CN113249634A - Stainless steel and method for producing formed article thereof - Google Patents
Stainless steel and method for producing formed article thereof Download PDFInfo
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- CN113249634A CN113249634A CN202110462691.7A CN202110462691A CN113249634A CN 113249634 A CN113249634 A CN 113249634A CN 202110462691 A CN202110462691 A CN 202110462691A CN 113249634 A CN113249634 A CN 113249634A
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- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 86
- 239000010935 stainless steel Substances 0.000 title claims abstract description 86
- 238000004519 manufacturing process Methods 0.000 title claims description 10
- 239000000843 powder Substances 0.000 claims abstract description 48
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims abstract description 21
- 229910000420 cerium oxide Inorganic materials 0.000 claims abstract description 21
- 238000002844 melting Methods 0.000 claims abstract description 21
- 230000008018 melting Effects 0.000 claims abstract description 21
- 238000000034 method Methods 0.000 claims abstract description 21
- BMMGVYCKOGBVEV-UHFFFAOYSA-N oxo(oxoceriooxy)cerium Chemical compound [Ce]=O.O=[Ce]=O BMMGVYCKOGBVEV-UHFFFAOYSA-N 0.000 claims abstract description 21
- 239000000919 ceramic Substances 0.000 claims abstract description 17
- 230000008569 process Effects 0.000 claims abstract description 15
- 229910052582 BN Inorganic materials 0.000 claims abstract description 13
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 claims abstract description 13
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims abstract description 12
- 239000007789 gas Substances 0.000 claims abstract description 10
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 10
- 239000011159 matrix material Substances 0.000 claims abstract description 9
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 14
- 239000002245 particle Substances 0.000 claims description 11
- 238000000498 ball milling Methods 0.000 claims description 10
- 238000002156 mixing Methods 0.000 claims description 9
- 229910052786 argon Inorganic materials 0.000 claims description 7
- 239000002131 composite material Substances 0.000 claims description 7
- 239000000463 material Substances 0.000 claims description 4
- 238000001035 drying Methods 0.000 claims description 3
- 238000005303 weighing Methods 0.000 claims description 3
- 229910001873 dinitrogen Inorganic materials 0.000 claims 1
- 238000005260 corrosion Methods 0.000 abstract description 23
- 230000007797 corrosion Effects 0.000 abstract description 22
- 238000002360 preparation method Methods 0.000 abstract description 6
- 238000001556 precipitation Methods 0.000 abstract description 4
- 238000005204 segregation Methods 0.000 abstract description 4
- 238000010309 melting process Methods 0.000 abstract description 3
- 238000011065 in-situ storage Methods 0.000 abstract description 2
- 239000000155 melt Substances 0.000 abstract description 2
- 238000005728 strengthening Methods 0.000 abstract description 2
- 238000004781 supercooling Methods 0.000 abstract description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 12
- 238000012876 topography Methods 0.000 description 9
- 238000007654 immersion Methods 0.000 description 8
- 230000000694 effects Effects 0.000 description 6
- 239000013078 crystal Substances 0.000 description 5
- 238000005516 engineering process Methods 0.000 description 5
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 4
- 238000000576 coating method Methods 0.000 description 4
- 230000006911 nucleation Effects 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 150000004767 nitrides Chemical class 0.000 description 3
- 238000010899 nucleation Methods 0.000 description 3
- 238000002161 passivation Methods 0.000 description 3
- 230000010287 polarization Effects 0.000 description 3
- 229910001404 rare earth metal oxide Inorganic materials 0.000 description 3
- 238000002791 soaking Methods 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 229910002092 carbon dioxide Inorganic materials 0.000 description 2
- 239000001569 carbon dioxide Substances 0.000 description 2
- 239000000460 chlorine Substances 0.000 description 2
- 229910052801 chlorine Inorganic materials 0.000 description 2
- 239000011248 coating agent Substances 0.000 description 2
- 239000006185 dispersion Substances 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 230000003014 reinforcing effect Effects 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 230000009471 action Effects 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910000422 cerium(IV) oxide Inorganic materials 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000000178 monomer Substances 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 238000000746 purification Methods 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 229910001256 stainless steel alloy Inorganic materials 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0207—Using a mixture of prealloyed powders or a master alloy
