CN113969332B - high-Mn ultralow-Ni dual-phase stainless steel and high-corrosion-resistance welding heat affected zone hot working method thereof - Google Patents
high-Mn ultralow-Ni dual-phase stainless steel and high-corrosion-resistance welding heat affected zone hot working method thereof Download PDFInfo
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Abstract
The invention discloses high-Mn ultralow-Ni duplex stainless steel and a high-corrosion-resistance welding heat affected zone hot working method thereof, belonging to the technical field of duplex stainless steel. The method comprises the steps of performing pre-forging treatment and pre-rolling treatment on a stainless steel casting blank, and performing water quenching to obtain a plate; carrying out solution treatment on the plate, and then carrying out water cooling; and carrying out welding heat cycle treatment after water cooling to obtain a welding heat treatment sample. The invention aims to reasonably control the heat treatment process and the welding heat parameters before welding to obtain the excellent intergranular corrosion resistance and the excellent corrosion resistance of a welding heat affected zone of the high Mn ultralow Ni duplex stainless steel, prepare a welding heat affected zone sample by controlling different solid solution temperatures and heat simulation welding input parameters of the high Mn ultralow Ni duplex stainless steel, and test the pitting corrosion resistance and the intergranular corrosion resistance by a potentiodynamic polarization curve and a double potentiodynamic reactivation method to obtain the high Mn ultralow Ni duplex stainless steel with the high pitting corrosion resistance and the high intergranular corrosion resistance of the welding heat affected zone.
Description
Technical Field
The invention relates to the technical field of duplex stainless steel, in particular to high Mn ultralow Ni duplex stainless steel and a high corrosion resistance welding heat affected zone hot working method thereof.
Background
The high-manganese nickel-saving type duplex stainless steel is a stainless steel with the duplex characteristics of austenite and ferrite, has good performance of resisting corrosion of various mediums, and is particularly widely popularized in the fields of petrochemical engineering, ocean engineering and the like in recent years. Compared with the austenitic stainless steel which is relatively mature in the prior research, the duplex stainless steel has good chloride corrosion resistance, has excellent welding performance compared with the austenitic stainless steel, and does not need post-welding heat treatment. Mn and N have similar functions and are used as austenite stabilizers, a certain amount of Mn is added to effectively promote the solubility of N in steel and obtain a two-phase balanced structure with good performance, and Mn replaces Ni element to improve the solubility of N and improve the comprehensive performance of the duplex stainless steel. At present, the price of Ni is 7-9 times of that of Mn under the same weight, ni element is a precious metal element and belongs to the strategic national resource, so the price rises year by year, and in addition, ni element has teratogenesis, carcinogenesis and other hazards to organisms, so the expensive Ni type duplex stainless steel is replaced by Mn with high corrosion resistance in a welding heat affected zone, the cost can be greatly reduced, the harm to human is also reduced, and the method has a great application prospect in the future.
With the expansion of the application field of duplex stainless steel, the corrosion resistance of duplex stainless steel is also continuously improved. However, there are many problems compared with the ordinary austenitic stainless steel welding, since the duplex stainless steel undergoes many thermal cycles during the welding process, although the process changes rapidly and for a short time, the proportion and distribution of phases in the weld zone and the heat affected zone of the welded joint are changed, and the corrosion resistance of the welded joint is affected. In addition, the duplex stainless steel contains more alloy elements, and intermetallic phases and carbonitrides are easily generated in the joint cooling process, so that a poor passivation element area is formed around weld metal, and the corrosion resistance of the joint is seriously affected. The 22Cr high Mn Ni-saving duplex stainless steel has excellent corrosion resistance in a welding heat affected zone. Chinese application CN108570629B discloses a high-strength corrosion-resistant duplex stainless steel and a method for preparing the same, which can improve the corrosion resistance of the duplex stainless steel by adjusting the N content in the steel during the refining process of molten steel, but the production process is extremely complex. The Chinese invention application CN111593269A discloses a seawater corrosion resistant duplex stainless steel and a preparation method thereof, and the preparation method is to add a certain amount of alloy elements and improve the seawater corrosion resistance after aging treatment. At present, the high Mn-saving Ni-saving type duplex stainless steel is still deficient in the environment that a heat affected zone of a welded joint is corrosive and complex.
