CN115261580A - Stainless steel surface grain boundary engineering treatment method based on cutting processing and product - Google Patents
Stainless steel surface grain boundary engineering treatment method based on cutting processing and product Download PDFInfo
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- 238000005520 cutting process Methods 0.000 title claims abstract description 31
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- 230000008569 process Effects 0.000 claims abstract description 20
- 239000002344 surface layer Substances 0.000 claims abstract description 12
- 238000001816 cooling Methods 0.000 claims description 16
- 238000003801 milling Methods 0.000 claims description 13
- 238000007514 turning Methods 0.000 claims description 12
- 229910000963 austenitic stainless steel Inorganic materials 0.000 claims description 7
- 238000010438 heat treatment Methods 0.000 claims description 7
- 239000006104 solid solution Substances 0.000 claims description 5
- 238000005516 engineering process Methods 0.000 claims description 3
- 238000003672 processing method Methods 0.000 claims description 2
- 239000000463 material Substances 0.000 abstract description 38
- 230000007797 corrosion Effects 0.000 abstract description 20
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
- C21D7/10—Modifying the physical properties of iron or steel by deformation by cold working of the whole cross-section, e.g. of concrete reinforcing bars
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D11/00—Process control or regulation for heat treatments
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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Abstract
The invention belongs to the technical field related to metal surface treatment processes, and discloses a stainless steel surface grain boundary engineering treatment method based on cutting processing and a product. The method comprises the following steps: the surface of the stainless steel to be treated is subjected to cutting processing, simultaneously, the surface layer of the stainless steel generates plastic deformation required by surface grain boundary engineering, and the stainless steel is cooled after annealing, so that a grain boundary engineering layer with a certain thickness is formed on the surface layer close to the stainless steel. The invention also discloses a product prepared by the method. The surface grain boundary engineering treatment process provided by the invention can form a grain boundary engineering layer with good uniformity, high proportion and low sigma CSL grain boundary proportion (more than or equal to 75%) and adjustable thickness on the surface of the stainless steel material, has wide application range and simple steps, can be applied to but not limited to surface treatment of various stainless steel complex component curved surfaces, and can obviously improve the surface corrosion resistance of the metal material.
Description
Technical Field
The invention belongs to the technical field related to metal surface treatment processes, and particularly relates to a stainless steel surface grain boundary engineering treatment method and a product based on material surface deformation formed by cutting.
Background
Watanabe firstly puts forward a concept of 'grain boundary design and control' in the eighties of the last century, then gradually develops a 'grain boundary engineering' (GBE) technology, and the grain boundary engineering mainly regulates and controls the grain boundary characteristic distribution of a material through a certain thermomechanical treatment process, improves the proportion of low sigma coincident position lattice (CSL) (1 sigma is less than or equal to 29) grain boundaries in a microstructure of the material, destroys the connectivity of a random large-angle grain boundary network, and finally achieves the purpose of improving the material performance.
The traditional deformation heat treatment process is to carry out deformation heat treatment on the whole metal material, such as the combination of common cold rolling and heat treatment, but the method is only suitable for thinner plates and cannot carry out deformation treatment on components with excessive thickness or complex shapes. Researchers at home and abroad explore the surface grain boundary engineering treatment on the surface of the stainless steel material by combining the surface deformation treatment technology such as ultrasonic impact, laser shot blasting and the like with the heat treatment, but the surface layer deformation generation method has the disadvantages of complex realization process, low processing efficiency and high cost.
CN114214494A discloses a surface grain boundary engineering treatment method for corrosion resistance of stainless steel, wherein it discloses that surface spinning treatment, annealing treatment and cooling are sequentially performed on solid-solution stainless steel, and a grain boundary engineering layer is formed on the surface of the stainless steel. The method is only suitable for surface treatment of various rotating bodies on special equipment, and is difficult to be applied to surface grain boundary engineering treatment of complex curved surface and irregular shape members. In addition, the surface treatment method generates plastic deformation on the whole section, and the thickness range of the formed grain boundary engineering layer is difficult to regulate and control in a simple and controllable mode.
Therefore, a surface treatment process method which can be completed on general equipment, is widely suitable for various complex surfaces and can effectively improve the intergranular corrosion resistance of the surface of the stainless steel material is needed.
