CN116117278A - Austenitic stainless steel hydrogen embrittlement-resistant weldment for hydrogen energy equipment and preparation method - Google Patents
Austenitic stainless steel hydrogen embrittlement-resistant weldment for hydrogen energy equipment and preparation method Download PDFInfo
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- CN116117278A CN116117278A CN202211441763.0A CN202211441763A CN116117278A CN 116117278 A CN116117278 A CN 116117278A CN 202211441763 A CN202211441763 A CN 202211441763A CN 116117278 A CN116117278 A CN 116117278A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K9/00—Arc welding or cutting
- B23K9/16—Arc welding or cutting making use of shielding gas
- B23K9/173—Arc welding or cutting making use of shielding gas and of a consumable electrode
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F17—STORING OR DISTRIBUTING GASES OR LIQUIDS
- F17C—VESSELS FOR CONTAINING OR STORING COMPRESSED, LIQUEFIED OR SOLIDIFIED GASES; FIXED-CAPACITY GAS-HOLDERS; FILLING VESSELS WITH, OR DISCHARGING FROM VESSELS, COMPRESSED, LIQUEFIED, OR SOLIDIFIED GASES
- F17C13/00—Details of vessels or of the filling or discharging of vessels
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F17—STORING OR DISTRIBUTING GASES OR LIQUIDS
- F17C—VESSELS FOR CONTAINING OR STORING COMPRESSED, LIQUEFIED OR SOLIDIFIED GASES; FIXED-CAPACITY GAS-HOLDERS; FILLING VESSELS WITH, OR DISCHARGING FROM VESSELS, COMPRESSED, LIQUEFIED, OR SOLIDIFIED GASES
- F17C2209/00—Vessel construction, in particular methods of manufacturing
- F17C2209/22—Assembling processes
- F17C2209/221—Welding
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F17—STORING OR DISTRIBUTING GASES OR LIQUIDS
- F17C—VESSELS FOR CONTAINING OR STORING COMPRESSED, LIQUEFIED OR SOLIDIFIED GASES; FIXED-CAPACITY GAS-HOLDERS; FILLING VESSELS WITH, OR DISCHARGING FROM VESSELS, COMPRESSED, LIQUEFIED, OR SOLIDIFIED GASES
- F17C2221/00—Handled fluid, in particular type of fluid
- F17C2221/01—Pure fluids
- F17C2221/012—Hydrogen
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/30—Hydrogen technology
- Y02E60/32—Hydrogen storage
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P90/00—Enabling technologies with a potential contribution to greenhouse gas [GHG] emissions mitigation
- Y02P90/45—Hydrogen technologies in production processes
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Abstract
The invention discloses an austenitic stainless steel hydrogen embrittlement-resistant weldment for hydrogen energy equipment and a preparation method thereof, wherein the ferrite content in the austenitic stainless steel hydrogen embrittlement-resistant weldment is 7-9%, and the proportion of dendritic ferrite content in the total ferrite content is more than 70%. According to the invention, the dendritic morphology features of ferrite can provide more channels for the diffusion of hydrogen atoms, the enrichment degree of the hydrogen atoms at the two-phase interface of austenite and ferrite is reduced, and the dominant distribution of the dendritic morphology can homogenize the hydrogen distribution of the whole weldment, so that the hydrogen embrittlement resistance of the weldment is improved.
Description
Technical Field
The invention relates to the technical field of hydrogen embrittlement resistance equipment, in particular to an austenitic stainless steel hydrogen embrittlement resistance weldment for hydrogen energy equipment and a preparation method thereof.
Background
The hydrogen energy is used as a novel development energy source, has the advantages of wide source, no pollution, recycling, and the like, thereby effectively relieving the problems of world resource shortage and environmental pollution, and is praised as the most ideal final energy source in the 21 st century. The high-pressure gas-phase hydrogen storage system has become an important point of world promotion of hydrogen energy industry, and austenitic stainless steel has good application prospect in the field of high-pressure gas-phase hydrogen storage due to good hydrogen embrittlement resistance, and is widely applied to the preparation of high-pressure gas-phase hydrogen storage components.
