CN114196880B - High-strength low-yield-ratio austenitic stainless steel and preparation method thereof - Google Patents
High-strength low-yield-ratio austenitic stainless steel and preparation method thereof Download PDFInfo
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- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- 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
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
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- 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
- C21D2211/008—Martensite
Abstract
A high-strength low-yield-ratio austenitic stainless steel and a preparation method thereof are disclosed, and the austenitic stainless steel comprises the following chemical components in percentage by weight: less than or equal to 0.10 percent of C, less than or equal to 1.00 percent of Si, 3.50 to 5.50 percent of Mn3.00 to 17.00 percent of Cr15.00 to 5.50 percent of Ni4.50 to 5.50 percent of N, less than or equal to 0.10 percent of P, less than or equal to 0.045 percent of S, and the balance of Fe and inevitable impurities; wherein the sum of the weight percentages of Cwt% and Nwt% is 0.12-0.18%. In the preparation process of the austenitic stainless steel: the heating temperature of the continuous casting billet is 1230-. The austenitic stainless steel prepared by the method can effectively meet the safety requirements of high strength and high yield ratio of the stainless steel material of the coal mine gas extraction pipe.
Description
Technical Field
The invention belongs to the technical field of austenitic stainless steel, and particularly relates to high-strength low-yield-ratio austenitic stainless steel and a preparation method thereof.
Background
In recent years, the coal mine gas extraction pipe is generally made of materials such as 304 stainless steel, however, due to the fact that the tensile strength and the yield strength are low, the pipe needs to be thick enough to meet the performance requirements of the pipe such as operation strength, rigidity and collision impact resistance under a mine, the weight of the pipe is increased due to the increase of the wall thickness, and adverse effects are brought to transportation and installation of the underground pipe. In addition, the geological structure of the working operation environment of the coal mine gas extraction pipe changes frequently, and the stress of the gas extraction pipe is more complex than that of the ground operation. Therefore, from the perspective of safe production, the important index of structural safety, "yield ratio", is the important mechanical property index of the pipe material. The yield ratio characterizes the deformation capacity of the material from plastic deformation to final fracture. In order to ensure the safety of the steel stress-bearing member and equipment, the steel is required to have sufficient plastic deformation before fracture, i.e. the steel is required to have a low yield ratio. Therefore, it is necessary to develop a stainless steel material for gas extraction pipes having high strength and a low yield ratio.
Disclosure of Invention
In order to overcome the defects in the prior art, the invention provides the high-strength low-yield-ratio austenitic stainless steel and the preparation method thereof, and the stainless steel with better structural safety is developed by adopting the idea of improving the material strength and reducing the yield ratio, so that the requirements of a mine gas extraction pipe and the like on the stainless steel material are met.
The invention is realized by the following technical scheme.
The high-strength low-yield-ratio austenitic stainless steel comprises the following chemical components in percentage by mass: less than or equal to 0.10 percent of C, less than or equal to 1.00 percent of Si, 3.50 to 5.50 percent of Mn, 15.00 to 17.00 percent of Cr, 4.50 to 5.50 percent of Ni, less than or equal to 0.10 percent of N, less than or equal to 0.045 percent of P, less than or equal to 0.030 percent of S, and the balance of Fe and inevitable impurities; wherein the sum of the weight percent of Cwt% and Nwt% is 0.12-0.18%.
C: c is an element capable of strongly forming and stabilizing and expanding the austenite region, and can act together with other austenitizing elements such as Mn and N to promote austenite formation. However, when the content of C is too large, C and Cr form Cr-rich carbide, which reduces the corrosion resistance of the material. Therefore, the C content is limited to 0.10% or less in the present invention.
Si: si is a ferrite-forming element which generally performs deoxidation during smelting, but an excessive Si content reduces the impact toughness and corrosion resistance of the steel. Therefore, the Si content in the present invention is limited to 1.00% or less.
Mn: mn is a relatively weak austenite-forming element, but has a strong austenite-stabilizing action, and can be combined with elements such as C, N to replace Ni to some extent, but if the Mn content is too high, the impact toughness of the steel is lowered. Therefore, the Mn content is limited to 3.50 to 5.50% in the present invention.