- C22C33/0228—Using a mixture of prealloyed powders or a master alloy comprising other non-metallic compounds or more than 5% of graphite
-
- B22F1/0003—
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y10/00—Processes of additive manufacturing
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y70/00—Materials specially adapted for additive manufacturing
- B33Y70/10—Composites of different types of material, e.g. mixtures of ceramics and polymers or mixtures of metals and biomaterials
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Manufacturing & Machinery (AREA)
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- Civil Engineering (AREA)
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- Structural Engineering (AREA)
- Mechanical Engineering (AREA)
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Abstract
The invention discloses stainless steel and a preparation method of a formed piece thereof, wherein the stainless steel takes 316L stainless steel as a matrix, and cerium oxide and boron nitride ceramic phases are dispersed and distributed in the matrix. The cerium oxide and the boron nitride ceramic phase effectively inhibit the grain boundary segregation of Cr element, hinder the precipitation of a second phase, and improve the intergranular corrosion resistance of the stainless steel. The preparation method utilizes a selective laser melting forming process to prepare a stainless steel forming piece, and nitrogen in a mixed gas atmosphere reacts with boron powder in a powder melting process to generate a boron nitride ceramic phase in situ. The supercooling degree of the melt in the selective laser melting process is extremely high, and the formed part has fine and smooth tissue and plays a role in fine grain strengthening.
Description
Technical Field
The invention relates to stainless steel and a preparation method of a formed part thereof, in particular to stainless steel with corrosion resistance enhanced by cooperation of rare earth oxide/nitride ceramic reinforced phase and a method for preparing the formed part of the stainless steel by adopting a selective laser melting forming technology.
Background
The stainless steel has excellent mechanical property, certain corrosion resistance and wide application range, and plays an important role in life. For example, 2-3% of Mo element is added into 316L stainless steel widely applied in the chemical industry, and the steel has excellent pitting corrosion resistance due to the proper Mo content. However, in the practical production and application process, the corrosion failure problem of the stainless steel is common, and the corrosion resistance of the 316L stainless steel is found to be rapidly deteriorated in the high-temperature high-chlorine carbon dioxide-containing environment. There is therefore still a need to develop various means for improving the corrosion resistance of stainless steel.
At present, the method for enhancing the corrosion resistance of stainless steel comprises the following steps: surface coating methods, surface high energy bombardment methods, alloying in stainless steel, and the like. The surface coating method is most common to form a ceramic reinforced coating on the surface of stainless steel by sintering and remelting, but has the problem that the coating is easy to peel off and fail. The surface high-energy bombardment technology can form a stable and compact passive film on the surface of the stainless steel, but leaves high residual compressive stress on the surface of the stainless steel, thereby limiting the use scene of the stainless steel. The addition of Mo, Ti and other alloy elements into stainless steel can improve the electrode potential of the stainless steel and improve the intergranular corrosion resistance of the stainless steel, but the stainless steel becomes brittle and has reduced mechanical properties.
Disclosure of Invention
The purpose of the invention is as follows: aiming at the problem that the corrosion resistance of 316L stainless steel is poor in a high-temperature high-chlorine carbon dioxide-containing environment, the invention provides stainless steel which has more excellent corrosion resistance than 316L stainless steel.
Another object of the present invention is to provide a method for producing a formed article of the above stainless steel.
The technical scheme is as follows: the stainless steel provided by the invention takes 316L stainless steel as a matrix, and cerium oxide and boron nitride ceramic phases are dispersed and distributed in the matrix.
