CN115679230B - Surface treatment process for improving hydrogen embrittlement resistance of nickel-based corrosion-resistant alloy - Google Patents
Surface treatment process for improving hydrogen embrittlement resistance of nickel-based corrosion-resistant alloy Download PDFInfo
- Publication number
- CN115679230B CN115679230B CN202211341487.0A CN202211341487A CN115679230B CN 115679230 B CN115679230 B CN 115679230B CN 202211341487 A CN202211341487 A CN 202211341487A CN 115679230 B CN115679230 B CN 115679230B
- Authority
- CN
- China
- Prior art keywords
- laser
- treatment
- nickel
- resistant alloy
- surface treatment
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 70
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 63
- 239000000956 alloy Substances 0.000 title claims abstract description 63
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 title claims abstract description 48
- 230000007797 corrosion Effects 0.000 title claims abstract description 48
- 238000005260 corrosion Methods 0.000 title claims abstract description 48
- 229910052739 hydrogen Inorganic materials 0.000 title claims abstract description 48
- 239000001257 hydrogen Substances 0.000 title claims abstract description 48
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 35
- 238000000034 method Methods 0.000 title claims abstract description 32
- 238000004381 surface treatment Methods 0.000 title claims abstract description 26
- 230000008569 process Effects 0.000 title claims abstract description 18
- 238000011282 treatment Methods 0.000 claims abstract description 39
- 230000032683 aging Effects 0.000 claims abstract description 23
- 238000012545 processing Methods 0.000 claims abstract description 19
- 238000013532 laser treatment Methods 0.000 claims abstract description 17
- 239000000243 solution Substances 0.000 claims abstract description 16
- 238000001816 cooling Methods 0.000 claims abstract description 13
- 239000006104 solid solution Substances 0.000 claims abstract description 11
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 12
- 230000004927 fusion Effects 0.000 claims description 11
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 238000005096 rolling process Methods 0.000 claims description 5
- 238000005498 polishing Methods 0.000 claims description 4
- 239000000126 substance Substances 0.000 claims description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 3
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 3
- 229910052782 aluminium Inorganic materials 0.000 claims description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 239000011651 chromium Substances 0.000 claims description 3
- 229910052802 copper Inorganic materials 0.000 claims description 3
- 239000010949 copper Substances 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 239000011572 manganese Substances 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 239000011733 molybdenum Substances 0.000 claims description 3
- 229910052758 niobium Inorganic materials 0.000 claims description 3
- 239000010955 niobium Substances 0.000 claims description 3
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 3
- 229910052710 silicon Inorganic materials 0.000 claims description 3
- 239000010703 silicon Substances 0.000 claims description 3
- 239000010936 titanium Substances 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- 238000005452 bending Methods 0.000 claims description 2
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 claims 2
- 239000000463 material Substances 0.000 abstract description 19
- 238000004519 manufacturing process Methods 0.000 abstract description 8
- 239000011159 matrix material Substances 0.000 description 8
- 238000010438 heat treatment Methods 0.000 description 7
- NBIIXXVUZAFLBC-UHFFFAOYSA-N Phosphoric acid Chemical compound OP(O)(O)=O NBIIXXVUZAFLBC-UHFFFAOYSA-N 0.000 description 6
- 239000007769 metal material Substances 0.000 description 5
- 239000013078 crystal Substances 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 229910000147 aluminium phosphate Inorganic materials 0.000 description 3
- 239000003795 chemical substances by application Substances 0.000 description 3
- 238000001514 detection method Methods 0.000 description 3
- 238000001887 electron backscatter diffraction Methods 0.000 description 3
- 239000007788 liquid Substances 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 231100000572 poisoning Toxicity 0.000 description 3
- 230000000607 poisoning effect Effects 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 238000010998 test method Methods 0.000 description 3
- 229910000934 Monel 400 Inorganic materials 0.000 description 2
- 238000003723 Smelting Methods 0.000 description 2
- 230000009471 action Effects 0.000 description 2
- 238000005253 cladding Methods 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- OANFWJQPUHQWDL-UHFFFAOYSA-N copper iron manganese nickel Chemical compound [Mn].[Fe].[Ni].[Cu] OANFWJQPUHQWDL-UHFFFAOYSA-N 0.000 description 2