Cr: cr is an important element for obtaining the corrosion resistance of the steel, Cr in the stainless steel is more than or equal to 12.5 percent, a stable surface passivation film can be formed, the corrosion resistance of the steel is improved, and the Cr content in the invention is controlled to be more than 15.00 percent; however, Cr is a main ferrite forming element, and too high Cr content requires more elements such as Ni and Mn to be added into steel to ensure that a single-phase austenite structure is obtained, thereby increasing the material cost. Therefore, the Cr content in the steel of the present invention is limited to 15.00 to 17.00%.
Ni: ni is an element that strongly expands and stabilizes austenite, but it is expensive, and too high Ni content increases material cost, and too low decreases material toughness. Therefore, the Ni content in the present invention is limited to 4.50 to 5.50%.
N: n is an element which strongly forms and stabilizes austenite, has the forming capability equivalent to that of C and is about 30 times that of Ni, and is also favorable for improving the strength and the corrosion resistance when being added into steel as an alloy element. However, as the N content increases, the tendency of the nitride to precipitate increases, which is disadvantageous for the impact properties of the material. Therefore, the N content is limited to 0.10% or less in the present invention.
P, S: p, S is a harmful element in stainless steel, which has adverse effects on the thermoplasticity and properties of the material, and P is limited to 0.045% or less and S is limited to 0.030% or less in the steel of the present invention.
C + N: the C and N elements are solid solution strengthening elements, which can obviously improve the strength of the material, and simultaneously, the C and N elements are main elements influencing the strength of an alpha 'martensite phase, and the formation of the alpha' martensite can certainly reduce the ductility and toughness index of the material while improving the strength, so that in order to ensure that the austenitic stainless steel has high strength, good ductility and toughness and low yield ratio, the total content of C and N is controlled to be 0.12-0.18%.
Further, M of the austenitic stainless steel d30 The temperature is 50-80 ℃;
M d30 the temperature is the temperature at which 30% of the cold deformation of the alloy will result in 50% transformation of austenite to martensite, expressed in degrees C. d30 The lower the temperature, the higher the resistance of the material to martensitic transformation and, in turn, the lower the tendency to work harden by martensite. M is a group of d30 Calculated according to the following formula:
M d30 =551-462（Cwt%+Nwt%）-9.2Siwt%-8.1Mnwt%-29Niwt%-13.7Crwt% 。 (1)
further, gamma of the austenitic stainless steel SFE Is 4.5-9.5 mJ/m 2 ；
γ SFE The metal stacking fault energy represents the difficulty of austenite deformation induction to form martensite in the deformation process. Gamma ray SFE Calculated according to the following formula:
γ SFE （mJ/m 2 ）=-53+6.2Niwt%+0.7Crwt%+3.2Mnwt% 。 (2)
a preparation method of high-strength low-yield-ratio austenitic stainless steel comprises the following steps of firstly, smelting an austenitic stainless steel raw material by an electric furnace and AOD or VOD and LF, and preparing a continuous casting blank by a continuous casting process; secondly, rolling the continuous casting billet into a plate by a hot continuous rolling process; thirdly, the plate is annealed and pickled in a continuous annealing and pickling production line to prepare a finished plate, which is characterized in that: the heating temperature of the plate blank before the rolling of the continuous casting billet is controlled to be 1230-; the rolling temperature of the hot continuous rolling process is controlled to be not lower than 970 ℃; the annealing temperature of the rolled plate is controlled between 1040 ℃ and 1100 ℃, the annealing time is controlled between 0.7 min/mm and 1.2min/mm, and the cooling mode is air cooling or cooling speed.
Furthermore, the prepared austenitic stainless steel is in an austenitic structure in a solution-annealed state, and has the characteristics of high strength and low yield ratio, and the room-temperature mechanical properties are as follows: yield strength R p0.2 Not less than 300MPa, tensile strength R m More than or equal to 1000MPa, yield ratio less than or equal to 0.40 and elongation after fracture more than or equal to 40 percent.