The melting point of cerium oxide and boron nitride ceramic phase in the stainless steel is far higher than that of 316L stainless steel, and cerium oxide particles and boron nitride ceramic phase which are dispersed can become nucleation centers, so that the dispersion strengthening effect is achieved while the grain boundary segregation of Cr is inhibited, the precipitation of a second phase is inhibited, and the intergranular corrosion resistance of the stainless steel is improved.
The method for preparing the formed piece of the stainless steel comprises the following steps:
(1) weighing 0.59-1.25% of nano cerium oxide powder, 0.039-0.11% of boron powder and the balance of 316L stainless steel powder by mass fraction, and drying;
(2) uniformly mixing nano cerium oxide powder, boron powder and 316L stainless steel powder by using a low-speed ball milling powder mixing process to obtain composite material powder;
(3) and melting and forming the composite material powder by adopting a selective laser melting and forming process under the atmosphere of mixed gas of argon and nitrogen to obtain a stainless steel formed part.
In summary, the preparation method is mainly to form a formed piece with a complex structure by uniformly mixing nano cerium oxide powder, boron powder and 316L stainless steel powder through a selective laser melting forming technology.
The mechanism of the preparation process is as follows: because the three kinds of powder particles are extremely fine and reach micron or even nanometer level, agglomeration phenomenon can occur even if the powder particles have slight moisture, and the powder to be weighed is dried firstly. Then, the even distribution of the nano cerium oxide powder and the boron powder in 316L stainless steel powder is realized by a low-speed ball milling powder mixing process, and the full dispersion distribution of the nano cerium oxide powder and the boron nitride ceramic phase in the prepared stainless steel is ensured. Under the mixed gas atmosphere of argon and nitrogen, a selective laser melting forming technology is adopted, in the melting forming process, the dispersed and distributed monomer boron powder can react with nitrogen under the action of laser to generate a boron nitride ceramic phase in situ, and the boron nitride ceramic phase and cerium oxide jointly inhibit the grain boundary segregation of Cr element and the precipitation of a second phase, so that the intergranular corrosion resistance of stainless steel is improved, crystal grains are refined, and the mechanical property of the stainless steel is maintained.
Specifically, the particle size of the 316L stainless steel powder is 15-65 μm. The 316L stainless steel powder is controlled within the grain size range, so that the effect of forming a nucleation center in a steel matrix by cerium oxide particles and boron nitride ceramic is ensured, and the tissue uniformity and the grain size of the stainless steel prepared by the preparation method are fully ensured.
Further, D of the 316L stainless steel powder50The particle size is 33 to 34 μm, and the powder has a particle size within the above range, and the above effect is more excellent.
In the step (2), the low-speed ball milling and powder mixing process is carried out in a centrifugal planetary ball mill, the ball-material ratio is 3: 1-8: 1, and the ball milling speed is 100-200 rpm/min. The low-speed ball milling is carried out under the parameters, the grinding effect on the powder particles is not pursued, and the three kinds of powder are mainly mixed uniformly.
In the step (3), the volume flow ratio of argon to nitrogen in the mixed gas is 8: 1-19: 1. By adding a proper amount of nitrogen in the protective gas atmosphere, the reaction of boron powder and nitrogen is effectively promoted, and the formation of a boron nitride ceramic phase on the molten stainless steel powder piece is promoted.
In the step (3), the laser power of the selective laser melting forming process is controlled to be 200-350W, and the scanning speed is controlled to be 1000-2500 mm/s.
The scanning interval of the selective laser melting forming process is 50-80 mu m.