- UGKDIUIOSMUOAW-UHFFFAOYSA-N iron nickel Chemical compound [Fe].[Ni] UGKDIUIOSMUOAW-UHFFFAOYSA-N 0.000 description 2
- 238000004372 laser cladding Methods 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 238000001878 scanning electron micrograph Methods 0.000 description 2
- 238000004626 scanning electron microscopy Methods 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- 229910001093 Zr alloy Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000006378 damage Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000009713 electroplating Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000007499 fusion processing Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910001293 incoloy Inorganic materials 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 229910001338 liquidmetal Inorganic materials 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 239000003345 natural gas Substances 0.000 description 1
- 229910021652 non-ferrous alloy Inorganic materials 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 239000003208 petroleum Substances 0.000 description 1
- 239000003209 petroleum derivative Substances 0.000 description 1
- 238000010248 power generation Methods 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000005406 washing Methods 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Landscapes
- Laser Beam Processing (AREA)
Abstract
The invention discloses a surface treatment process for improving hydrogen embrittlement resistance of a nickel-based corrosion-resistant alloy, which comprises the following steps of: (1) laser fusing treatment: carrying out laser treatment on the nickel-based corrosion-resistant alloy sample, wherein the laser power is 100-200W, and the laser processing speed is 5-10 mm/s; (2) solution treatment: carrying out solid solution on the sample subjected to laser treatment at 1000-1040 ℃ for 0.25-0.5 h, and then carrying out air cooling; (3) aging treatment: and (3) aging the air-cooled sample at 600-800 ℃ for 10-22 hours, and then air-cooling to finish the surface treatment. The invention can improve the hydrogen embrittlement resistance of the material by simple methods such as solid solution aging and the like on the premise of not changing the alloy components, has the characteristics of simple production process, high production speed, lower equipment requirement, high production efficiency, small heat influence, reliable quality and the like, and can also be used for processing parts with a certain degree of complexity.
Description
Technical Field
The invention relates to the technical field of alloy surface treatment, in particular to a surface treatment process for improving hydrogen embrittlement resistance of a nickel-based corrosion-resistant alloy.
Background
The hydrogen embrittlement refers to the phenomenon that the mechanical properties of a metal material are seriously degraded due to hydrogen absorption or hydrogen permeation in the processes of smelting, processing, heat treatment, acid washing, electroplating and the like or in a hydrogen-containing medium for a long time, so that brittle failure occurs. The phenomenon of hydrogen embrittlement is found not only in ordinary steels, but also in stainless steels, aluminum alloys, titanium alloys, nickel-based corrosion resistant alloys and zirconium alloys. From the mechanical point of view, hydrogen embrittlement is represented by: the hydrogen has little influence on the yield strength and the ultimate strength of the metal material, but seriously reduces the elongation and the area shrinkage, obviously shortens the fatigue life and obviously reduces the impact toughness value. Under the continuous action of tensile stress lower than the breaking strength, the material is suddenly brittle broken after a period of time.
The nickel-base corrosion-resistant alloy not only has unique corrosion resistance and even high-temperature corrosion resistance in various industrial corrosion environments, but also has the properties of high strength, good plastic toughness, smelting, casting, cold-hot deformation, processing and forming, welding and the like, and is widely applied to industries such as nuclear industry, petroleum and natural gas exploitation, storage and transportation equipment, hydroelectric power generation, chemical industry, high-temperature pulp production equipment and the like. The nickel-base corrosion-resistant alloy has excellent hydrogen embrittlement resistance and is widely used for manufacturing oil pipeline valves, bolts and other parts in petroleum industry. With the wide application of the nickel-based corrosion-resistant alloy in various industries, the performance requirements of the nickel-based corrosion-resistant alloy in the industry are higher and higher, and the market demands for the nickel-based corrosion-resistant alloy with better hydrogen embrittlement resistance are growing.