Disclosure of Invention
Aiming at the defects or improvement requirements of the prior art, the invention provides a stainless steel surface grain boundary engineering treatment method based on cutting processing and a product thereof, and solves the problems of difficult implementation, complex process, low processing efficiency and high cost of a complex-shaped member in a treatment process for improving the intergranular corrosion resistance of the stainless steel surface.
In order to achieve the above object, according to one aspect of the present invention, there is provided a method for processing stainless steel surface grain boundary engineering based on cutting, the method comprising the steps of:
and carrying out surface cutting treatment on the stainless steel to be treated to enable the surface layer of the stainless steel to generate plastic deformation, and cooling after annealing so as to form a grain boundary engineering layer with a certain thickness on the surface of the stainless steel.
Further preferably, the magnitude of said plastic deformation is controlled by the tool geometry and the machining process parameters.
Further preferably, the thickness control range of the surface grain boundary engineering layer is as follows: 0-3 mm.
Further preferably, the lattice grain boundary proportion of the low sigma coincidence position of the surface grain boundary engineering layer after heat treatment is not less than 75%, and the residual stress generated by cutting machining is eliminated.
Further preferably, the surface treatment is milling or turning.
Further preferably, the annealing temperature is 850-1000 ℃, and the heat preservation time is 24-120 h.
Further preferably, the cooling rate is not less than 200 ℃/s.
Further preferably, the stainless steel to be treated is austenitic stainless steel in a solid solution state.
According to another aspect of the invention, there is provided a product obtained by the above-described treatment method.
Generally, compared with the prior art, the technical scheme conceived by the invention has the following beneficial effects:
1. according to the invention, milling or turning is adopted, surface layer materials are removed in the process of processing the stainless steel parts, and meanwhile, certain plastic deformation is introduced into the surface layer area, so that driving force is provided for recrystallization nucleation and strain-induced grain boundary migration in the surface area in the next annealing treatment process, a grain boundary engineering layer (GBE layer) with uniform thickness is formed on the surface layer of the stainless steel materials, and the thickness of the GBE layer can be simply and effectively regulated and controlled by controlling the annealing treatment time; by controlling the annealing temperature, the grain size in the workpiece can be prevented from being recrystallized and grown, so that the integral mechanical property of the workpiece is not obviously changed;
2. the surface deformation process adopted by the invention is a common mechanical processing method such as milling or turning, which is the most economical and rapid mode for realizing the geometric requirement of the appearance of the curved surface part, has high processing efficiency and low cost, and can process simple plane plates and rotating bodies and components with any complex curved surface shape compared with the traditional cold rolling processing process and surface spinning processing process;
3. the surface layer deformation process method adopted by the invention can be completed on a numerical control machine tool, can be applied to surfaces with complex shapes and irregular shapes, and realizes plastic deformation treatment on different parts on a curved surface by controlling the motion track and cutting amount of a processing cutter on the surface of a workpiece through the numerical control machine tool; 4. the process method can be applied to the cutting process of the complex curved surface component, and the embodiment result shows that the method can form a grain boundary engineering layer with adjustable thickness range on the surface of the stainless steel material, the low sigma CSL grain boundary proportion of the surface grain boundary layer is not less than 75 percent, the residual stress introduced by cutting is eliminated, and the corrosion resistance is excellent.
Drawings
FIG. 1 is a metallographic structure diagram of a longitudinal section of a grain boundary engineered layer (GBE layer) on a surface of a stainless steel material obtained in example 1;
FIG. 2 is a metallographic structure diagram of a longitudinal section of a GBE layer on the surface of a stainless steel material obtained in example 2;
FIG. 3 is a metallographic structure diagram of a longitudinal section of a GBE layer on the surface of a stainless steel material obtained in example 3;
FIG. 4 is a different type of grain boundary distribution pattern of the GBE layer at the longitudinal section of the surface of the stainless steel material obtained in example 3;
FIG. 5 is a metallographic structure diagram of a longitudinal section of a GBE layer on the surface of a stainless steel material obtained in example 4;
FIG. 6 is a graph showing different types of grain boundary distributions of a GBE layer on a surface of a stainless steel material obtained in example 4;
FIG. 7 is a statistical comparison of the specific grain boundary ratios of the stainless steel substrate and GBE layer obtained in examples 3 and 4;
FIG. 8 shows the intergranular corrosion morphology of the GBE layer in a longitudinal section of the stainless steel obtained in example 4;
FIG. 9 shows the intergranular corrosion morphology of the GBE layer and the transition region of the substrate in the longitudinal section of the stainless steel obtained in example 4;
FIG. 10 shows the intergranular corrosion morphology of a longitudinal section of a substrate region of stainless steel obtained in example 4;
FIG. 11 is a graph showing different types of grain boundary distribution profiles of a GBE layer on a surface of a stainless steel material obtained in example 5.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the present invention is further described in detail below with reference to the accompanying drawings and embodiments. It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention. In addition, the technical features involved in the embodiments of the present invention described below may be combined with each other as long as they do not conflict with each other.