Compared with the prior art, the invention has the beneficial effects that:
the high-strength low-yield-ratio austenitic stainless steel provided by the invention further optimizes and limits M by selecting a reasonable component system and matching alloy element components and contents d30 、γ SFE And the total amount of C and N, fully regulating and controlling the transformation of austenite deformation induced martensite. The austenitic stainless steel which meets the requirements of high strength and low yield ratio is obtained by inducing martensite transformation through austenite deformation and combining with a material work hardening mechanism, and the solution is realizedThe method has the advantages that the contradiction that the yield ratio is reduced due to the improvement of the strength of other steels can be effectively solved, the safety requirements of high strength and high yield ratio of the stainless steel material for the coal mine gas extraction pipe can be effectively met, and meanwhile, the method has the advantages of corrosion resistance and light weight.
Drawings
FIG. 1 is a microstructure diagram of a hot-rolled austenitic stainless steel sheet prepared in example 1 in a solution-annealed state.
Detailed Description
The following examples are intended to illustrate the invention but are not intended to limit the scope of the invention. Unless otherwise specified, the examples follow conventional experimental conditions. In addition, it will be apparent to those skilled in the art that various modifications or improvements can be made to the material components and amounts in these embodiments without departing from the spirit and scope of the invention as defined in the appended claims.
Example one
Smelting stainless steel by adopting an electric furnace, AOD and LF refining mode, and continuously casting to obtain a casting blank with the thickness of 200 mm; heating the casting blank to 1260 plus or minus 10 ℃ in a stepping heating furnace, and preserving the heat for 210 min; after discharging, rolling the steel plate into a hot rolled coil with the thickness of 5mm on a hot continuous rolling unit, wherein the final rolling temperature is 985 ℃; the hot-rolled coil is annealed and surface pickled in a continuous annealing and pickling line, the annealing temperature is 1050 +/-10 ℃, the annealing time is 5.5min, and the cooling mode is water cooling.
The annealed microstructure of the plate prepared in the first embodiment is single-phase austenite. The chemical composition of the austenitic stainless steel of the present example is shown in table 1, the mechanical properties and corrosion performance results are shown in table 2, and the annealed microstructure is shown in fig. 1.
Example two
Smelting stainless steel by adopting an electric furnace + VOD + LF refining mode, and obtaining a continuous casting billet with the thickness of 180mm through a continuous casting process; heating the continuous casting blank to 1250 +/-10 ℃ in a stepping heating furnace, and keeping the temperature for 200 min; after discharging, rolling the steel plate into a hot rolled coil with the thickness of 6mm on a hot continuous rolling unit, wherein the final rolling temperature is 997 ℃; the hot-rolled coil is annealed and surface pickled in a continuous annealing and pickling line, the annealing temperature is 1060 +/-10 ℃, the annealing time is 6min, and the cooling mode is water cooling.
The annealed microstructure of the plate obtained in the second example is single-phase austenite. The chemical composition of the austenitic stainless steel of the present example is shown in table 1, and the results of mechanical properties and corrosion properties are shown in table 2.
EXAMPLE III
Smelting stainless steel by adopting an electric furnace, AOD and LF refining mode, and obtaining a continuous casting billet with the thickness of 160mm through a continuous casting process; heating the continuous casting billet to 1240 +/-10 ℃ in a chamber heating furnace, preserving the heat for 185min, and rolling the continuous casting billet out of the furnace into a hot-rolled coil with the thickness of 3mm on a hot continuous rolling unit, wherein the final rolling temperature is 1008 ℃; the hot-rolled coil is annealed and surface pickled in a continuous annealing and pickling line, the annealing temperature is 1070 +/-10 ℃, the annealing time is 2.4min, and the cooling mode is water cooling. The annealed microstructure of the plate of this example was single-phase austenite.
The chemical compositions of the austenitic stainless steel prepared in the third embodiment are shown in table 1, and the results of the mechanical properties and the corrosion properties are shown in table 2.
Mechanical property tests and corrosion tests were conducted for examples 1 to 3 and comparative examples 1 to 2 in table 1. Wherein, the room temperature tensile test adopts standard GB/T228.1; the corrosion test adopts standard GB/T17989, corrosion medium: 6% FeCl 3 The test temperature was 35 ℃.