In improving the hydrogen embrittlement resistance of nickel-base corrosion-resistant alloys, there are some cases in which the hydrogen embrittlement resistance of nickel-base corrosion-resistant alloys is improved by a special heat treatment method. For example, chinese patent application CN 110564948A proposes a method of converting part of the straight grain boundaries in an alloy into zigzag grain boundaries by controlling a cooling rate heat treatment, which can convert high-energy straight grain boundaries into low-energy zigzag grain boundaries, to some extent improving the hydrogen embrittlement resistance of an iron-nickel-based corrosion resistant alloy. The process belongs to the integral heat treatment of materials, and the possibility of deterioration of the mechanical properties of matrix materials often exists when the hydrogen embrittlement resistance is improved. On the other hand, the air cooling heat treatment method is only one for J100 alloy, so that the method has certain limitations.
There are also reports of enhancing the performance of alloys by laser cladding nickel-based corrosion resistant alloy coatings, for example, chinese patent application CN 108130528A proposes a method of cladding nickel-based corrosion resistant alloy coatings on the surface of Monel 400 alloy, which is mainly to improve the performance of the base material by cladding a layer of self-formulated nickel-based corrosion resistant alloy powder on Monel 400 base by laser cladding. Although this method provides a significant improvement in hardness and wear resistance of the material, it does not involve hydrogen resistance. And the method needs to prepare proper nickel-based corrosion-resistant alloy powder in advance, which certainly increases a plurality of working procedures and brings uncertainty to experimental results.
At present, a method for improving the hydrogen embrittlement resistance of the alloy by adopting laser fusion and solid solution aging is not reported. Laser fusion processes are processes in which a laser with a high power density interacts with a metal in a very short time, so that localized areas of the metal surface are instantaneously heated to a relatively high temperature to melt them. The melted surface metal is then rapidly solidified by means of the endothermic and conductive action of the liquid metal matrix. The solution treatment is to heat the alloy to a proper temperature and for a sufficient time to dissolve certain components in the alloy into the matrix to form a uniform solid solution, then rapidly cool the alloy to leave the components dissolved into the matrix in a supersaturated solid solution, thus improving the ductility and toughness of the alloy and creating conditions for further precipitation hardening treatments. Solution treatment is often used for nonferrous alloys. Aging treatment refers to a heat treatment process in which a metal or alloy workpiece (such as low-carbon steel) is subjected to solution treatment, quenched from a high temperature or subjected to cold working deformation to a certain extent, and then placed at a higher temperature or room temperature to maintain the shape and size of the workpiece, and the performance of the workpiece changes with time. Generally, over time, the hardness, strength, plastic toughness, and internal stress of the material change.
Disclosure of Invention
The invention aims to solve the problems and provide a surface treatment process for a nickel-based corrosion-resistant alloy, which reduces the hydrogen embrittlement sensitivity of the nickel-based corrosion-resistant alloy by improving the proportion of the hydrogen-resistant grain boundary on the surface layer and improves the hydrogen damage resistance of the existing nickel-based corrosion-resistant alloy.
In order to achieve the purpose, the invention adopts the following technical scheme:
a surface treatment process for improving hydrogen embrittlement resistance of nickel-based corrosion-resistant alloy is characterized by comprising the following steps:
(1) And (3) laser fusion treatment: carrying out laser treatment on the nickel-based corrosion-resistant alloy sample, wherein the laser power is 100-200W, and the laser processing speed is 5-10 mm/s;
(2) Solution treatment: carrying out solid solution on the sample subjected to laser treatment at 1000-1040 ℃ for 0.25-0.5 h, and then carrying out air cooling;
(3) Aging treatment: and (3) aging the air-cooled sample at 600-800 ℃ for 10-22 hours, and then air-cooling to finish the surface treatment.
Preferably, the alloy sample is polished to remove scale and ensure surface flatness for laser machining prior to laser treatment in step (1).