The invention provides a stainless steel surface grain boundary engineering method based on cutting processing, which comprises the following steps: milling or turning the surface of the stainless steel material, preserving the heat for 24-120 h at 850-1000 ℃, and then rapidly cooling to room temperature. The surface treatment process provided by the invention can form a grain boundary engineering layer with good uniformity, high proportion and low sigma CSL grain boundary proportion (more than or equal to 75 percent) and adjustable range on the surface of the stainless steel material, has wide application range and simple steps, can be applied to but not limited to surface treatment of various stainless steel complex member curved surfaces, and can obviously improve the surface corrosion resistance of the metal material.
In the invention, the milling or turning processing mode is preferably carried out at room temperature, the milling or turning mode is preferably rough milling or rough turning, the processing mode can obtain necessary geometric dimension and shape aiming at various stainless steel complex component curved surfaces, and simultaneously large plastic deformation is introduced in the stainless steel surface layer area, thereby providing driving force for optimizing the grain boundary characteristic distribution by surface recrystallization nucleation growth and strain induced grain boundary migration in the next heat treatment process.
In the invention, the annealing treatment is carried out in air, the grain boundary engineering layer represented in the example is the surface layer of the material after removing the scale, and the thickness of the grain boundary engineering layer can be further increased when the annealing treatment is carried out under the protective gas such as nitrogen.
In the invention, the temperature range of the annealing treatment is 850-1000 ℃, and the heat preservation time of the annealing treatment is 24-120 h. In the invention, the selected temperature range is close to and lower than the recrystallization nucleation temperature of the untreated stainless steel substrate, the recrystallization nucleation growth, the strain-induced grain boundary migration and other behaviors can occur in the deformation region of the cutting surface of the stainless steel, and meanwhile, the temperature range does not cause the growth of the grain size in the material and does not influence the overall mechanical property of the material. The heat preservation time of the annealing treatment can simply and effectively regulate and control the thickness of the surface grain boundary engineering layer and eliminate the residual stress introduced by cutting.
In the present invention, the cooling rate is preferably not less than 200 ℃/s. The present invention is advantageous in suppressing precipitation of the second phase and preventing the stainless steel from suffering intergranular sensitization by controlling the cooling rate within the above range. The cooling method of the present invention has no special requirement, and the method is well known to those skilled in the art, such as water cooling.
The present invention will be further illustrated with reference to specific examples.
Example 1
The 304 austenitic stainless steel is selected, and the element compositions of the materials are shown in the following table:
| element(s) | C | Si | P | Mn | Cr | Ni | Fe |
| Mass percent (%) | 0.0389 | 0.446 | 0.0225 | 0.675 | 19.15 | 8.2 | balance |
Carrying out surface milling treatment on a solid-solution 304 stainless steel plate at room temperature, carrying out rough milling treatment on milling processing through a numerical control milling machine, wherein the feed rate is 150mm/min, the rotating speed of a main shaft is 600r/min, and the milling depth is 0.5mm; cutting the cut stainless steel plate into square blocks of 15mm multiplied by 9.5mm, and annealing at 900 ℃ for 24h; and cooling the annealed stainless steel plate to room temperature at the speed of 200 ℃/s.
Example 2
Austenitic stainless steel was selected in the same manner as in example 1
The surface treatment method is the same as that of the example 1, the stainless steel plate after the surface cutting treatment is cut into square blocks of 15mm multiplied by 9.5mm, and the annealing temperature is 900 ℃, and the heat preservation time is 48h; and cooling the annealed stainless steel plate to room temperature at the speed of 200 ℃/s.
Example 3
Austenitic stainless steel was selected in the same manner as in example 1
The surface treatment method is the same as that of the example 1, the stainless steel plate after the surface cutting treatment is cut into square blocks of 15mm multiplied by 9.5mm, and the annealing temperature is 900 ℃, and the heat preservation time is 72 hours; and cooling the annealed stainless steel plate to room temperature at the speed of 200 ℃/s.