As can be seen from Table 2, the austenitic stainless steels prepared in examples 1 to 3 have higher yield strength and tensile strength than those of the stainless steel 304, and lower yield ratio than those of the stainless steel 304, and the corrosion resistance comparable to that of the stainless steel 304, compared with the conventional stainless steel 304.
The above description is only for the specific embodiments of the present invention, but the scope of the present invention is not limited thereto, and any changes or substitutions that can be easily conceived by those skilled in the art within the technical scope of the present invention are also within the scope of the present invention. Therefore, the protection scope of the present invention shall be subject to the protection scope of the appended claims.
Claims (3)
1. A preparation method of high-strength low-yield-ratio austenitic stainless steel comprises the following steps of firstly, smelting an austenitic stainless steel raw material by an electric furnace and AOD or VOD and LF, and preparing a continuous casting blank by a continuous casting process; secondly, rolling the continuous casting billet into a plate by a hot continuous rolling process; thirdly, the plate is annealed and pickled in a continuous annealing and pickling production line to prepare a finished plate, which is characterized in that: the heating temperature of the plate blank before the rolling of the continuous casting billet is controlled to be 1230-; the rolling temperature of the hot continuous rolling process is controlled to be not lower than 970 ℃; the annealing temperature of the rolled plate is controlled between 1040 ℃ and 1100 ℃, the annealing time is controlled between 0.7 min/mm and 1.2min/mm, and the cooling mode is air cooling or cooling speed;
the austenitic stainless steel comprises the following chemical components in percentage by mass: less than or equal to 0.10 percent of C, less than or equal to 1.00 percent of Si, 3.50 to 5.50 percent of Mn, 15.00 to 17.00 percent of Cr, 4.50 to 5.50 percent of Ni, less than or equal to 0.10 percent of N, less than or equal to 0.045 percent of P, less than or equal to 0.030 percent of S, and the balance of Fe and inevitable impurities; wherein the sum of the weight percentages of Cwt% and Nwt% is 0.12-0.18%;
the prepared austenitic stainless steel is in an austenitic structure in a solution annealing state, and has the room-temperature mechanical properties as follows: yield strength R p0.2 Not less than 300MPa, tensile strength R m More than or equal to 1000MPa, the yield ratio is less than or equal to 0.40, and the elongation after fracture is more than or equal to 40 percent.
2. A method of making a high strength low yield austenitic stainless steel as claimed in claim 1, wherein: m of the austenitic stainless steel d30 The temperature is 50-80 ℃; m is a group of d30 The temperature is the temperature at which 30% of the cold deformation of the alloy will result in 50% transformation of austenite to martensite, expressed in degrees C. d30 Calculated according to the following formula:
M d30 =551-462（Cwt%+Nwt%）-9.2Siwt%-8.1Mnwt%-29Niwt%-13.7Crwt% 。
3. a method as claimed in claim 1The preparation method of the high-strength low-yield-ratio austenitic stainless steel is characterized by comprising the following steps of: gamma of the austenitic stainless steel SFE Is 4.5-9.5 mJ/m 2 ；γ SFE Is a metal stacking fault energy of gamma SFE Calculated according to the following formula:
γ SFE （mJ/m 2 ）=-53+6.2Niwt%+0.7Crwt%+3.2Mnwt% 。
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| JP4289756B2 (en) * | 2000-03-16 | 2009-07-01 | 新日鐵住金ステンレス株式会社 | High strength metastable austenitic stainless steel wire |
| EP1867743B9 (en) * | 2005-04-04 | 2015-04-29 | Nippon Steel & Sumitomo Metal Corporation | Austenitic stainless steel |
| CN101270455B (en) * | 2007-03-23 | 2010-08-11 | 宝山钢铁股份有限公司 | 1000MPa grade nickel-saving type metastable austenite stainless steel |
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| JP5091732B2 (en) * | 2008-03-17 | 2012-12-05 | 日新製鋼株式会社 | Stainless steel for low Ni springs with excellent sag resistance and bendability |
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