Preferably, in the step (1), the laser treatment is laser scanned along the rolling direction of the sheet, and the laser spot diameter is 1 to 2mm.
Preferably, the nickel-based corrosion resistant alloy is an iron-nickel-based corrosion resistant alloy.
Preferably, the chemical components of the nickel-based corrosion resistant alloy are as follows, nickel: 45.0-55.0%, chromium: 19.5-23.0%, titanium: 0.5-2.5%, aluminum: 0.01-0.7%, silicon: less than or equal to 0.5 percent, carbon: 0.005-0.04%, molybdenum: 3.0-4.0%, niobium: 2.5-4.5%, copper: 1.5-3.0%, manganese: less than or equal to 1.0 percent, iron: the balance.
Preferably, the laser power of the laser fusing treatment is 100 to 180W or 100 to 150W or 150 to 200W, and the laser processing speed is 5 to 7mm/s or 7 to 10mm/s.
Preferably, the solution treatment is carried out at 1000-1040 ℃ for 0.3-0.5 h or 0.4-0.5 h or 0.5h.
Preferably, the aging treatment is carried out at 600-750 ℃ for 12-20 hours.
Further preferably, the aging treatment is conducted at 600-730 ℃ or 615-730 ℃ or 620-725 ℃ for 14-18 hours or 15-17 hours or 16 hours.
In the technical scheme, the thickness of the nickel-based corrosion-resistant alloy sample plate is 2-4 mm or 2-3 mm, and the plate is straight and has no obvious bending.
The beneficial effects of the invention are as follows:
1. the invention can improve the hydrogen embrittlement resistance of the material by simple methods such as solid solution aging and the like after laser without changing the alloy components, and has the characteristics of simple production process, high production speed, lower requirement on equipment and the like.
2. The invention adopts laser fusion treatment, which not only has the characteristics of high production efficiency, small heat influence, reliable quality and the like, but also can be used for processing parts with a certain complexity.
Drawings
FIG. 1 is an SEM image of laser-fused experimental nickel-base corrosion resistant alloy of example 1.
FIG. 2 is an EBSD image of the experimental group nickel-base corrosion resistant alloy of example 1 after laser fusing.
FIG. 3 is an EBSD chart after the experimental group nickel-base corrosion resistant alloy solution process in example 1.
FIG. 4 is an EBSD chart of the aging process for the experimental group nickel-base corrosion resistant alloy in example 1.
Fig. 5 is an SEM image of the nickel-base corrosion-resistant alloy of example 2 after laser and solid solution.
Detailed Description
The invention is further illustrated, but is not limited, by the following examples.
The nickel-based corrosion-resistant alloy in each embodiment of the invention is Incoloy alloy945, the thickness of the sample plate is 2mm, and the chemical components are as follows: nickel: 45.0-55.0%, chromium: 19.5-23.0%, titanium: 0.5-2.5%, aluminum: 0.01-0.7%, silicon: less than or equal to 0.5 percent, carbon: 0.005-0.04%, molybdenum: 3.0-4.0%, niobium: 2.5-4.5%, copper: 1.5-3.0%, manganese: less than or equal to 1.0 percent, iron: the balance.
Example 1
1. Alloy surface treatment
Samples of 3 parallel experimental groups according to the present invention were prepared, and operated as follows:
1. and 945, polishing the nickel-based corrosion-resistant alloy sample to remove iron scales, ensuring the surface flatness so as to facilitate laser processing, and ensuring the uniformity of the surface quality after laser processing.
2. And (3) laser fusion treatment: and carrying out laser treatment on the polished sample, and carrying out laser scanning along the rolling direction of the plate, wherein the laser power is 100W, the laser processing speed is 5mm/s, the spot diameter is 1mm, the lap joint rate is 50%, and the defocusing amount is 2mm. SEM analysis is carried out after the laser treatment is finished, as shown in figure 1, the grain size of a molten pool area after the laser is far smaller than that of a matrix area, the upper part of the molten pool is columnar crystal, and the bottom part of the molten pool is equiaxed crystal.