Example 4
Austenitic stainless steel was selected in the same manner as in example 1
The surface treatment mode is the same as that of the embodiment 1, the stainless steel plate after the surface cutting treatment is cut into square blocks of 15mm multiplied by 9.5mm, the annealing temperature is 900 ℃, and the heat preservation time is 96h; and cooling the annealed stainless steel plate to room temperature at the speed of 200 ℃/s.
Example 5
Austenitic stainless steel was selected in the same manner as in example 1
Carrying out surface turning treatment on a solid-solution 304 stainless steel plate at room temperature, carrying out turning treatment on a bar with the diameter of 40mm by a lathe, wherein the feed rate is 0.1mm/r, the rotating speed of a main shaft is 600r/min, the turning depth is 0.6mm, cutting the turned stainless steel bar into a cylinder with the thickness of 20mm, and carrying out annealing treatment, wherein the annealing temperature is 900 ℃, and the heat preservation time is 96 hours; and cooling the annealed stainless steel plate to room temperature at the speed of 200 ℃/s.
And (3) electrolytic corrosion is carried out in 10% oxalic acid solution to obtain metallographic structure diagrams of longitudinal sections in examples 1-4, and an Olympus DSX 510 ultra-depth-of-field microscope is adopted to represent the thickness of the surface grain boundary engineering layer. A GeminiSEM300 field emission scanning electron microscope is adopted to represent the grain boundary characteristic distribution and the corrosion morphology of the longitudinal section in the embodiments 3-5, and OIM software is used to analyze the low sigma CSL grain boundary proportion in the surface grain boundary engineering layer. The intergranular corrosion performance of the material of example 5 was evaluated according to the 10% oxalic acid etching test recommended in GB/T4334-2020, and the stainless steel material obtained in the example was exposed to heat at 650 ℃ for 2 hours and sensitized prior to the 10% oxalic acid etching test.
FIG. 1 is a metallographic structure diagram of a longitudinal section of a GBE layer on the surface of a stainless steel material obtained in example 1, and it is obvious that after annealing treatment for 24 hours, a GBE protective layer is formed within a range of 0-570 microns, grains of the GBE protective layer are obviously grown and contain a large number of annealed twin crystals, and the size of the grains in the stainless steel material is basically not changed.
FIG. 2 is a metallographic structure diagram of a longitudinal section of a GBE layer on the surface of a stainless steel material obtained in example 2, and it is obvious that after annealing treatment for 48 hours, a GBE protective layer is formed within a range of 0-640 micrometers, grains of the GBE protective layer are obviously grown and contain a large number of annealed twin crystals, and the size of the grains in the stainless steel material is basically not changed.
Fig. 3 is a metallographic structure diagram of a longitudinal section of a GBE layer on a surface of a stainless steel material obtained in example 3, fig. 4 is a distribution diagram of different types of grain boundaries of the longitudinal section of the GBE layer on the surface of the stainless steel material obtained in example 3, a black solid line is a random large-angle grain boundary, a gray solid line is a low sigma coincident position lattice (∑ CSL) grain boundary, and it is obvious that after 72 hours of annealing treatment, a GBE protective layer is formed in a range of 0 to 1250 micrometers, grains of the GBE protective layer grow significantly and include a large amount of low sigma CSL grain boundaries, a random grain boundary network is broken, and the size of grains inside the stainless steel material is not changed basically.
FIG. 5 is a metallographic structure diagram of a longitudinal section of a GBE layer on the surface of a stainless steel material obtained in example 4, and FIG. 6 is a distribution diagram of different types of grain boundaries of the longitudinal section of the GBE layer on the surface of the stainless steel material obtained in example 4, as is apparent from the diagram, a GBE protective layer is formed within a range of 0 to 2000 μm, grains of the GBE protective layer are obviously grown, a large number of low-sigma CSL grain boundaries are included, a random grain boundary network is broken, and the size of grains inside the stainless steel material is basically unchanged.
As can be seen from fig. 1, 2, 3 and 5, the thickness of the surface GBE protective layer increases with the increase of the annealing time, which indicates that the thickness range of the surface GBE layer can be easily controlled by the annealing time, and the crystal grains of the internal matrix of the stainless steel workpiece treated by the surface treatment scheme of the present invention do not grow, and the overall mechanical properties of the workpiece are not affected.