The austenitic stainless steel base material is processed by adopting a welding process, so that more preparation choices can be provided for the structure and the size of the high-pressure gas-phase hydrogen storage component. In order to manufacture the hydrogen storage component meeting the actual engineering requirements, and further to construct a safe and stable high-pressure gas-phase hydrogen storage system, the process of welding the austenitic stainless steel base metal is indispensable. However, thermal cycling that occurs during the welding process can promote more complex microstructures (ferrite phase) in the hydrogen storage welded component, resulting in different susceptibility to hydrogen embrittlement between the hydrogen storage welded component and the substrate. In addition, the high-pressure gas-phase hydrogen storage part is in service in a high-pressure hydrogen environment for a long time, so that the hydrogen storage welding part is more prone to hydrogen embrittlement, the service life of the hydrogen storage welding part is greatly reduced, and even serious safety accidents of the high-pressure gas-phase hydrogen storage system can be caused.
Therefore, how to improve the hydrogen embrittlement resistance of the welded component for hydrogen energy equipment is an important problem to be solved. Although there are some documents in the prior art for improving the hydrogen embrittlement resistance of weldments, for example, CN202011076334.9 in the patent document discloses a welding process for austenitic stainless steel 316L materials in a high-pressure hydrogen environment, which is proposed to change the welding filler material, increase the nickel content and nickel equivalent in the weldments, and promote the austenitization of the weldments, so as to improve the hydrogen embrittlement resistance of the weldments. However, the method proposed in this document does not consider the influence of ferrite inherent in the base material and welding thermal cycle on hydrogen embrittlement of the weld joint caused by newly generated ferrite, and there is no comparative example in this document, and it is difficult to determine the effect of this method on improving hydrogen embrittlement resistance of the weld joint, and at the same time, the welding filler material having a high nickel content is expensive, resulting in high production costs of the weld joint.
Disclosure of Invention
Based on the above, the invention aims to provide an austenitic stainless steel hydrogen embrittlement resistance weldment for hydrogen energy equipment and a preparation method thereof, so as to improve the hydrogen embrittlement resistance of the weldment.
In a first aspect, the invention provides an austenitic stainless steel hydrogen embrittlement resistant weldment for hydrogen energy equipment, wherein the ferrite content in the austenitic stainless steel hydrogen embrittlement resistant weldment is 7-9%, and the dendritic ferrite content accounts for more than 70% of the total ferrite content.
Compared with the prior art, the dendritic morphology feature of ferrite can provide more channels for diffusion of hydrogen atoms, the enrichment degree of the hydrogen atoms at the interface of austenite and ferrite is reduced, and the dominant distribution of the dendritic morphology can homogenize the hydrogen distribution of the whole weldment, so that the hydrogen embrittlement resistance of the weldment is improved.
Further, the dendritic ferrite includes a main shaft, and a plurality of dendrite axes extend from the main shaft.
Further, the number of the dendrite axes is not less than 5.
Further, the length of the spindle is greater than 15um.
Further, the spindle has an axial width greater than that of the dendrite axis.
Further, when the spindle is non-linear, the length of the connecting line between the initial end and the tail end of the spindle is greater than 1/2 of the length of the spindle.
In a second aspect, the present invention provides a method for producing an austenitic stainless steel hydrogen embrittlement resistant weldment for hydrogen energy equipment, the method comprising the steps of:
positioning and placing two stainless steel plates with the thickness of 3mm in a welding environment, wherein the stainless steel plates are processed into V-shaped grooves, the angle of the grooves is 60 degrees, the blunt edge is 1mm, and the root gap is 1mm;
and welding the two stainless steel plates to be welded by a welding gun with the stainless steel welding wire in a consumable electrode active gas shielded welding mode, wherein the welding current is 195-205A, the welding voltage is 25-27V, and the welding speed is 33-37 cm/min.
Further, the stainless steel welding wire is made of ER308 stainless steel, and the diameter of the stainless steel welding wire is 1.2mm.