3. Solution treatment: the laser-treated sample was solutioned at 1000℃for 0.5h, followed by air cooling.
4. Aging treatment: and (3) aging the air-cooled sample at 621 ℃ for 16 hours, and then air-cooling to finish the surface treatment.
At the same time, 3 parallel control samples were prepared, which were treated in steps 1, 3, and 4 above (i.e., only solution aging treatment was performed, and no laser fusion treatment was performed).
2. Performance detection
And carrying out hydrogen filling stretching on the sample subjected to the surface treatment. The hydrogen charging liquid is a mixture of phosphoric acid and poisoning agent, the hydrogen charging temperature is 75 ℃, the normal pressure is adopted, and the hydrogen charging time is 5 hours. Stretching is carried out according to GB/T228.1-2010 section 1 room temperature test method for tensile test of metallic materials, and the mechanical properties of 3 parallel samples are averaged. The mechanical properties of the experimental and control samples are shown in table 1 below:
TABLE 1
As is clear from the results in Table 1, the nickel-based corrosion-resistant alloy surface-treated by the method of the present invention has an average tensile strength of 1135MPa, a yield strength of 833MPa, and an elongation of 13.4%. The control group is only free of laser treatment, other treatment steps are identical to those of the experimental group, and the mechanical properties of the control group sample after being charged with hydrogen are as follows: the tensile strength is 1028MPa, the yield strength is 758MPa, and the elongation is 9.2%. The comparison of the two materials can find that the tensile strength, the yield strength and the elongation of the material after laser are obviously improved, and the hydrogen embrittlement resistance of the material is obviously improved.
The invention adopts laser solid solution aging to carry out surface treatment on the nickel-based corrosion-resistant alloy, and the mechanism is mainly to improve the hydrogen embrittlement resistance of the material by improving the proportion of sigma 3 crystal boundaries, and the increase of the sigma 3 crystal boundaries can improve the corrosion resistance of the alloy and also improve the hydrogen embrittlement resistance of the material. Firstly, the rapid heating and rapid cooling of the laser fusion refines the grains, the effect of fine grain strengthening is achieved, the average grain size of a molten pool area is about one third of that of the matrix grains (figure 2), the grain size of the bottom of the molten pool is about one fiftieth of that of the matrix grains, and the proportion of sigma 3 hydrogen-resistant grain boundaries is only 2%. Second, the solution process increases the proportion of Σ3 hydrogen resistant grain boundaries, and the Σ3 grain boundaries of the surface layer fused region increases from 2% to 43.3% (fig. 3). Finally, the aging process increases the sigma 3 grain boundaries to 54.2% (fig. 4), which further improves the hardness and plasticity of the material.
Example 2
1. Alloy surface treatment
Samples of 3 parallel experimental groups according to the present invention were prepared, and operated as follows:
1. and 945, polishing the nickel-based corrosion-resistant alloy sample to remove iron scales, ensuring the surface flatness so as to facilitate laser processing, and ensuring the uniformity of the surface quality after laser processing.
2. And (3) laser fusion treatment: and carrying out laser treatment on the polished sample, and carrying out laser scanning along the rolling direction of the plate, wherein the laser power is 200W, the laser processing speed is 10mm/s, the spot diameter is 1mm, the lap joint rate is 50%, and the defocusing amount is 2mm.
3. Solution treatment: and (3) carrying out solid solution on the sample subjected to laser treatment for 0.5h at 1040 ℃, and finally carrying out air cooling. SEM analysis is then carried out, as shown in FIG. 5, in which the grain size of the laser region after solutionizing is still smaller than that of the matrix region, and at this time, fine grains growing at the bottom of the molten pool can be observed.
4. Aging treatment: the air-cooled sample was aged at 721℃for 16 hours, and then air-cooled, thereby completing the surface treatment.
At the same time, 3 parallel control samples were prepared, which were treated in steps 1, 3, and 4 above (i.e., only solution aging treatment was performed, and no laser fusion treatment was performed).
