainless steel of pipe blank
CN102770572A (en) * 2010-02-18 2012-11-07 新日铁住金不锈钢株式会社 Duplex stainless steel material for vacuum vessels, and process for manufacturing same
CN106756485A (en) * 2016-12-13 2017-05-31 东北大学 A kind of method that sensing of pressurizeing prepares high nitrogen steel with electroslag furnace under protective Ar gas remelting duplex

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EP0271459A1 (en) * 1986-11-17 1988-06-15 Sandvik Aktiebolag heat exchanger
CN101876024A (en) * 2009-04-30 2010-11-03 宝山钢铁股份有限公司 Production method for high-chrome continuous cast billet containing N duplex stainless steel of pipe blank
CN102770572A (en) * 2010-02-18 2012-11-07 新日铁住金不锈钢株式会社 Duplex stainless steel material for vacuum vessels, and process for manufacturing same
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* Cited by examiner, † Cited by third party
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CN114619007A (en) * 2022-02-14 2022-06-14 包头钢铁（集团）有限责任公司 Production method of low-alloy high-nitrogen steel continuous casting billet
CN114619007B (en) * 2022-02-14 2024-03-08 包头钢铁（集团）有限责任公司 Production method of low-alloy high-nitrogen steel continuous casting blank

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Application publication date: 20201201