Has the advantages that: compared with the prior art, the cerium oxide and the boron nitride ceramic phase are dispersed in the 316L stainless steel matrix, so that the grain boundary segregation of the Cr element is effectively inhibited, the precipitation of a second phase is hindered, the intergranular corrosion resistance of the stainless steel is improved, the purification effect of the cerium oxide on the grain boundary is fully utilized, and the corrosion resistance of the stainless steel is improved to a certain extent. Meanwhile, the rare earth oxide cerium oxide and the nitride ceramic reinforcing phase have higher melting points than the stainless steel powder and can be dispersedly distributed in the stainless steel matrix, so that nucleation mass points are provided for the solidification of the alloy, the minimum nucleation work is reduced, and the grain size of 316L stainless steel is further reduced. In addition, the supercooling degree of the melt in the selective laser melting process is extremely high, and the formed part has fine and smooth tissue and plays a role in fine grain reinforcement. The maximum resistance value of the stainless steel passive film2.02E+5Ω·cm2And the corrosion resistance is more excellent than that of rolled 316L stainless steel.
Drawings
FIG. 1 is a tissue topography of example 1;
FIG. 2 is a tissue topography map of example 2;
FIG. 3 is a tissue topography of example 3;
FIG. 4 is a tissue topography map of example 4;
FIG. 5 is a tissue topography of example 5;
FIG. 6 is a topographical view of the tissue of example 6;
FIG. 7 is a topographical view of the tissue of example 7;
FIG. 8 is a tissue topography map of example 8;
FIG. 9 is the tissue topography of example 9;
FIG. 10 is the tissue topography of example 10;
FIG. 11 is the topographic tissue map of example 11;
FIG. 12 is the tissue topography of example 12;
FIG. 13 is a comparative schematic of potentiodynamic polarization curves of examples 1, 2, 3, 4 after 72h of oilfield produced water immersion;
FIG. 14 is a comparative schematic of potentiodynamic polarization curves of examples 5, 6, 7, 8 after 72h of oilfield produced water immersion;
FIG. 15 is a comparative schematic of potentiodynamic polarization curves of examples 9, 10, 11, 12 after 72h of oilfield produced water immersion;
FIG. 16 is a graph of phase angle versus frequency for examples 1, 2, 3, and 4 after 72h of soaking in oilfield produced water;
FIG. 17 is a graph of amplitude versus frequency for examples 1, 2, 3, and 4 after 72h of oilfield produced water immersion;
FIG. 18 is a graph of phase angle versus frequency for examples 5, 6, 7, and 8 after 72h of soaking in oilfield produced water;
FIG. 19 is a graph of amplitude versus frequency for examples 5, 6, 7, and 8 after 72h of immersion in oilfield produced water;
FIG. 20 is a graph of phase angle versus frequency for examples 9, 10, 11, 12 after 72h of soaking in oilfield produced water;
FIG. 21 is a graph of amplitude versus frequency for examples 9, 10, 11, 12 after 72h of immersion in oilfield produced water;
FIG. 22 is a Nyquist plot of examples 1, 2, 3, 4 after 72h of oilfield produced water immersion;
FIG. 23 is a Nyquist plot of examples 5, 6, 7, 8 after 72h of oilfield produced water immersion;
FIG. 24 is a Nyquist plot of examples 9, 10, 11, 12 after 72h of oilfield produced water soak.
Detailed Description
Based on the requirement of the corrosion resistance of 316L stainless steel, the invention utilizes a selective laser melting and forming technology to melt stainless steel alloy composite material powder by high-energy laser beams and stack the powder layer by layer to prepare the stainless steel with good corrosion resistance and mechanical property and synergistically enhanced rare earth oxide/nitride ceramic reinforcing phase.
The following experimental procedures are provided to further illustrate the present invention.
The equipment adopted in the test comprises an analytical balance, an oven, a centrifugal planetary ball mill, a selective laser melting and forming device, an electrochemical workstation and a scanning electron microscope.
Specifically, in example 1, 1.5g of nano cerium oxide powder, 0.1072g of boron powder and 150g of 316L stainless steel powder were used. Wherein the particle size of 316L stainless steel powder is 15-65 μm, and D50Mixing at low speed of centrifugal planetary ball mill (33.4 μm) at 200rpm/min, and ball-to-material ratio of 5: 1. And (2) forming the composite material powder by adopting a selective laser melting forming process under the atmosphere of argon and nitrogen mixed gas with a volume flow ratio of 10:1 to obtain a stainless steel formed part, wherein the laser power is 200W, the scanning speed is set to be 1000mm/s, and the scanning pitch is set to be 60 mu m.