At present, the corrosion resistance problem of austenitic stainless steel is relatively concerned domestically, the research on the corrosion resistance of a welding heat affected zone of high-manganese duplex stainless steel is less, the application of the current high-Mn duplex stainless steel in a very strong corrosive environment is less, a plurality of problems still exist in the use of the high-Mn duplex stainless steel due to the complexity of the corrosivity of the welding heat affected zone, and the problems such as high production cost and the like are solved, so that the use of the high-Mn ultralow Ni type duplex stainless steel in the corrosive complex environment is difficult to meet, the corrosion resistance of the high-Mn ultralow Ni type duplex stainless steel in the welding heat affected zone is researched, the problems can be effectively solved, and the application of the Ni saving duplex stainless steel in the corrosive complex environment can be effectively improved.
Disclosure of Invention
The invention aims to provide high-Mn ultralow-Ni dual-phase stainless steel and a high-corrosion-resistance welding heat affected zone hot working method thereof, so as to improve the corrosion resistance of the high-Mn dual-phase stainless steel welding heat affected zone. The method is characterized by obtaining the stainless steel based on vacuum smelting and hot compression experiments, testing the corrosion resistance of different heat input high Mn ultralow Ni duplex stainless steel solid solution states and welding heat simulation samples by adopting a cyclic potentiodynamic polarization curve and a double potentiodynamic reactivation method (DLEPR), analyzing the influence rules of different solid solution temperatures and different heat inputs on the corrosivity of a welding heat affected zone, and obtaining the high Mn ultralow Ni duplex stainless steel with a high corrosion resistance in the welding heat affected zone.
In order to achieve the purpose, the invention provides the following scheme:
one of the purposes of the invention is to provide a hot working method for a high-corrosion-resistance welding heat affected zone of stainless steel, which comprises the following steps:
(1) Adopting a vacuum smelting furnace to refine stainless steel, performing pre-forging treatment on a stainless steel casting blank, then performing pre-rolling treatment, and performing normal-temperature water quenching to obtain a plate;
(2) Carrying out solution treatment on the plate obtained in the step (1), and then carrying out normal-temperature water cooling;
(3) And (3) processing the water-cooled plate obtained in the step (2) into a size of 10.5mm multiplied by 60mm, and performing welding heat cycle treatment on a Gleeble-3800 thermal simulation experiment machine.
Further, in the step (1), the stainless steel casting blank comprises the following chemical components in percentage by mass: c:0.008 to 0.012%, si:0.02 to 0.04%, mn:10.50 to 11.10%, cr:21.06 to 22.05%, ni:0.02 to 0.04%, mo:0.72 to 1.01%, cu:0.25 to 0.36%, N:0.18 to 0.23%, P: less than or equal to 0.01 percent, S: less than or equal to 0.01 percent, and the balance of Fe and inevitable impurities.
Further, in the step (1), the conditions of the pre-forging process are as follows: the forging is started at 1100-1200 ℃, the forging ratio is 3-4, the finish forging temperature is more than or equal to 980 ℃, and the forging is cooled.
Further, in the step (1), the conditions of the pre-rolling treatment are as follows: the initial rolling temperature is set to be 1120-1180 ℃, and the final rolling temperature is higher than 960 ℃.
Further, in the step (2), the solution treatment is performed in a box-type resistance furnace under the conditions of: 960-1070 ℃,30-60min.
Further, when the temperature of the solution treatment is 960-1000 ℃, the heat input range is 0.80-1.50KJ/mm, and the pitting potential E is b When the temperature is more than or equal to 0.179V, the welding heat affected zone has high pitting corrosion resistance; the temperature of the solution treatment is 1030-1070 ℃, the heat input range is 0.80-2.08KJ/mm, ra<The weld heat affected zone at 27.00% has high resistance to intergranular corrosion.