Drawings
FIG. 1 is a schematic diagram of the structure of ferrite in an austenitic stainless steel hydrogen embrittlement resistant weldment for hydrogen energy equipment according to the present invention;
FIG. 2 is a schematic view of a welded V-groove of a welded workpiece according to the present invention;
FIG. 3 (a) is a microstructure of a 304 austenitic stainless steel hydrogen embrittlement resistant weldment after welding treatment in comparative example 1;
FIG. 3 (b) is a microstructure of a 304 austenitic stainless steel hydrogen embrittlement resistant weldment after welding treatment in comparative example 2;
FIG. 3 (c) is a microstructure of a 304 austenitic stainless steel hydrogen embrittlement resistant weldment after welding treatment in example 1;
FIG. 4 (a) shows the evolution of the potential distribution before and after charging of the non-dendritic ferrite (1) in comparative example 1;
FIG. 4 (b) shows the evolution of the potential distribution before and after charging of the non-dendritic ferrite (2) in comparative example 2;
FIG. 4 (c) shows the evolution of the potential distribution before and after charging of dendritic ferrite in example 1;
FIG. 5 is a stress-strain graph of comparative example 1, comparative example 2, and example 1;
FIG. 6 (a) is a graph showing the central morphology of the tensile fracture in comparative example 1;
FIG. 6 (b) is a graph of the stretch break edge topography of comparative example 1;
FIG. 6 (c) is a graph showing the central morphology of the tensile fracture in comparative example 2;
FIG. 6 (d) is a graph of the stretch break edge topography of comparative example 2;
FIG. 6 (e) is a graph showing the central morphology of the tensile fracture in example 1;
FIG. 6 (f) is a graph of the stretch break edge topography of example 1; .
Description of main reference numerals:
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The invention will be further described in the following detailed description in conjunction with the above-described figures.
Detailed Description
In order that the invention may be readily understood, a more complete description of the invention will be rendered by reference to the appended drawings. Several embodiments of the invention are presented in the figures. This invention may, however, be embodied in many different forms and should not be construed as limited to the embodiments set forth herein. Rather, these embodiments are provided so that this disclosure will be thorough and complete.
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. The terminology used herein in the description of the invention is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention. The term "and/or" as used herein includes any and all combinations of one or more of the associated listed items.
Referring to fig. 1, in a first aspect, an austenitic stainless steel hydrogen embrittlement resistant weldment for hydrogen energy equipment provided in an embodiment of the present invention has a ferrite content in the austenitic stainless steel hydrogen embrittlement resistant weldment of 7% -9%, and a dendritic ferrite content accounts for more than 70% of a total ferrite content.
In the invention, the dendritic morphology feature of ferrite can provide more channels for the diffusion of hydrogen atoms, the enrichment degree of the hydrogen atoms at the interface of austenite and ferrite is reduced, and the dominant distribution of the dendritic morphology can homogenize the hydrogen distribution of the whole weldment, so that the hydrogen embrittlement resistance of the weldment is improved.
Referring to fig. 1, specifically, the dendritic ferrite includes a main shaft 10, and a plurality of dendrite axes 11 extending from the main shaft 10.
In a preferred embodiment of the present invention, the number of dendrite axes 11 is not less than 5 in order to have a better hydrogen embrittlement resistance.
In another preferred embodiment of the present invention, the spindle 10 has a larger axial width than the dendrite axis 11 so as to have a better hydrogen embrittlement resistance.
In a preferred embodiment of the present invention, the length of the spindle 10 is greater than 15um, so as to have better hydrogen embrittlement resistance.
In another preferred embodiment of the present invention, when the spindle 10 is non-linear, the length of the connection line between the initial end and the final end of the spindle 10 is greater than 1/2 of the length of the spindle 10. If the main shaft is in a bent or curved state, the hydrogen embrittlement resistance of the main shaft is relatively poor.
