CN114774656A - Process for regulating and controlling grain boundary characteristic distribution of hub material by utilizing reverse rolling - Google Patents
Process for regulating and controlling grain boundary characteristic distribution of hub material by utilizing reverse rolling Download PDFInfo
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- CN114774656A CN114774656A CN202210410924.3A CN202210410924A CN114774656A CN 114774656 A CN114774656 A CN 114774656A CN 202210410924 A CN202210410924 A CN 202210410924A CN 114774656 A CN114774656 A CN 114774656A
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- 238000005096 rolling process Methods 0.000 title claims abstract description 53
- 239000000463 material Substances 0.000 title claims abstract description 48
- 230000002441 reversible effect Effects 0.000 title claims abstract description 36
- 238000000034 method Methods 0.000 title claims abstract description 29
- 230000008569 process Effects 0.000 title claims abstract description 23
- 238000009826 distribution Methods 0.000 title claims abstract description 21
- 230000001276 controlling effect Effects 0.000 title claims abstract description 17
- 230000001105 regulatory effect Effects 0.000 title claims abstract description 13
- 238000010438 heat treatment Methods 0.000 claims abstract description 26
- 229910000963 austenitic stainless steel Inorganic materials 0.000 claims abstract description 18
- 238000010791 quenching Methods 0.000 claims abstract description 16
- 230000000171 quenching effect Effects 0.000 claims abstract description 16
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 16
- 238000000137 annealing Methods 0.000 claims description 23
- 206010070834 Sensitisation Diseases 0.000 claims description 11
- 230000008313 sensitization Effects 0.000 claims description 11
- 238000004321 preservation Methods 0.000 claims description 7
- 229910001220 stainless steel Inorganic materials 0.000 claims description 4
- 239000010935 stainless steel Substances 0.000 claims description 4
- 238000005260 corrosion Methods 0.000 abstract description 19
- 230000007797 corrosion Effects 0.000 abstract description 18
- 238000000265 homogenisation Methods 0.000 abstract description 2
- 229910045601 alloy Inorganic materials 0.000 abstract 2
- 239000000956 alloy Substances 0.000 abstract 2
- 239000005457 ice water Substances 0.000 abstract 1
- 239000000203 mixture Substances 0.000 abstract 1
- 230000007420 reactivation Effects 0.000 description 12
- 238000012360 testing method Methods 0.000 description 9
- 230000000930 thermomechanical effect Effects 0.000 description 9
- 239000000243 solution Substances 0.000 description 6
- 230000001235 sensitizing effect Effects 0.000 description 5
- 238000006056 electrooxidation reaction Methods 0.000 description 4
- ZNNZYHKDIALBAK-UHFFFAOYSA-M potassium thiocyanate Chemical compound [K+].[S-]C#N ZNNZYHKDIALBAK-UHFFFAOYSA-M 0.000 description 4
- 230000008859 change Effects 0.000 description 3
- 239000003795 chemical substances by application Substances 0.000 description 3
- 239000003822 epoxy resin Substances 0.000 description 3
- 238000002474 experimental method Methods 0.000 description 3
- 229920000647 polyepoxide Polymers 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000005457 optimization Methods 0.000 description 2
- 239000003208 petroleum Substances 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 230000002829 reductive effect Effects 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000002003 electron diffraction Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000005324 grain boundary diffusion Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
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- 238000012986 modification Methods 0.000 description 1
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- 238000001556 precipitation Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
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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
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- 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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
-
- 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
- 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
-
- 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
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
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- Physics & Mathematics (AREA)
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Abstract
The invention discloses a process for regulating and controlling the grain boundary characteristic distribution of a hub material by utilizing reverse rolling, which comprises the steps of firstly carrying out solution treatment on an austenitic stainless steel alloy, then carrying out reverse rolling deformation treatment on the alloy after the solution treatment, and controlling the total deformation amount of the reverse rolling to be 3-20% and the primary rolling deformation amount to be 1.5-10%. And finally, placing the reversely rolled material in a heat treatment furnace, preserving heat for 5-60 min at 1000-1150 ℃, and quickly putting the sample into an ice-water mixture for water quenching treatment after heating. The method can prepare the austenitic stainless steel with excellent intergranular corrosion resistance, and when the same equivalent strain is introduced in the reverse rolling deformation mode and the unidirectional rolling deformation mode, the residual stress in the reverse rolling deformation is lower, namely the introduction of larger deformation and the homogenization of deformation can be realized.