2. Performance detection
And carrying out hydrogen filling stretching on the sample subjected to the surface treatment. The hydrogen charging liquid is a mixture of phosphoric acid and poisoning agent, the hydrogen charging temperature is 75 ℃, the normal pressure is adopted, and the hydrogen charging time is 5 hours. Stretching is carried out according to GB/T228.1-2010 section 1 room temperature test method for tensile test of metallic materials, and the mechanical properties of 3 parallel samples are averaged. The mechanical properties of the experimental and control samples are shown in table 2 below:
TABLE 2
As is clear from the results in Table 2, the nickel-based corrosion-resistant alloy surface-treated by the method of the present invention had an average tensile strength of 1097MPa, a yield strength of 784MPa and an elongation of 17.7%. The control group is only free of laser treatment, other treatment steps are identical to those of the experimental group, and the mechanical properties of the control group sample after being charged with hydrogen are as follows: the tensile strength is 1012MPa, the yield strength is 773MPa, and the elongation is 11.5%. The comparison of the two materials can find that the tensile strength and the elongation of the material after laser are obviously improved, and the hydrogen embrittlement resistance of the material is obviously improved.
Example 3
1. Alloy surface treatment
Samples of 3 parallel experimental groups according to the present invention were prepared, and operated as follows:
1. and 945, polishing the nickel-based corrosion-resistant alloy sample to remove iron scales, ensuring the surface flatness so as to facilitate laser processing, and ensuring the uniformity of the surface quality after laser processing.
2. And (3) laser fusion treatment: and carrying out laser treatment on the polished sample, and carrying out laser scanning along the rolling direction of the plate, wherein the laser power is 150W, the laser processing speed is 7mm/s, the spot diameter is 1mm, the lap joint rate is 50%, and the defocusing amount is 2mm.
3. Solution treatment: the laser-treated sample was solutioned at 1020℃for 0.5h, followed by air cooling.
4. Aging treatment: the air-cooled sample was aged at 721℃for 16 hours, and then air-cooled, thereby completing the surface treatment.
At the same time, 3 parallel control samples were prepared, which were treated in steps 1, 3, and 4 above (i.e., only solution aging treatment was performed, and no laser fusion treatment was performed).
2. Performance detection
And carrying out hydrogen filling stretching on the sample subjected to the surface treatment. The hydrogen charging liquid is a mixture of phosphoric acid and poisoning agent, the hydrogen charging temperature is 75 ℃, the normal pressure is adopted, and the hydrogen charging time is 5 hours. Stretching is carried out according to GB/T228.1-2010 section 1 room temperature test method for tensile test of metallic materials, and the mechanical properties of 3 parallel samples are averaged. The mechanical properties of the experimental and control samples are shown in table 3 below:
TABLE 3 Table 3
As is clear from the results in Table 3, the nickel-based corrosion-resistant alloy surface-treated by the method of the present invention had an average tensile strength of 1197MPa, a yield strength of 875MPa, and an elongation of 15.6%. The control group is only free of laser treatment, other treatment steps are identical to those of the experimental group, and the mechanical properties of the control group sample after being charged with hydrogen are as follows: the tensile strength is 1075MPa, the yield strength is 768MPa, and the elongation is 10.8%. The comparison of the two materials can find that the tensile strength, the yield strength and the elongation of the material after laser are obviously improved, and the hydrogen embrittlement resistance of the material is obviously improved.
Claims (6)
1. A surface treatment process for improving hydrogen embrittlement resistance of nickel-based corrosion-resistant alloy is characterized by comprising the following steps:
and (3) laser fusion treatment: carrying out laser treatment on the nickel-based corrosion-resistant alloy sample, wherein the laser treatment is scanned along the rolling direction of the plate, the laser power is 100-200W, and the laser processing speed is 5-10 mm/s; the nickel-based corrosion-resistant alloy comprises the following chemical components in percentage by weight: 45.0-55.0%, chromium: 19.5-23.0%, titanium: 0.5-2.5%, aluminum: 0.01-0.7%, silicon: less than or equal to 0.5 percent, carbon: 0.005-0.04%, molybdenum: 3.0-4.0%, niobium: 2.5-4.5%, copper: 1.5-3.0%, manganese: less than or equal to 1.0 percent, iron: the balance;
solution treatment: carrying out solid solution on the sample subjected to laser treatment at 1000-1040 ℃ for 0.4-0.5 h, and then carrying out air cooling;
aging treatment: and (3) aging the air-cooled sample at 600-750 ℃ for 10-20 hours, and then air-cooling to finish the surface treatment.