In a second aspect, the present invention provides a method for producing an austenitic stainless steel hydrogen embrittlement resistant weldment for hydrogen energy equipment, the method comprising the steps of:
positioning and placing two stainless steel plates with the thickness of 3mm in a welding environment, wherein the stainless steel plates are processed into V-shaped grooves, the angle of the grooves is 60 degrees, the blunt edge is 1mm, and the root gap is 1mm;
and welding the two stainless steel plates to be welded by adopting a welding gun provided with a stainless steel welding wire through consumable electrode active gas shielded welding, wherein the welding current is 195-205A, the welding voltage is 25-27V, and the welding speed is 33-37 cm/min.
Further, the stainless steel welding wire is made of ER308, and the diameter of the stainless steel welding wire is 1.2mm.
The technical scheme of the invention is described below by using specific embodiments and combining the drawings.
Comparative example 1
The welding workpiece is 304 austenitic stainless steel plate with the thickness of 3mm, and the welding wire is ER308 with the diameter of 1.2mm. The welding workpiece is processed into a V-shaped groove, the groove angle is 60 degrees, the blunt edge is 1mm, and the root gap is 1mm (as shown in figure 2). Polishing and cleaning the plates before welding to remove the influences of greasy dirt, rust, oxide films and the like. And welding the welding workpiece by adopting active gas shielded welding of a consumable electrode. In the welding process, the shielding gas adopts Ar+20% CO with the gas flow of 10L/min 2 The mixed gas (when the gas flow is too large, turbulent gas flow can be formed to destroy gas protection, thereby causing weld seam pore defects, and when the gas flow is too small, the protection capability of a molten pool is weakened, pores are easy to generate), the extension length of a welding wire is 12mm, the welding current is 180A, the welding voltage is 25V, the welding speed is 40cm/min, after a weldment is cooled to room temperature, the appearance of the weld seam is inspected, welding defect detection is carried out, and the welding quality of the weldment is determined to be good;
cutting a 10mm 1mm weld slice sample, polishing, and observing the microstructure of the sample, as shown in fig. 3 (a), wherein ferrite is distributed in a non-dendritic form such as a lath form, a block form and the like;
using SKPFM atomic force microscopy probe technique, performing potential distribution comparison experiment before and after sample hydrogen charging, as shown in fig. 4 (a);
cutting a standard tensile sample, polishing and charging hydrogen, and then carrying out a slow strain rate experiment on the sample, as shown in fig. 5;
the weldment was tested for hydrogen embrittlement resistance and the sample fracture morphology was observed as shown in fig. 6 (a) and 6 (b).
Comparative example 2
The welding workpiece is 304 austenitic stainless steel plate with the thickness of 3mm, and the welding wire is ER308 with the diameter of 1.2mm. The welding workpiece is processed into a V-shaped groove, the groove angle is 60 degrees, the blunt edge is 1mm, and the root gap is 1mm (as shown in figure 2). Polishing and cleaning the plates before welding to remove the influences of greasy dirt, rust, oxide films and the like. And welding the welding workpiece by adopting active gas shielded welding of a consumable electrode. During welding, the shielding gas is extractedAr+20% CO with gas flow rate of 10L/min 2 The mixed gas (when the gas flow is too large, turbulent gas flow can be formed to destroy gas protection, thereby causing weld seam pore defects, and when the gas flow is too small, the protection capability of a molten pool is weakened, pores are easy to generate), the extension length of a welding wire is 12mm, the welding current is 220A, the welding voltage is 25V, the welding speed is 40cm/min, after a weldment is cooled to room temperature, the appearance of the weld seam is inspected, welding defect detection is carried out, and the welding quality of the weldment is determined to be good;
cutting a 10mm 1mm weld slice sample, polishing the sample, and observing the microstructure of the sample, as shown in fig. 3 (b), wherein ferrite is distributed in a non-dendritic form such as a ring shape;
using SKPFM atomic force microscopy probe technique, making potential distribution comparison experiment before and after sample hydrogen charging, as shown in FIG. 4 (b);
cutting a standard tensile sample, polishing and charging hydrogen, and then carrying out a slow strain rate experiment on the sample, as shown in fig. 5;
the weldment was tested for hydrogen embrittlement resistance and the sample fracture morphology was observed as shown in fig. 6 (c) and 6 (d).