Description
Technical Field
The invention relates to the field of metal material deformation and heat treatment processes, in particular to a process for regulating and controlling the grain boundary characteristic distribution of a hub material by utilizing reverse rolling.
Background
Austenitic stainless steel has excellent mechanical properties and good corrosion resistance under conventional conditions, and is widely applied to industries such as petroleum, chemical industry, power stations and the like. However, leakage accidents caused by intergranular corrosion and intergranular stress corrosion cracking often occur during the use of the austenitic stainless steel, which causes great economic loss to enterprises and seriously endangers production and personal safety. Therefore, how to improve the intergranular corrosion resistance and the intergranular stress corrosion resistance of the austenitic stainless steel has important significance for prolonging the service life of stainless steel components and ensuring the safe operation of petroleum, chemical equipment and power stations.
Grain boundaries, an important structural feature of polycrystalline materials, have a significant impact on the properties of the material. Many phenomena (grain boundary diffusion, precipitation, corrosion) are found to be closely related to the structure of grain boundaries, mainly due to the energy and structure differences of different grain boundaries. Based on the CSL model, grain boundaries can be divided into low Σ CSL grain boundaries (Σ ≦ 29) (also referred to as special grain boundaries) and Random Boundary (RB) (Σ > 29). Numerous studies have shown that low sigma CSL grain boundaries exhibit strong inhibitory effects on slip, fracture, corrosion and stress corrosion cracking, sensitization and solute segregation (equilibrium and non-equilibrium), some even completely immune. Random grain boundaries, due to their high energy and high mobility, often serve as nuclei for crack growth and as channels for propagation, leading to the occurrence of intergranular corrosion cracks and intergranular stress corrosion cracks. Therefore, controlling and optimizing the distribution of grain boundary characteristics inside the material becomes an important means for improving and enhancing the material performance. Based on the understanding that different grain boundary structures have different properties, Watanabe first proposed the concept of "grain boundary control and design" in 1984. Subsequently, this concept was developed as "grain boundary engineering". The grain boundary engineering is to regulate and control the grain boundary characteristic distribution of the material through a certain thermomechanical treatment process, and realize the improvement of the low sigma CSL grain boundary proportion and the interruption of the network connectivity of a high-energy random grain boundary, thereby achieving the purpose of controlling and optimizing the material performance. In the past three decades, grain boundary engineering has been widely used to improve the grain boundary related properties of materials.
The annealing twin crystal-based grain boundary engineering process mainly comprises two steps of deformation and heat treatment, and is divided into two main categories of single-step deformation heat treatment and repeated deformation heat treatment, and the process can be divided into the following categories according to the deformation and the annealing conditions: the method comprises four steps of single-step recrystallization annealing, single-step strain annealing, repeated recrystallization annealing and repeated strain annealing, wherein the strain is almost introduced by rolling deformation. For unidirectional rolling deformation, the strain of the plate in the thickness direction after the rolling deformation treatment is not uniformly distributed, the strain from the surface to the center of the plate thickness is in a decreasing trend, an obvious texture is generated, and the anisotropy of the plate is greatly improved. For reverse rolling deformation, uniform deformation of the material can be realized, the anisotropy of the plate is reduced, the forming rate of the plate is improved, and uniform microstructure and performance can be obtained in the subsequent annealing process. At present, the grain boundary engineering is mostly realized by using unidirectional rolling deformation or unidirectional stretching/compressing deformation combined with subsequent annealing heat treatment to optimize the grain boundary characteristic distribution of materials, but no report of controlling the grain boundary characteristic distribution of austenitic stainless steel by using reverse rolling deformation combined with annealing treatment so as to improve the intergranular corrosion resistance of austenitic stainless steel exists; therefore, the process for regulating and controlling the grain boundary characteristic distribution of the hub material by utilizing reverse rolling is provided.