Further, in the step (3), the welding heat cycle treatment conditions are as follows: the heat input range is 0.80-3.08KJ/mm, the temperature is raised to 1345 ℃ at the temperature rise rate of 200 ℃/s, and the temperature is kept for 1s.
The invention also aims to provide the high-Mn ultralow-Ni duplex stainless steel processed by the high-corrosion-resistance welding heat affected zone hot processing method.
The invention discloses the following technical effects:
the method of the invention is to reasonably control the heat treatment process and the welding heat parameters before welding to obtain the excellent intergranular corrosion resistance and pitting corrosion resistance of the high Mn ultralow Ni dual-phase stainless steel welding heat affected zone. The invention carries out smelting, forging and rolling treatment in a vacuum furnace, then carries out solution treatment at 960-1000 ℃, and then carries out welding thermal cycle in the heat input range of 0.80-1.50KJ/mm to obtain a high Mn ultralow Ni dual-phase stainless steel welding heat affected zone with pitting potential E b More than or equal to 0.179V and has high pitting corrosion resistance. Smelting in a vacuum furnace, forging and rolling, performing solution treatment at 1030-1070 ℃, and performing welding thermal cycle in a thermal input range of 0.80-2.08J/mm to obtain a welding thermal simulation influence area of the Mn ultralow Ni duplex stainless steel and an intercrystalline sensitivity value Ra<27.00%, corresponding to high intergranular corrosion resistance. The processing method of the high-corrosion-resistance welding heat affected zone of the high-Mn ultralow-Ni duplex stainless steel can promote the application of the low-cost stainless steel in the special fields of chemical pipelines, petrochemical industry, ocean engineering and the like.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings needed in the embodiments will be briefly described below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and it is obvious for those skilled in the art to obtain other drawings without creative efforts.
FIG. 1 is a cyclic voltammetry polarization test curve of five heat input samples and solid solution state samples in the range of welding thermal parameters of 0.848-2.935 KJ/mm at a solid solution temperature of 980 ℃ in example 1;
FIG. 2 is a double-ring electrochemical potentiodynamic reactivation method test curve (DLEPR) of a solid solution state sample of example 1 at a solid solution temperature of 980 ℃ and a welding thermal parameter of 0.848-2.935 KJ/mm under five different heat inputs;
FIG. 3 is a cyclic voltammetry polarization test curve of five different samples with different heat inputs and solid solution states in the range of solid solution temperature 1050 ℃ and welding thermal parameter 0.848-2.935 KJ/mm in example 2;
FIG. 4 is a double-loop electrochemical potentiodynamic reactivation method test curve (DLEPR) of a solid solution state sample of example 2 under five different heat inputs within a solid solution temperature of 1050 ℃ and a welding thermal parameter of 0.848-2.935 KJ/mm;
FIG. 5 is a graph showing the sensitivity of intergranular corrosion of five different heat input welding heat samples in example 1 at a solid solution temperature of 980 ℃ and a welding heat parameter of 0.848-2.935 KJ/mm;
FIG. 6 is a graph showing the comparison of the intergranular corrosion sensitivities of five different heat input welding heat samples in example 2 at a solid solution temperature of 1050 ℃ and a welding heat parameter of 0.848-2.935 KJ/mm;
FIG. 7 is a structural diagram of pitting corrosion resistance of a welding heat sample corresponding to the welding heat parameter of 0.848KJ/mm at a solid solution temperature of 980 ℃ in example 1;
FIG. 8 is a microstructure diagram of intergranular corrosion of a welding heat sample corresponding to the welding heat parameter of 1.895KJ/mm at the solid solution temperature of 1050 ℃ in example 2.
Detailed Description
Reference will now be made in detail to various exemplary embodiments of the invention, the detailed description should not be construed as limiting the invention but rather as a more detailed description of certain aspects, features and embodiments of the invention.
It is to be understood that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention. Further, for numerical ranges in this disclosure, it is understood that each intervening value, between the upper and lower limit of that range, is also specifically disclosed. Every smaller range between any stated value or intervening value in a stated range and any other stated or intervening value in a stated range is encompassed within the invention. The upper and lower limits of these smaller ranges may independently be included or excluded in the range.
Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. Although only preferred methods and materials are described herein, any methods and materials similar or equivalent to those described herein can be used in the practice or testing of the present invention. All documents mentioned in this specification are incorporated herein by reference to disclose and describe the methods and/or materials in connection with which the documents are cited. In case of conflict with any incorporated document, the present specification will control.
It will be apparent to those skilled in the art that various modifications and variations can be made in the specific embodiments of the present disclosure without departing from the scope or spirit of the disclosure. Other embodiments will be apparent to those skilled in the art from consideration of the specification. The description and examples are intended to be illustrative only.
As used herein, the terms "comprising," "including," "having," "containing," and the like are open-ended terms that mean including, but not limited to.
The room temperature referred to in the present invention is a room temperature, which is well known to those skilled in the art, and the room temperature referred to in the present invention is 25 ℃.
In the invention, cutting, back derusting, copper wire welding, gradual grinding, polishing, cleaning and sealing and insulating treatment of a non-working surface by adopting a rosin and paraffin mixture are all conventional operations.
Example 1
The stainless steel casting blank comprises the following chemical components in percentage by mass: c:0.01%, si:0.03%, mn:10.95%, cr:21.66%, ni:0.03%, mo:0.88%, cu:0.31%, N:0.21%, P:0.01%, S:0.01%, and the balance of Fe and inevitable impurities.
(1) Adopting a stainless steel cast blank smelted by a 50kg vacuum smelting furnace, pre-forging the stainless steel cast blank, starting forging at 1150 ℃, wherein the forging ratio is 3, the finish forging temperature is 980 ℃, and rapidly cooling after forging; then, carrying out pre-rolling treatment, setting the initial rolling temperature to be 1120 ℃, setting the final rolling temperature to be 980 ℃, and carrying out water quenching to obtain a plate;
(2) Carrying out solution treatment on the plate obtained in the step (1), wherein the conditions are as follows: at 980 ℃ for 30min, and then carrying out normal-temperature water cooling;
(3) And (3) processing the water-cooled plate obtained in the step (2) into a size of 10.5mm multiplied by 60mm, performing welding thermal cycle treatment at the speed of 0.848KJ/mm,1.468KJ/mm,1.895KJ/mm,2.542KJ/mm and 2.935KJ/mm respectively, heating to 1345 ℃ at the heating rate of 200 ℃/s, and preserving heat for 1s to obtain the high-Mn ultralow-Ni duplex stainless steel sample. The sample is subjected to cutting, back derusting, copper wire welding, gradual grinding, polishing, cleaning and sealing and insulating treatment on a non-working surface by adopting a rosin and paraffin mixture, and a 10mm multiplied by 10mm area is reserved on the working surface.
(4) Preparing a pitting solution and an intercrystalline corrosion solution, wherein the pitting solution is a 3.5wt% NaCl solution (1000 mLH) 2 O and 35g NaCl), the intergranular corrosion solution is H 2 SO 4 NaCl and KSCN as 1.2:1.1:0.01 molar ratio (1000 mL H) 2 O、54.35mL H 2 SO 4 29.25g NaCl, 0.97g KSCN). The corrosion resistance of the alloy is tested by a cyclic voltammetry potentiodynamic polarization curve and a double-ring potentiodynamic reactivation method (DLEPR). The electrochemical parameters for the potentiometric polarization curve fitting are collated in Table 1.