Example 1
The welding workpiece is 304 austenitic stainless steel plate with the thickness of 3mm, and the welding wire is ER308 with the diameter of 1.2mm. The welding workpiece is processed into a V-shaped groove, the groove angle is 60 degrees, the blunt edge is 1mm, and the root gap is 1mm (as shown in figure 2). Polishing and cleaning the plates before welding to remove the influences of greasy dirt, rust, oxide films and the like. And welding the welding workpiece by adopting active gas shielded welding of a consumable electrode. In the welding process, the shielding gas adopts Ar+20% CO with the gas flow of 10L/min 2 The mixed gas (when the gas flow is too large, turbulent gas flow can be formed to destroy gas protection, thereby causing weld seam pore defects, and when the gas flow is too small, the protection capability of a molten pool is weakened, pores are easy to generate), the extending length of a welding wire is 12mm, the welding current is 200A, the welding voltage is 25V, the welding speed is 35cm/min, after a weldment is cooled to room temperature, the appearance of the weld seam is inspected, welding defect detection is carried out, and the welding quality of the weldment is determined to be good;
cutting a 10mm 1mm weld slice sample, polishing the sample, and observing the microstructure of the sample, wherein ferrite is distributed in a dendritic form as shown in fig. 3 (c);
using SKPFM atomic force microscopy probe technique, making potential distribution comparison experiment before and after sample hydrogen charging, as shown in figure 4 (c);
cutting a standard tensile sample, polishing and charging hydrogen, and then carrying out a slow strain rate experiment on the sample, as shown in fig. 5;
the weldment was tested for hydrogen embrittlement resistance and the sample fracture morphology was observed as shown in fig. 6 (e) and 6 (f).
It is to be noted that the invention is mainly applied to the preparation of hydrogen-contacting components such as the inner cylinder of the cylinder body of the high-pressure hydrogen storage container, the inner layer of the sealing head and the like. Specifically, in the invention, the welding parent metal is austenitic stainless steel, and the microstructure is basically pure austenitic phase. However, due to the welding process, the applied heat input can cause localized high temperature + post-weld cooling processes at the weld location of the weldment. This process results in the occurrence of an austenite transformation, whereby transformation of the austenite phase to the ferrite phase occurs, so that the welded microstructure assumes an austenite phase + ferrite phase.
Since the behavior of hydrogen in both the austenitic phase and the ferritic phase is greatly different. The concrete steps are as follows: the diffusion rate of hydrogen in the ferrite phase is high, but the solubility is low; the diffusion rate of hydrogen in the austenitic phase is low but the solubility is high. This results in the diffusion of hydrogen into the ferrite, which diffuses rapidly to the boundary of the two phases due to low solubility but rapid diffusion, but which slows down when reaching the boundary of the austenitic phase, and which dissolves in a large amount, thus causing the accumulation and enrichment of hydrogen at the boundary of the two phases.
Referring to fig. 4 (a) to 4 (c), the evolution of the potential distribution before and after the ferrite of different forms is observed to reflect the strength of the hydrogen atom enrichment degree according to the height of the potential difference value. Specifically, after ferrite is regulated by the technology of the invention, the dendritic morphological characteristics of the ferrite can provide more channels for the diffusion of hydrogen atoms, so that the enrichment degree of the hydrogen atoms at the interface between austenite and ferrite is reduced, as shown in table 1 (only the marked points from 4 (a) to 4 (c) are shown).
Table 1 shows potential data at the interface of the ferrite of different forms before and after hydrogen charging
| Before hydrogen charging (mV) | After charging hydrogen (mV) | Potential difference value (mV) | |
| Comparative example 1 | -113 | 287 | 400 |
| Example 1 | -104 | 268 | 372 |
| Comparative example 2 | -109 | 274 | 383 |
Referring to fig. 5, compared with comparative examples 1 and 2, the plasticity of the weldment after being charged with hydrogen is improved, and the result shows that the hydrogen embrittlement resistance of the weldment is improved.