Disclosure of Invention
The invention aims to solve the problems of the prior art by providing a process for regulating and controlling the grain boundary characteristic distribution of a hub material by reverse rolling.
In order to achieve the purpose, the invention provides the following technical scheme: a process for regulating and controlling the grain boundary characteristic distribution of a hub material by utilizing reverse rolling comprises the following specific steps:
s1: firstly, carrying out solid solution treatment on an austenitic stainless steel plate and then carrying out water quenching;
s2: carrying out reverse rolling deformation treatment on the stainless steel plate by using a four-high mill;
s3: and (3) placing the material subjected to the reverse rolling deformation treatment in a heat treatment furnace, adjusting the heat treatment temperature and time, carrying out annealing heat treatment on the material, and taking out the material after heat preservation for water quenching.
S4: and (4) carrying out sensitization treatment on the processed material, and then carrying out water quenching.
As a preferable technical scheme of the invention, the solution treatment in S1 is water quenching after the austenitic stainless steel is subjected to heat preservation at 1050 ℃ for 30 min.
As a preferable technical scheme of the invention, the total deformation of the reverse rolling in the S2 is 3% -20%, and the single rolling deformation is 1.5% -20%.
As a preferable technical scheme of the invention, the heat treatment temperature in the S3 is 1000-1150 ℃, and the heat treatment time is 5-60 min.
In a preferred embodiment of the present invention, the sensitization temperature in S4 is 650 ℃ and the sensitization time is 2 hours.
The invention has the beneficial effects that: the method can prepare the austenitic stainless steel with excellent intergranular corrosion resistance, and when the same equivalent strain is introduced in the reverse rolling deformation mode and the unidirectional rolling deformation mode, the residual stress in the reverse rolling deformation is lower, namely the introduction of larger deformation and the homogenization of deformation can be realized.
Drawings
FIG. 1 is a schematic view of a reverse rolling deformation process of the present invention;
FIG. 2 is a graph of a distribution of grain boundary characteristics of austenitic stainless steel; wherein (a) is the starting material; (b) after the unidirectional rolling deformation heat treatment.
Detailed Description
The following detailed description of the preferred embodiments of the present invention, taken in conjunction with the accompanying drawings, will make the advantages and features of the invention more readily understood by those skilled in the art, and thus will more clearly and distinctly define the scope of the invention.
A process for regulating and controlling the grain boundary characteristic distribution of a hub material by utilizing reverse rolling comprises the following specific steps:
s1: firstly, carrying out solid solution treatment on an austenitic stainless steel plate and then carrying out water quenching, wherein the solid solution treatment is to carry out water quenching on the austenitic stainless steel after heat preservation for 30min at 1050 ℃;
s2: carrying out reverse rolling deformation treatment on the stainless steel plate by using a four-roller rolling mill, wherein the total deformation of reverse rolling is 3-20%, and the deformation of single rolling is 1.5-20%;
s3: and (3) placing the material subjected to the reverse rolling deformation treatment in a heat treatment furnace, adjusting the heat treatment temperature and time, annealing the material, keeping the temperature, taking out, and performing water quenching, wherein the heat treatment temperature is 1000-1150 ℃, and the heat treatment time is 5-60 min.
S4: and (3) sensitizing the processed material, and then quenching the sensitized material with water, wherein the sensitizing temperature is 650 ℃, and the sensitizing time is 2 hours.
In the following examples and comparative examples, the optimization effect of the material on the grain boundary structure characteristics is shown by low Σ CSL grain boundary ratio (%), and the higher the value is, the better the optimization effect of the grain boundary is; the corrosion resistance of the material is expressed by the reactivation current ratio (%), and the lower the reactivation current ratio, the better the corrosion resistance of the material is.