TABLE 1
FIG. 1 shows the zeta potential polarization curves of five samples with different heat inputs and solid solution states of 0.848KJ/mm,1.468KJ/mm,1.895KJ/mm,2.542KJ/mm and 2.935KJ/mm after solid solution at 980 ℃. As can be seen from Table 1, the pitting potential E is within the range of 0.80 to 1.50KJ/mm in heat input b More than or equal to 0.179V. Therefore, the pitting potential E is between 0.80 and 1.50KJ/mm b When the temperature is more than or equal to 0.179V, the welding heat affected zone has high pitting corrosion resistance. FIG. 7 shows SEM pitting morphology with heat input of 0.848KJ/mm, wherein δ represents ferrite phase and γ represents austenite phase, and it can be seen that pitting is mainly concentrated at ferrite and austenite grain boundaries and partially concentrated at ferrite and austenite grain boundariesInside the ferrite grains, no pitting occurred in the austenite phase. FIG. 2 shows five different heat input and solid solution state sample DLEPR test curves corresponding to 0.848KJ/mm,1.468KJ/mm,1.895KJ/mm,2.542KJ/mm and 2.935KJ/mm after solid solution at 980 ℃, and FIG. 5 shows five different heat input sample intercrystalline corrosion sensitivity values (Ra) corresponding to cooling t after solid solution at 980 ℃ and corresponding to 0.848KJ/mm,1.468KJ/mm,1.895KJ/mm,2.542KJ/mm and 2.935KJ/mm 8/5 The cooling time was 10s,30s,50s,90s and 120s, and it was found that Ra exhibited a tendency of increasing and then decreasing fluctuation, the solution temperature was solution-treated at 960-1000 ℃ and the heat input was 0.80-2.08KJ/mm, ra<The welding heat affected zone has high intergranular corrosion resistance at 72.50 percent.
Example 2
The stainless steel casting blank comprises the following chemical components in percentage by mass: c:0.01%, si:0.03%, mn:10.95%, cr:21.66%, ni:0.03%, mo:0.88%, cu:0.31%, N:0.21%, P:0.01%, S:0.01%, and the balance of Fe and unavoidable impurities.
(1) Adopting a stainless steel cast blank smelted by a 50kg vacuum smelting furnace, pre-forging the stainless steel cast blank, starting forging at 1150 ℃, wherein the forging ratio is 3, the finish forging temperature is 980 ℃, and rapidly cooling after forging; then, carrying out pre-rolling treatment, setting the initial rolling temperature to be 1120 ℃, setting the final rolling temperature to be 980 ℃, and carrying out water quenching to obtain a plate;
(2) Carrying out solution treatment on the plate obtained in the step (1) under the conditions that: at 1050 ℃ for 30min, and then carrying out normal-temperature water cooling;
(3) And (3) processing the water-cooled plate obtained in the step (2) into a size of 10.5mm multiplied by 60mm, performing welding thermal cycle treatment at the speed of 0.848KJ/mm,1.468KJ/mm,1.895KJ/mm,2.542KJ/mm and 2.935KJ/mm, heating to 1345 ℃ at the heating rate of 200 ℃/s, and preserving heat for 1s to obtain the high-Mn ultralow-Ni duplex stainless steel sample. The sample is subjected to cutting, back derusting, copper wire welding, gradual grinding, polishing, cleaning and sealing and insulating treatment on a non-working surface by adopting a rosin and paraffin mixture, and a 10mm multiplied by 10mm area is reserved on the working surface.
(4) Preparing a pitting solution and an intercrystalline corrosion solution, wherein the pitting solution is a 3.5wt% NaCl solution (1000 mLH) 2 O and 35g NaCl), and the intergranular corrosion solution is H 2 SO 4 NaCl and KSCN as 1.2:1.1:0.01 molar ratio (1000 mL H) 2 O、54.35mL H 2 SO 4 29.25g NaCl, 0.97g KSCN). And (3) testing the corrosion resistance of the alloy by using a cyclic voltammetry potentiodynamic polarization curve and a double-ring potentiodynamic reactivation method (DLEPR). The electrochemical parameters for the potentiometric polarization curve fitting are collated in Table 2.