2. The surface treatment process according to claim 1, wherein: polishing the alloy sample to remove iron oxide scale and ensure surface flatness for laser processing before laser processing in step (1).
3. The surface treatment process according to claim 1, wherein: in the step (1), the diameter of a laser spot is 1-2 mm.
4. The surface treatment process according to claim 1, wherein: and carrying out solution treatment at 1000-1040 ℃ for 0.5h.
5. The surface treatment process according to claim 1, wherein: aging treatment is carried out at 600-730 ℃ for 14-18 h.
6. The surface treatment process according to claim 1, wherein: the thickness of the nickel-based corrosion-resistant alloy sample plate is 2-4 mm, and the plate is straight and has no obvious bending.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211341487.0A CN115679230B (en) | 2022-10-25 | 2022-10-25 | Surface treatment process for improving hydrogen embrittlement resistance of nickel-based corrosion-resistant alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211341487.0A CN115679230B (en) | 2022-10-25 | 2022-10-25 | Surface treatment process for improving hydrogen embrittlement resistance of nickel-based corrosion-resistant alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN115679230A CN115679230A (en) | 2023-02-03 |
| CN115679230B true CN115679230B (en) | 2024-01-05 |
Family
ID=85045313
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202211341487.0A Active CN115679230B (en) | 2022-10-25 | 2022-10-25 | Surface treatment process for improving hydrogen embrittlement resistance of nickel-based corrosion-resistant alloy |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115679230B (en) |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108660380A (en) * | 2018-08-03 | 2018-10-16 | 中国科学院金属研究所 | Low energy crystal boundary ratio method in iron nickel base alloy is improved by single step thermomechanical treatment |
| CN108998649A (en) * | 2018-07-17 | 2018-12-14 | 中国科学院金属研究所 | Improve the method for iron nickel base alloy resistant to hydrogen performance by improving special grain boundary ratio |
| CN110484702A (en) * | 2019-07-30 | 2019-11-22 | 中国科学院金属研究所 | A kind of heat treatment method for realizing that iron nickel base alloy crystal boundary is serrating |
| CN110964995A (en) * | 2019-11-27 | 2020-04-07 | 中国科学院金属研究所 | Increase sigma 3 IN IN718 nickel-base superalloynMethod for proportion of type crystal boundary |
| CN111500831A (en) * | 2020-06-12 | 2020-08-07 | 山东建筑大学 | Heat treatment process of 17-4PH base |
| CN114540732A (en) * | 2022-02-24 | 2022-05-27 | 上海电机学院 | Method for synergistically obtaining low sigma grain boundaries and saw-tooth grain boundaries |
| CN114540733A (en) * | 2022-02-28 | 2022-05-27 | 上海电机学院 | Method for improving high-temperature mechanical property of nickel-based alloy by synergistically obtaining two types of special crystal boundaries |
-
2022
- 2022-10-25 CN CN202211341487.0A patent/CN115679230B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108998649A (en) * | 2018-07-17 | 2018-12-14 | 中国科学院金属研究所 | Improve the method for iron nickel base alloy resistant to hydrogen performance by improving special grain boundary ratio |
| CN108660380A (en) * | 2018-08-03 | 2018-10-16 | 中国科学院金属研究所 | Low energy crystal boundary ratio method in iron nickel base alloy is improved by single step thermomechanical treatment |
| CN110484702A (en) * | 2019-07-30 | 2019-11-22 | 中国科学院金属研究所 | A kind of heat treatment method for realizing that iron nickel base alloy crystal boundary is serrating |
| CN110964995A (en) * | 2019-11-27 | 2020-04-07 | 中国科学院金属研究所 | Increase sigma 3 IN IN718 nickel-base superalloynMethod for proportion of type crystal boundary |
| CN111500831A (en) * | 2020-06-12 | 2020-08-07 | 山东建筑大学 | Heat treatment process of 17-4PH base |