Example 1:
the austenitic stainless steel sheet was reverse-rolled and deformed by a four-high rolling mill (as shown in fig. 1), and the reverse-rolling deformation amounts were 3%, 6%, 10%, and 20%. Then, annealing treatment of keeping the temperature of 1050 ℃ for 5min is carried out on the deformation sample in a heat treatment furnace, water quenching is carried out after heat preservation, and the specific process parameters are shown in table 2; the low sigma CSL ratio inside the sample after the thermomechanical treatment changes along with the change of the reverse rolling deformation, and specific test results are shown in Table 2.
Inlaying the sample subjected to the thermomechanical treatment by using epoxy resin and a curing agent to prepare a standard electrochemical corrosion sample; at room temperature at 0.5M H2SO4The samples were subjected to an Electrokinetic Potential Reactivation (EPR) test in +0.01M KSCN solution, the reactivation current ratio was varied with the reverse rolling strain, and the reactivation current ratios measured after sensitizing the samples at 650 ℃ for 2 hours are shown in Table 2.
TABLE 2 test results for different rolling reductions
Example 2:
the austenitic stainless steel plate is reversely rolled and deformed by a four-high mill (as shown in figure 1), and the reverse rolling deformation amount is selected to be 6%. And then, annealing the deformation sample in a heat treatment furnace at 1000 ℃, 1050 ℃, 1100 ℃ and 1150 ℃ for 5min, keeping the temperature, taking out the deformation sample, and performing water quenching, wherein the specific process parameters are shown in Table 3. The low sigma CSL ratio inside the sample after the thermomechanical treatment was varied with the annealing temperature, and the specific test results are shown in Table 3.
Inlaying the sample subjected to the thermomechanical treatment with epoxy resin and a curing agent to prepare a standard electrochemical corrosion sample; at room temperature at 0.5M H2SO4Carrying out potentiodynamic reactivation (EPR) experiments on the samples in +0.01M KSCN solution, wherein the reactivation current ratio changes along with the change of annealing temperature; the reactivation current ratios and the self-corrosion potentials measured after sensitization of the test specimens at 650 ℃ for 2h are listed in Table 3.
TABLE 3 test results for different annealing temperatures
Example 3:
carrying out reverse rolling deformation on the austenitic stainless steel plate by using a four-roller mill, selecting 6% of reverse rolling deformation, then carrying out annealing treatment on a deformation sample in a heat treatment furnace, wherein the annealing temperature is 1050 ℃, the annealing time is 5min, 10min, 30min and 60min respectively, taking out after heat preservation, and carrying out water quenching, wherein specific process parameters are shown in a table 4; the low sigma CSL proportion inside the sample after the thermomechanical treatment changes along with the change of the annealing time, and specific test results are shown in Table 4;
inlaying the sample subjected to the thermomechanical treatment with epoxy resin and a curing agent to prepare a standard electrochemical corrosion sample; at room temperature at 0.5M H2SO4The samples were subjected to an Electrokinetic Potential Reactivation (EPR) experiment in +0.01M KSCN solution, the reactivation current ratio was varied with the annealing time, and the reactivation current ratios measured after sensitizing the samples at 650 ℃ for 2h are shown in Table 4.
TABLE 4 test results for different annealing times
Comparative example 1:
in order to compare the difference of the structure and performance of the material after the deformation heat treatment and the parent material, a piece of original material is taken to be subjected to solution treatment for 30min at 1050 ℃, then is subjected to sensitization for 2h at 650 ℃, and then is subjected to 0.5MH at normal temperature2SO4The electrochemical corrosion experiment is carried out in the KSCN solution of +0.01M, and the test results are shown in the table 5;
TABLE 5 results of measurements on thermo-mechanical treated materials and base materials
It can be found that under the same sensitization condition, the corrosion resistance of the crystal boundary structure optimized sample is obviously improved compared with that of the parent metal.