TABLE 2
As can be seen from Table 2, the pitting potential E is within the range of 0.80 to 1.50KJ/mm in heat input b More than or equal to 0.01V. Therefore, the pitting potential E is between 0.80 and 1.50KJ/mm b When the voltage is more than or equal to 0.01V, the welding heat affected zone has high pitting corrosion resistance. FIG. 3 shows the zeta potential polarization curves of samples with different heat input and solid solution states of 0.848KJ/mm,1.468KJ/mm,1.895KJ/mm,2.542KJ/mm and 2.935KJ/mm after solid solution at 1050 ℃. FIG. 4 shows the DLEPR test curves of five different heat input and solid solution state samples of 0.848KJ/mm,1.468KJ/mm,1.895KJ/mm,2.542KJ/mm,2.935KJ/mm after 1050 ℃ solid solution, and FIG. 6 shows the intercrystalline corrosion sensitivity values (Ra) of five different heat input samples of 0.848KJ/mm,1.468KJ/mm,1.895KJ/mm,2.542KJ/mm,2.935KJ/mm after 1050 ℃ solid solution, corresponding to the cooling t 8/5 The cooling time is 10s,30s,50s,90s and 120s, it can be seen that Ra shows the trend of increasing and then reducing fluctuation, the solid solution temperature is treated by solid solution at 1030-1070 ℃, the heat input is 0.80-2.08KJ/mm, and Ra shows that<The weld heat affected zone at 27.00% has high intergranular corrosion resistance, and SEM intergranular corrosion morphology with heat input of 1.895KJ/mm is shown in FIG. 8, wherein delta represents a ferrite phase and gamma represents an austenite phase, and it can be seen that corrosion is mainly concentrated at ferrite and austenite grain boundaries and is partially concentrated inside ferrite grains.
Example 3
The stainless steel casting blank comprises the following chemical components in percentage by mass: c:0.008%, si:0.04%, mn:10.50%, cr:22.05%, ni:0.02%, mo:1.01%, cu:0.25%, N:0.23%, P:0.01%, S:0.01%, and the balance of Fe and inevitable impurities.
(1) Adopting a stainless steel cast blank refined by a 50kg vacuum smelting furnace, pre-forging the stainless steel cast blank, starting forging at 1100 ℃, wherein the forging ratio is 4, the finish forging temperature is 1000 ℃, and cooling after forging; then, carrying out pre-rolling treatment, setting the initial rolling temperature to be 1120 ℃, setting the final rolling temperature to be 970 ℃, and carrying out water quenching to obtain a plate;
(2) Carrying out solution treatment on the plate obtained in the step (1) under the conditions that: at 960-1000 ℃ for 60min, and then carrying out normal temperature water cooling;
(3) And (3) processing the water-cooled plate obtained in the step (2) into a size of 10.5mm multiplied by 60mm, performing welding thermal cycle treatment with the heat input of 0.848KJ/mm, heating to 1345 ℃ at the heating rate of 200 ℃/s, and preserving heat for 1s to obtain the high-Mn ultralow-Ni duplex stainless steel sample. Preparing a pitting solution and an intercrystalline corrosion solution, wherein the pitting solution is 3.5wt% of NaCl solution (1000 mLH) 2 O and 35g NaCl), the intergranular corrosion solution is H 2 SO 4 NaCl and KSCN as 1.2:1.1:0.01 molar ratio (1000 mL H) 2 O、54.35mL H 2 SO 4 29.25g NaCl, 0.97g KSCN) were added to the steel. The results are shown in Table 3.
TABLE 3
As is clear from Table 3, when the solid solution temperature was 980 ℃ and the heat input was 0.848KJ/mm, the pitting potential E was b More than or equal to 0.179V. Therefore, the pitting potential E is 0.848KJ/mm at the solid solution heat input of 980 DEG C b When the temperature is more than or equal to 0.179V, the welding heat affected zone has high pitting corrosion resistance.
Example 4
The stainless steel casting blank comprises the following chemical components in percentage by mass: c:0.012%, si:0.02%, mn:11.10%, cr:21.06%, ni:0.04%, mo:0.72%, cu:0.36%, N:0.18%, P:0.01%, S:0.01%, and the balance of Fe and inevitable impurities.