Example 5 is different from example 1 in that the power of the laser was set to 250W and the scanning rate was set to 1000 mm/s.
Example 6 is different from example 5 in that the scanning rate was set to 1500 mm/s.
Example 7 is different from example 5 in that the scanning rate was set to 2000 mm/s.
Example 8 is different from example 5 in that the scanning rate was set to 2500 mm/s.
Example 9 is different from example 1 in that the power of the laser was set to 275W and the scanning pitch was set to 50 μm.
Example 10 is different from example 1 in that the scanning pitch is set to 60 μm.
Example 11 is different from example 1 in that the scanning pitch is set to 70 μm.
Example 12 is different from example 1 in that the scanning pitch is set to 80 μm.
Through performance tests, stainless steel with good corrosion resistance is obtained in examples 1 to 12. As shown in fig. 1 to 12, it can be seen that the columnar grain size of the stainless steel samples of all examples is fine. Analysis of the test results revealed that as the laser power was increased, the temperature of the molten pool increased, the cooling rate decreased, and the crystal grain size gradually increased. As the laser scanning rate increases, the cooling rate increases, resulting in BN/CeO2The grain size of the reinforced stainless steel gradually decreases. When the laser scanning distance is increased, the temperature of a molten pool is reduced, the cooling rate is increased, the G/R value is reduced, the columnar crystal structure in the crystal grains is increased, and the crystal grain size is reduced.
From FIGS. 13-15, it can be seen that the stainless steel obtained in the three examples has a passivation region, wherein the self-corrosion current density of the stainless steel under the parameters of example 1 is 9.13E-6A cm-2The passivation interval is 1.296mV at most, and the corrosion rate of the passivation film is slowest. As can be seen from FIGS. 16 to 24, the stainless steel obtained in example 12 had a capacitive arc size of 1.07E + 4. omega. cm at the maximum2And the corrosion resistance is more excellent.
In addition, the mass fraction of the nano cerium oxide powder is 0.9-1.9 g and the mass fraction of the boron powder is 0.06-0.16 g based on 150g of 316L stainless steel powder. Respectively weighing 0.9g, 1.0g and,1.3g, 1.6g and 1.9g of nano cerium oxide powder, 0.06g, 0.08g, 0.09g, 0.12g and 0.16g of boron powder, and preparing a plurality of combination ratios, and drying for later use to verify whether the technical scheme of the invention can achieve the target effect. Then, for each group of mixture ratio, a centrifugal planetary ball mill is used for carrying out low-speed ball milling at the ball milling speed of 100-200 rpm/min, the ball-material ratio is randomly selected from 3: 1-8: 1, and the three kinds of powder are uniformly mixed. Melting the powder by adopting selective laser melting forming equipment under the atmosphere of mixed gas of argon and nitrogen with the volume flow ratio of 8:1, 9:1, 12:1, 16:1 and 19:1, wherein the laser power is controlled to be 200-350W, the scanning speed is controlled to be 1500-2500 mm/s, and the scanning distance is set to be 50-80 mu m. And melting and forming the composite material powder in each component ratio to obtain a stainless steel formed part. And then testing the prepared stainless steel forming piece by adopting equipment such as an electrochemical workstation, a scanning electron microscope and the like. The obtained results show that the stainless steel obtained by the technical scheme of the invention has excellent corrosion resistance, wherein the resistance value of the passive film of the stainless steel can reach 2.02E +5 omega cm to the maximum2。
Claims (8)
1. The stainless steel is characterized in that 316L stainless steel is used as a matrix, and cerium oxide and boron nitride ceramic phases are dispersed and distributed in the matrix.