FIG. 7 is a statistical comparison of the specific grain boundary ratios of the stainless steel substrate and GBE layer obtained in examples 3 and 4, and it can be seen from the figure that the grain boundary ratio of low sigma CSL in the GBE protective layer in example 3 reaches 81.9%, and the grain boundary ratio of low sigma CSL in the GBE protective layer in example 4 reaches 75.8%, which are both significantly higher than 54.5% of the substrate, indicating that the GBE protective layer has good corrosion resistance.
FIG. 8 shows the intergranular corrosion morphology of the longitudinal section of the stainless steel obtained in example 4, FIG. 9 shows the intergranular corrosion morphology of the GBE layer and the transition region of the substrate obtained in example 4, and FIG. 10 shows the intergranular corrosion morphology of the substrate region obtained in the longitudinal section of the stainless steel obtained in example 4. From fig. 8 to fig. 11, it is apparent that the density of intergranular corrosion channels in the GBE layer region is much less than that in the interior of the base material, and the corrosion network in the surface layer region is broken by the low- Σ CSL grain boundaries, indicating that the corrosion resistance of the GBE layer on the surface of the material is significantly improved.
FIG. 11 is a distribution diagram of different types of grain boundaries of the GBE layer in the longitudinal section of the stainless steel material obtained in example 5, and it is apparent from the diagram that after turning, annealing and cooling, a GBE protective layer is formed in the range of 0-1600 μm, a random grain boundary network is broken, the proportion of low sigma CSL grain boundaries reaches 88%, which is significantly higher than 54.5% of a matrix, and the GBE protective layer has excellent corrosion resistance.
It will be understood by those skilled in the art that the foregoing is only an exemplary embodiment of the present invention, and is not intended to limit the invention to the particular forms disclosed, since various modifications, substitutions and improvements within the spirit and scope of the invention are possible and within the scope of the appended claims.
Claims (9)
1. A stainless steel surface grain boundary engineering treatment method based on cutting processing is characterized by comprising the following steps:
and carrying out surface cutting processing on the stainless steel to be processed to enable the surface layer of the stainless steel to generate plastic deformation, and cooling after annealing so as to form a grain boundary engineering layer on the surface of the stainless steel.
2. The method for processing the stainless steel surface grain boundary engineering based on the cutting processing as claimed in claim 1, wherein the magnitude of the plastic deformation is controlled by the geometrical shape of a cutter and the parameters of the cutting processing technology.
3. The stainless steel surface grain boundary engineering treatment method based on cutting processing as claimed in claim 1 or 2, characterized in that the thickness regulation range of the surface grain boundary engineering layer is as follows: 0-3 mm.
4. The method for processing the stainless steel surface grain boundary engineering based on the cutting processing as set forth in claim 1 or 2, characterized in that the proportion of the lattice grain boundary at the low sigma superposition position of the surface grain boundary engineering layer after the heat treatment is not less than 75%.
5. The method for processing the stainless steel surface grain boundary engineering based on the cutting processing as claimed in claim 1 or 2, wherein in the process of preparing the surface grain boundary engineering, the surface cutting processing method is milling or turning processing.
6. The method for the grain boundary engineering treatment of the stainless steel surface based on the cutting processing as claimed in claim 1 or 2, characterized in that the annealing temperature is 850-1000 ℃ and the holding time is 24-120 hours.
7. The method for the grain boundary engineering treatment of the stainless steel surface based on the cutting processing as claimed in claim 1 or 2, wherein the cooling rate is not lower than 200 ℃/s.
8. The method for processing the stainless steel surface grain boundary engineering based on the cutting processing as claimed in claim 1 or 2, characterized in that the stainless steel to be processed is austenitic stainless steel in a solid solution state.
9. A product obtained by the treatment method of any one of claims 1 to 8.
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|---|---|---|---|---|
| CN101323900A (en) * | 2007-06-15 | 2008-12-17 | 中国科学院金属研究所 | High speed processing method for realizing superfine crystal grain structure on metallic material surface |
| CN104278138A (en) * | 2014-09-03 | 2015-01-14 | 上海大学 | Grain boundary engineering technique for enhancing corrosion resistance of 304 stainless steel |
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| CN108842044A (en) * | 2018-07-23 | 2018-11-20 | 东北大学 | A method of improving low ∑ value special grain boundary ratio in AL6XN stainless steel |
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