Referring to fig. 6 (a) to 6 (f), the tensile fracture analysis after the weld of comparative examples 1 and 2 and example 1 after the hydrogen filling showed that: compared with comparative examples 1 and 2, after the treatment of the technology of the invention, the size and depth of the ductile fos of the fracture of the weldment are larger, and the proportion of the dissociated fracture area at the edge of the fracture is reduced, which also shows that the technology of the invention improves the hydrogen embrittlement resistance of the 304 austenitic stainless steel hydrogen embrittlement resistance weldment.
The base material used in the present invention is not limited to 304 austenitic stainless steel, and other austenitic stainless steels are equally applicable.
In summary, the invention has the following advantages:
firstly, the ferrite morphology distribution in the weldment is regulated and controlled in a dendritic morphology through the welding process and the parameters, the enrichment degree of hydrogen atoms at the two-phase interface of austenite and ferrite is reduced, the whole hydrogen distribution of the weldment is homogenized, and the hydrogen embrittlement resistance of the weldment is improved;
second, the invention does not need to use expensive welding filling materials, does not need to carry out additional processing treatment on welding parts, and has low production cost.
Thirdly, the practical operation of the invention is not limited by the size and shape of weldment, which is beneficial to the popularization in the high-pressure gas-phase hydrogen storage field.
In this specification, each embodiment is described in a progressive manner, and each embodiment focuses on a difference from other embodiments, and the same or similar parts between the embodiments are referred to each other. And the above examples only represent a few embodiments of the present invention, which are described in more detail and are not to be construed as limiting the scope of the invention. It should be noted that it will be apparent to those skilled in the art that several variations and modifications can be made without departing from the spirit of the invention, which are all within the scope of the invention. Accordingly, the scope of protection of the present invention is to be determined by the appended claims.
Claims (8)
1. An austenitic stainless steel hydrogen embrittlement resistant weldment for hydrogen energy equipment, which is characterized in that: the ferrite content in the austenitic stainless steel hydrogen embrittlement resistant weldment is 7% -9%, and the proportion of dendritic ferrite content in the total ferrite content is more than 70%.
2. The austenitic stainless steel hydrogen embrittlement resistant weldment for hydrogen energy equipment of claim 1, wherein the dendritic ferrite includes a main shaft and a plurality of dendrite axes extending from the main shaft.
3. The austenitic stainless steel hydrogen embrittlement resistant weld joint for hydrogen energy equipment according to claim 2, wherein the number of the dendrite axes is not less than 5.
4. The austenitic stainless steel hydrogen embrittlement resistant weldment for hydrogen energy equipment of claim 2, wherein the length of the main shaft is greater than 15um.
5. The austenitic stainless steel hydrogen embrittlement resistant weld joint for hydrogen energy equipment according to claim 2, wherein an axial width of the main shaft is larger than an axial width of the dendrite axis.
6. The austenitic stainless steel hydrogen embrittlement resistant weld joint for hydrogen energy equipment according to claim 2, wherein when the main shaft is non-linear, a length of a line connecting an initial end and a terminal end of the main shaft is greater than 1/2 of a length of the main shaft.
7. A method for producing an austenitic stainless steel hydrogen embrittlement resistant weldment for hydrogen energy equipment according to any one of claims 1 to 6, characterized in that the production method comprises the steps of:
positioning and placing two stainless steel plates with the thickness of 3mm in a welding environment, wherein the stainless steel plates are processed into V-shaped grooves, the angle of the grooves is 60 degrees, the blunt edge is 1mm, and the root gap is 1mm;
and welding the two stainless steel plates to be welded by a welding gun with the stainless steel welding wire in a consumable electrode active gas shielded welding mode, wherein the welding current is 195-205A, the welding voltage is 25-27V, and the welding speed is 33-37 cm/min.
8. The method for producing an austenitic stainless steel hydrogen embrittlement resistant welding member for hydrogen energy equipment according to claim 7, wherein the stainless steel wire is ER308 stainless steel, and has a diameter of 1.2mm.
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| CN111283308B (en) * | 2020-03-09 | 2021-09-14 | 武汉一冶钢结构有限责任公司 | All-position shielded metal arc welding process for ultralow-temperature 304LN austenitic stainless steel medium plate |
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