(1) Adopting a stainless steel cast blank smelted by a 50kg vacuum smelting furnace, and performing pre-forging treatment on the stainless steel cast blank under the conditions that: starting forging at 1200 ℃, wherein the forging ratio is 3, the finish forging temperature is 980 ℃, and cooling after forging; then carrying out pre-rolling treatment under the conditions as follows: setting the initial rolling temperature to 1180 ℃, setting the final rolling temperature to 980 ℃, and performing water quenching to obtain a plate;
(2) Carrying out solution treatment on the plate obtained in the step (1), wherein the conditions are as follows: 1030-1070 ℃, and 60min, and then carrying out normal temperature water cooling;
(3) And (3) processing the water-cooled plate obtained in the step (2) into a size of 10.5mm multiplied by 60mm, performing welding heat cycle treatment, wherein the heat input is 0.848KJ/mm, heating to 1345 ℃ at the heating rate of 200 ℃/s, and preserving heat for 1s to obtain the high-Mn ultralow-Ni dual-phase stainless steel sample. Preparing a pitting solution and an intercrystalline corrosion solution, wherein the pitting solution is a 3.5wt% NaCl solution (1000 mLH) 2 O and 35g NaCl), and the intergranular corrosion solution is H 2 SO 4 NaCl and KSCN as 1.2:1.1:0.01 molar ratio (1000 mL H) 2 O、54.35mL H 2 SO 4 29.25g NaCl and 0.97g KSCN) to test the corrosion resistance. The results are shown in Table 4.
TABLE 4
As is clear from Table 4, when the solid solution temperature was 1050 ℃ and the heat input was 0.848KJ/mm, the pitting potential E was b More than or equal to 0.01V. Therefore, the pitting potential E is set at 1050 ℃ at a solid solution heat input of 0.848KJ/mm b When the voltage is more than or equal to 0.01V, the welding heat affected zone has high pitting corrosion resistance.
The above-described embodiments are merely illustrative of the preferred embodiments of the present invention, and do not limit the scope of the present invention, and various modifications and improvements of the technical solutions of the present invention can be made by those skilled in the art without departing from the spirit of the present invention, and the technical solutions of the present invention are within the scope of the present invention defined by the claims.
Claims (6)
1. A hot working method for a high corrosion resistance welding heat affected zone of stainless steel is characterized by comprising the following steps:
(1) Pre-forging the stainless steel casting blank, then pre-rolling, and performing water quenching to obtain a plate;
(2) Carrying out solution treatment on the plate obtained in the step (1), and then carrying out water cooling at normal temperature;
(3) Carrying out welding thermal cycle treatment on the plate subjected to water cooling in the step (2);
the stainless steel casting blank comprises the following chemical components in percentage by mass: c:0.008 to 0.012%, si:0.02-0.04%, mn:10.50-11.10%, cr:21.06-22.05%, ni:0.02 to 0.04%, mo:0.72-1.01%, cu:0.25-0.36%, N:0.18-0.23%, P: less than or equal to 0.01 percent, S: less than or equal to 0.01 percent, and the balance of Fe and inevitable impurities;
the welding heat cycle treatment conditions are as follows: the heat input range is 0.80-3.08KJ/mm, the temperature is raised to 1345 ℃ at the heating rate of 200 ℃/s, and the temperature is kept for 1s.
2. The high corrosion resistance weld heat affected zone hot working method of a stainless steel according to claim 1, wherein in step (1), the conditions of the pre-forging process are: starting forging at 1100-1200 deg.C, forging ratio of 3-4, and final forging temperature of 980 deg.C or above, and cooling.
3. The high corrosion resistance welding heat affected zone hot working method of a stainless steel according to claim 1, wherein in step (1), the conditions of the pre-rolling treatment are as follows: the initial rolling temperature is set to be 1120-1180 ℃, and the final rolling temperature is higher than 960 ℃.
4. The method for hot working a high corrosion resistance welding heat affected zone of stainless steel according to claim 1, wherein in step (2), the solution treatment is performed in a box type resistance furnace under the conditions of: 960-1070 deg.C, 30-60min.
5. The method for hot working a weld heat affected zone with high corrosion resistance of stainless steel as claimed in claim 4, wherein the solution treatment temperature is 960-1000 ℃ and the heat input range is 0.80-1.50KJ/mm; the heat input range is 0.80-2.08KJ/mm when the temperature of the solution treatment is 1030-1070 ℃.
6. A high Mn ultra-low Ni duplex stainless steel processed by the high corrosion resistance weld heat affected zone hot working method of the stainless steel defined in any one of claims 1 to 5.
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