2. A method for producing a shaped article of the stainless steel according to claim 1, comprising the steps of:
(1) weighing 0.59-1.25% of nano cerium oxide powder, 0.039-0.11% of boron powder and the balance of 316L stainless steel powder by mass fraction, and drying;
(2) uniformly mixing nano cerium oxide powder, boron powder and 316L stainless steel powder by using a low-speed ball milling powder mixing process to obtain composite material powder;
(3) and melting and forming the composite material powder by adopting a selective laser melting and forming process under the atmosphere of mixed gas of argon and nitrogen to obtain a stainless steel formed part.
3. The method for producing a shaped article of stainless steel according to claim 2, wherein the 316L stainless steel powder has a particle diameter of 15 to 65 μm.
4. The method of manufacturing a shaped article of stainless steel according to claim 3, wherein D of the 316L stainless steel powder is D50The particle size is 33 to 34 μm.
5. The method for preparing a shaped piece of stainless steel according to claim 2, wherein in the step (2), the low-speed ball milling and powder mixing process is performed in a centrifugal planetary ball mill, the ball-to-material ratio is 3: 1-8: 1, and the ball milling speed is 100-200 rpm/min.
6. The method for producing a shaped article of stainless steel according to claim 2, wherein in the step (3), the volume flow ratio of argon gas and nitrogen gas of the mixed gas is 8:1 to 19: 1.
7. The method for manufacturing a shaped article of stainless steel according to claim 2, wherein in the step (3), the laser power of the selective laser melting and forming process is controlled to 200 to 350W, and the scanning speed is controlled to 1000 to 2500 mm/s.
8. The method for producing a shaped article of stainless steel according to claim 7, wherein a scanning pitch of the selective laser melting forming process is 50 to 80 μm.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114226753A (en) * | 2021-12-14 | 2022-03-25 | 华中科技大学 | Boron nitride in-situ composite reinforced metal additive integrated manufacturing method |
| WO2024060607A1 (en) * | 2022-09-21 | 2024-03-28 | 华北理工大学 | Method for preparing high-nitrogen stainless steel by selective laser melting of pure metal prepared powder |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5289509A (en) * | 1976-01-23 | 1977-07-27 | Mitsubishi Metal Corp | Wear-resistant composite materials |
| CN110382138A (en) * | 2017-01-06 | 2019-10-25 | 通用电气公司 | For the nucleocapsid alloy powder of increasing material manufacturing, increasing material manufacturing method and the precipitate dispersions of increasing material manufacturing reinforced alloys component |
| CN110578141A (en) * | 2019-09-30 | 2019-12-17 | 辽宁科技大学 | Method for improving surface corrosion resistance of 316L stainless steel by laser cladding technology |
-
2021
- 2021-04-27 CN CN202110462691.7A patent/CN113249634A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5289509A (en) * | 1976-01-23 | 1977-07-27 | Mitsubishi Metal Corp | Wear-resistant composite materials |
| CN110382138A (en) * | 2017-01-06 | 2019-10-25 | 通用电气公司 | For the nucleocapsid alloy powder of increasing material manufacturing, increasing material manufacturing method and the precipitate dispersions of increasing material manufacturing reinforced alloys component |
| CN110578141A (en) * | 2019-09-30 | 2019-12-17 | 辽宁科技大学 | Method for improving surface corrosion resistance of 316L stainless steel by laser cladding technology |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114226753A (en) * | 2021-12-14 | 2022-03-25 | 华中科技大学 | Boron nitride in-situ composite reinforced metal additive integrated manufacturing method |
| CN114226753B (en) * | 2021-12-14 | 2023-02-10 | 华中科技大学 | Boron nitride in-situ composite reinforced metal additive integrated manufacturing method |
| WO2024060607A1 (en) * | 2022-09-21 | 2024-03-28 | 华北理工大学 | Method for preparing high-nitrogen stainless steel by selective laser melting of pure metal prepared powder |
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