The material processed by the method is made into a standard metallographic specimen, and after grinding, polishing and electrolytic corrosion, the grain boundary characteristic distribution of the material is tested by utilizing a back scattering electron diffraction technology, wherein the low sigma CSL grain boundary proportion in the structure can be as high as 76.11%; under the same sensitization condition, the reactivation current is reduced from 14.58% of the parent metal to 7.32%, and the corrosion resistance of the material is obviously improved.
Fig. 2 (a) shows the grain boundary characteristic distribution in the material structure after the thermomechanical treatment by the above-described method, in which the low Σ CSL grain boundary ratio is 74.79%, and fig. 2 (b) shows the grain boundary characteristic distribution in the base material structure, in which the low Σ CSL grain boundary is 59.87%, the black line in the drawing represents a high-energy free grain boundary, and the gray line represents a low Σ CSL grain boundary.
The above examples only show several embodiments of the present invention, and the description thereof is specific and detailed, but not to be construed as limiting the scope of the invention. It should be noted that, for a person skilled in the art, several variations and modifications can be made without departing from the inventive concept, which falls within the scope of the present invention.
Claims (5)
1. A process for regulating and controlling the grain boundary characteristic distribution of a hub material by utilizing reverse rolling is characterized by comprising the following steps:
the method comprises the following specific steps:
s1: firstly, carrying out solution treatment on an austenitic stainless steel plate and then carrying out water quenching;
s2: carrying out reverse rolling deformation treatment on the stainless steel plate by using a four-high mill;
s3: and (3) placing the material subjected to the reverse rolling deformation treatment in a heat treatment furnace, adjusting the heat treatment temperature and time, carrying out annealing heat treatment on the material, and taking out the material after heat preservation for water quenching.
S4: and (4) carrying out sensitization treatment on the processed material, and then carrying out water quenching.
2. The process for regulating and controlling the grain boundary characteristic distribution of the hub material by utilizing the reverse rolling as claimed in claim 1, wherein the process comprises the following steps: the solution treatment in the S1 is water quenching after the austenitic stainless steel is subjected to heat preservation at 1050 ℃ for 30 min.
3. The process for regulating and controlling the grain boundary characteristic distribution of the hub material by utilizing the reverse rolling as claimed in claim 1, wherein the process comprises the following steps: the total deformation of the reverse rolling in the S2 is 3% -20%, and the single rolling deformation is 1.5% -20%.
4. The process for regulating and controlling the grain boundary characteristic distribution of the hub material by utilizing the reverse rolling as claimed in claim 1, wherein the step of rolling comprises the following steps: the heat treatment temperature in the S3 is 1000-1150 ℃, and the heat treatment time is 5-60 min.
5. The process for regulating and controlling the grain boundary characteristic distribution of the hub material by utilizing the reverse rolling as claimed in claim 1, wherein the step of rolling comprises the following steps: the sensitization treatment temperature in the S4 is 650 ℃, and the sensitization time is 2 h.
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Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH10317104A (en) * | 1997-05-16 | 1998-12-02 | Nippon Steel Corp | Austenitic stainless steel excellent in intergranular stress corrosion crack resistance ant its production |
| CN109971925A (en) * | 2019-05-17 | 2019-07-05 | 淮海工学院 | Improve the thermomechanical treatment process method of austenitic stainless steel anti intercrystalline corrosion performance |
| CN209424283U (en) * | 2018-12-05 | 2019-09-24 | 德龙钢铁有限公司 | A kind of hot-strip rough rolling device for small dimension continuous casting billet |
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- 2022-04-19 CN CN202210410924.3A patent/CN114774656A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH10317104A (en) * | 1997-05-16 | 1998-12-02 | Nippon Steel Corp | Austenitic stainless steel excellent in intergranular stress corrosion crack resistance ant its production |
| CN209424283U (en) * | 2018-12-05 | 2019-09-24 | 德龙钢铁有限公司 | A kind of hot-strip rough rolling device for small dimension continuous casting billet |
| CN109971925A (en) * | 2019-05-17 | 2019-07-05 | 淮海工学院 | Improve the thermomechanical treatment process method of austenitic stainless steel anti intercrystalline corrosion performance |
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