| CN114540732A (en) * | 2022-02-24 | 2022-05-27 | 上海电机学院 | Method for synergistically obtaining low sigma grain boundaries and saw-tooth grain boundaries |
| CN114540733A (en) * | 2022-02-28 | 2022-05-27 | 上海电机学院 | Method for improving high-temperature mechanical property of nickel-based alloy by synergistically obtaining two types of special crystal boundaries |
Non-Patent Citations (1)
| Title |
|---|
| Nanocrystallization of Ni-based superalloy K403 by laser shock peening;An Zhibin;《红外与激光工程》;第第45 卷卷(第第9 期期);1-6 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN115679230A (en) | 2023-02-03 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US5560790A (en) | Zirconium-based material, products made from said material for use in the nuclear reactor core, and process for producing such products | |
| CN111961893B (en) | High-strength high-plasticity high-entropy alloy and preparation method thereof | |
| CN114480893B (en) | Method for reducing additive manufacturing cracks of nickel-based superalloy and nickel-based superalloy | |
| CN103614597A (en) | Anti-exfoliation corrosion high-strength aluminum-zinc-magnesium-copper alloy and heat treatment process | |
| CN114657417B (en) | High-strength plastic titanium alloy suitable for cold deformation processing and preparation method thereof | |
| CN114622145B (en) | Cobalt-free maraging steel with dual-phase structure and preparation method thereof | |
| CN114293120B (en) | Pulse electric field auxiliary heat treatment method for improving plasticity and toughness of titanium alloy | |
| CN111826549A (en) | High-toughness titanium alloy and method for preparing bar by using same | |
| CN117568669A (en) | Creep-resistant copper-aluminum composite board for lithium battery negative electrode collecting column and manufacturing method thereof | |
| CN114214494A (en) | Surface grain boundary engineering treatment method for corrosion resistance of stainless steel | |
| CN115679230B (en) | Surface treatment process for improving hydrogen embrittlement resistance of nickel-based corrosion-resistant alloy | |
| CN110484702B (en) | Heat treatment method for realizing grain boundary sawtooth of iron-nickel-based alloy | |
| ZHENG et al. | Microstructure and mechanical properties of Al–Zn–Mg–Cu (7075) alloy tubes prepared via power stagger spinning | |
| CN117025937A (en) | Laser impact method for improving creep deformation cooperative manufacturing capability of thin-wall aluminum-lithium alloy | |
| CN109182906A (en) | A kind of high temperature resistance and high strength nut and its production method | |
| CN115121993A (en) | Preparation method of high-performance nickel-based alloy welding wire | |
| CN113025933B (en) | Intermetallic compound toughened heterostructure zirconium alloy and preparation method thereof | |
| CN107740002A (en) | A kind of novel control nitrogen austenitic stainless steel and preparation method thereof | |
| CN111910138A (en) | Step-by-step thermal mechanical treatment process for casting aluminum-silicon alloy | |
| CN115255234B (en) | Titanium material forging processing technology and application thereof in core component of new energy lithium battery equipment | |
| CN115927973B (en) | Martensitic stainless steel and preparation method and application thereof | |
| WO2024080326A1 (en) | Method for manufacturing high-strength component having exceptional resistance to hydrogen embrittlement | |
| RU2797390C1 (en) | Super-thick steel sheet for a vessel with good impact strength at low temperatures in the middle and its manufacturing method | |
| Logakannan et al. | Effect of Strain Rate on Tensile and Fracture Behavior of Ultrafine grained Al6061 processed through Cryorolling and Warm rolling | |
| Verma et al. | A Comparative Study of Various Methods for Improving the Properties of Cantor Alloy (CoCrFeMnNi High Entropy Alloy) |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |