CN115029646B - Ultra-high strength stainless steel manufactured by additive - Google Patents
Ultra-high strength stainless steel manufactured by additive Download PDFInfo
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- CN115029646B CN115029646B CN202210565963.0A CN202210565963A CN115029646B CN 115029646 B CN115029646 B CN 115029646B CN 202210565963 A CN202210565963 A CN 202210565963A CN 115029646 B CN115029646 B CN 115029646B
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- 239000000654 additive Substances 0.000 title claims abstract description 115
- 230000000996 additive effect Effects 0.000 title claims abstract description 115
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 81
- 239000010935 stainless steel Substances 0.000 title claims abstract description 77
- 238000004519 manufacturing process Methods 0.000 claims abstract description 104
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 98
- 239000000843 powder Substances 0.000 claims abstract description 54
- 229910052742 iron Inorganic materials 0.000 claims abstract description 41
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 40
- 239000000956 alloy Substances 0.000 claims abstract description 40
- 238000002844 melting Methods 0.000 claims description 64
- 230000008018 melting Effects 0.000 claims description 64
- 239000002245 particle Substances 0.000 claims description 3
- 229910001566 austenite Inorganic materials 0.000 abstract description 32
- 239000000463 material Substances 0.000 abstract description 13
- 229910052804 chromium Inorganic materials 0.000 abstract description 3
- 230000000052 comparative effect Effects 0.000 description 36
- 230000000694 effects Effects 0.000 description 17
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 14
- 229910000734 martensite Inorganic materials 0.000 description 12
- 230000000087 stabilizing effect Effects 0.000 description 11
- 238000010146 3D printing Methods 0.000 description 7
- 239000011159 matrix material Substances 0.000 description 7
- 230000009466 transformation Effects 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 6
- 230000007547 defect Effects 0.000 description 6
- 238000012360 testing method Methods 0.000 description 5
- 238000009826 distribution Methods 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 238000004881 precipitation hardening Methods 0.000 description 4
- 238000010586 diagram Methods 0.000 description 3
- 229910001105 martensitic stainless steel Inorganic materials 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 238000002360 preparation method Methods 0.000 description 3
- 238000007639 printing Methods 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 230000007480 spreading Effects 0.000 description 3
- 238000003892 spreading Methods 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 238000002441 X-ray diffraction Methods 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 230000000717 retained effect Effects 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 238000012876 topography Methods 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- 229910000883 Ti6Al4V Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000003153 chemical reaction reagent Substances 0.000 description 1
- 238000011960 computer-aided design Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000008034 disappearance Effects 0.000 description 1
- 239000005457 ice water Substances 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/20—Direct sintering or melting
- B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- 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
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
The invention discloses an additive manufactured ultrahigh-strength stainless steel, which is manufactured by adopting iron-based alloy powder through additive manufacturing, wherein the iron-based alloy powder comprises the following elemental components in percentage by mass: c:0.1% -0.6%, cr:10% -20%, mn:0.1% -2%, si:0.2% -1.5%, ni:0.5% -10.0%, nb:0.01-0.1%, mo:0.05% -0.6% and the balance of Fe. According to the invention, C, ni and Cr elements are added into the iron-based alloy powder, and the corresponding dosage is adjusted to stabilize austenite in the ultra-high strength stainless steel material, so that the prepared ultra-high strength stainless steel has the ultra-high tensile strength and excellent plasticity, wherein the tensile strength of the prepared ultra-high strength stainless steel is up to 1550MPa, and the elongation is up to 19.1%; meanwhile, the iron-based alloy powder for preparing the ultra-high strength stainless steel has the advantages of simple components, low cost and wide application prospect.
Description
Technical Field
The invention belongs to the technical field of additive manufacturing metal materials, and particularly relates to ultra-high strength stainless steel for additive manufacturing.
Background
In recent years, the selective laser melting additive manufacturing (also called 3D printing) technology adopts layer-by-layer powder-laying selective laser melting, so that a computer-aided design can be adopted to form complex parts, and the high-speed heating and cooling can refine the formed material structure, and the technology is widely applied to the forming preparation of metal parts such as stainless steel, titanium alloy, aluminum alloy and the like, wherein the most printed stainless steel has 316L, 17-4PH and 15-5PH precipitation hardening (precipitation hardening (PH)) stainless steel, the strength of the 316L after the selective laser melting additive manufacturing is about 600MPa, and the total extension is about 30-50% (Y.M.Wang, T.Voisin, J.T.McKeown, J.Ye, N.P.Calta, Z.Li, Z.Zeng, Y.Zhang, W.Chen, T.T.Roehling, additively manufactured hierarchical stainless steels with high strength and ductility, nature materials 17 (1) (2018)) and the technology is mainly applied to the production of parts with lower strength level requirements. Additive manufacturing 17-4PH and 15-5PH stainless steels have improved strength, mainly through precipitation hardening, tensile strength after additive forming and subsequent heat treatment reaches above 1000MPa (1000-1450), elongation about 12-15%, but strength levels are still lower (T.LeBrun, T.Nakamoto, K.Horikawa, H.Kobayashi, effect of retained austenite on subsequent thermal processing and resultant mechanical properties of selective laser melted-4PH stainless steel,Materials&Design 81 (2015) 44-53.H.K.Rafi,T.L.Starr,B.E.Stucker,A comparison of the tensile,fatigue,and fracture behavior of Ti-6Al-4V and 15-5PH stainless steel parts made by selective laser melting,The International Journal of Advanced Manufacturing Technology 69 (5) (2013) 1299-1309.T.Debroy,H.L.Wei,J.S.Zuback,T.Mukherjee,J.W.Elmer,J.O.Milewski,A.M.Beese,A.E.Wilsonheid,A.De,W.Zhang,Additive manufacturing of metallic components-Process, structure and properties, prog. Mater Sci.92 (2018) 112-224). So that the application of the conventionally used stainless steel under the condition of severe strength requirements is limited.
In order to solve the problems, in the Chinese patent invention patent No. 202110755596.6 published in the prior art, an iron-based alloy powder for additive manufacturing, an application thereof and ultra-high strength steel for additive manufacturing are disclosed, wherein the iron-based alloy powder for additive manufacturing comprises the following chemical components in percentage by mass: c:0.20% -0.45%, ni:2.12% -9.65%, mn:0.25% -2.45%, si:0.21% -1.45%, cr:0.45% -1.45%, mo:0.15% -1.15%, V:0.11% -1.15% and the balance of Fe. The iron-based alloy powder for additive manufacturing adopts the proportion, is used for preparing the ultra-high strength steel by additive manufacturing, can further improve the plasticity and impact toughness of the ultra-high strength steel, has no crack defect, and the tensile strength of the manufactured ultra-high strength steel can reach 1900MPa, but the elongation rate is only 12.5%. In the Chinese patent No. 202011397712.3, an improvement of 0Cr is disclosed 16 Ni 5 Mo 1 Heat treatment method for toughness and plasticity of martensitic stainless steel, 0Cr in the invention 16 Ni 5 Mo 1 The martensitic stainless steel comprises the following elements in percentage by massThe amount is as follows: c: less than or equal to 0.07 percent, cr:15.00-17.00%, ni:3.50-5.00%, mo:0.70-1.50%, si: less than or equal to 1.00 percent, mn: less than or equal to 1.50 percent, P: less than or equal to 0.035 percent, S: less than or equal to 0.025 percent, cu: less than or equal to 0.35 percent, sn: less than or equal to 0.03 percent, and the balance of Fe and unavoidable impurity elements. The invention reduces the quenching termination temperature, and adds an ice-water mixture cold treatment step with low cost and convenient operation, which can effectively refine grains and basically eliminate residual austenite after quenching. After the 0Cr16Ni5Mo1 martensitic stainless steel is subjected to heat treatment, the strength of the material completely reaches the standard, the yield strength is more than or equal to 850MPa, the toughness and plasticity are effectively improved, the elongation is more than or equal to 16%, and the tensile strength cannot reach 1000MPa.
In summary, the ultra-high strength steel manufactured by additive in the prior art can achieve the effects of high tensile strength and high elongation, but has low elongation when meeting the high tensile strength, but cannot achieve the high tensile strength when meeting the high elongation. Therefore, how to prepare the ultra-high strength steel meeting both high tensile strength (tensile strength is more than 1500 MPa) and high elongation (elongation is more than 15%) is a technical problem to be solved.
Disclosure of Invention
Aiming at the technical problems that the additive manufacturing stainless steel in the prior art can not simultaneously meet the high tensile strength and the high elongation; the technical effect that the strength of the ultra-high strength stainless steel is more than 1500MPa and the elongation is more than 15% is achieved by the ultra-high strength stainless steel manufactured by additive.
In order to achieve the above purpose, the invention adopts the following technical scheme:
an additively manufactured ultra-high strength stainless steel, the ultra-high strength stainless steel being manufactured by additive manufacturing using an iron-based alloy powder, the iron-based alloy powder comprising the following elemental components in percentage by mass: c:0.1% -0.6%, cr:10% -20%, mn:0.1% -2%, si:0.2% -1.5%, ni:0.5% -10.0%, nb:0.01-0.1%, mo:0.05% -0.6% and the balance of Fe.
According to the invention, C, ni and Cr elements are added into the iron-based alloy powder, and the corresponding dosage is adjusted to achieve the effect of stabilizing austenite in the ultra-high strength stainless steel material, and the Cr element has the effect of stabilizing austenite and also has the effect of improving corrosion resistance. According to the invention, a large amount of Cr elements are added to improve the corrosion resistance of the material and stabilize austenite in the material, and the Cr elements are matched with other two austenite stabilizing elements C and Ni to be used, so that the material obtains a microstructure containing a large amount of residual austenite, the microstructure of the ultra-high strength stainless steel manufactured by additive manufacturing is an austenite and martensite double-phase matrix structure, the volume fraction of the residual austenite in the double-phase matrix structure is 50% -60%, and the residual austenite in the double-phase matrix structure can generate a transformation induced plasticity effect through transformation to martensite, so that the ultra-high strength stainless steel manufactured by the additive manufacturing has excellent plasticity; thereby achieving the effect of excellent plasticity while the ultra-high strength stainless steel has ultra-high tensile strength.
As a preferred technical scheme of the invention, the iron-based alloy powder comprises the following element components in percentage by mass: c:0.15% -0.45%, cr:12% -18%, mn:0.1% -0.5%, si:0.3% -0.9%, ni:1.2% -6.8%, nb:0.02-0.07%, mo:0.1% -0.55% and the balance of Fe.
As a preferred technical scheme of the invention, the iron-based alloy powder comprises the following element components in percentage by mass: c:0.38%, cr:13%, mn:0.30%, si:0.68%, ni:2.5%, nb:0.04%, mo:0.5%, the balance being Fe.
As a preferred technical scheme of the invention, the iron-based alloy powder comprises the following element components in percentage by mass: c:0.25%, cr:16%, mn:0.33%, si:0.70%, ni:4.8%, nb:0.04%, mo:0.5%, the balance being Fe.
As a preferred technical scheme of the invention, the iron-based alloy powder comprises the following element components in percentage by mass: c:0.16%, cr:18%, mn:0.35%, si:0.72%, ni:6.5%, nb:0.03%, mo:0.5%, the balance being Fe.
As a preferred embodiment of the present invention, the particle size of the iron-based alloy powder is between 15 and 53. Mu.m.
As a preferred embodiment of the present invention, the additive manufacturing is selective laser melting additive manufacturing.
As a preferred technical scheme of the invention, the laser power of the selective laser melting additive manufacturing is 160-180W.
As a preferred technical scheme of the invention, the scanning speed of the selective laser melting additive manufacturing is one of 800mm/s, 850mm/s, 900mm/s, 950mm/s, 1000mm/s, 1050mm/s, 1100mm/s, 1150mm/s or 1200 mm/s.
As a preferable technical scheme of the invention, the scanning interval of the selective laser melting additive manufacturing is 0.08mm, and the powder laying thickness of the selective laser melting additive manufacturing is 0.03mm.
The beneficial effects of the invention are as follows:
the ultra-high strength stainless steel has excellent plasticity while having ultra-high strength tensile property, wherein the tensile strength is up to 1550MPa, and the elongation is up to 19.1%; meanwhile, the iron-based alloy powder for preparing the ultra-high strength stainless steel has the advantages of simple components, low cost and wide application prospect.
Drawings
FIG. 1 is a morphology diagram of an iron-based alloy stainless powder of example 2 of the present invention;
FIG. 2 is a comparative distribution diagram of example 1 and comparative example 1 of the present invention;
FIG. 3 is a comparative graph showing the distribution of defects in the internal pores of the printed samples of example 2 and comparative example 2 according to the present invention;
FIG. 4 is a scanning electron microscope topography of the ultra-high strength steel of example 2 of the present invention;
FIG. 5 is a graph showing the result of X-ray diffraction of retained austenite in the ultra-high-strength steel according to example 2 of the present invention;
FIG. 6 is a graph of tensile stress strain for inventive example 1, example 2, comparative example 1, comparative example 2, and additive manufactured 17-4PH stainless steel.
Detailed Description
The embodiment of the application solves the problem that the stainless steel manufactured by the additive cannot meet the requirements of high tensile strength and high elongation simultaneously in the prior art by providing the ultra-high-strength stainless steel manufactured by the additive.
In order to solve the technical problems, the embodiment of the application adopts the following general ideas:
according to the invention, C, ni and Cr elements are added into the iron-based alloy powder, and the corresponding dosage is adjusted to achieve the effect of stabilizing austenite in the ultra-high strength stainless steel material, and the Cr element has the effect of stabilizing austenite and also has the effect of improving corrosion resistance. According to the invention, a large amount of Cr elements are added to improve the corrosion resistance of the material and stabilize austenite in the material, and the Cr elements are matched with other two austenite stabilizing elements C and Ni to be used, so that the material obtains a microstructure containing a large amount of residual austenite, the microstructure of the ultra-high strength stainless steel manufactured by additive manufacturing is an austenite and martensite double-phase matrix structure, the volume fraction of the residual austenite in the double-phase matrix structure is 50% -60%, and the residual austenite of the double-phase matrix structure can generate a transformation induced plasticity effect through transformation from the residual austenite to martensite, so that the ultra-high strength stainless steel manufactured by the additive manufacturing has excellent plasticity; thereby achieving the effect of excellent plasticity while the ultra-high strength stainless steel has ultra-high tensile strength.
In order to make the objects, technical solutions and advantages of the embodiments of the present invention more clear, the technical solutions of the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings of the embodiments of the present invention. It will be apparent that the described embodiments are some, but not all, embodiments of the invention. All other embodiments, which can be made by a person skilled in the art without creative efforts, based on the described embodiments of the present invention fall within the protection scope of the present invention. Unless defined otherwise, technical or scientific terms used herein should be given the ordinary meaning as understood by one of ordinary skill in the art to which this invention belongs. The specific conditions are not noted in the examples and are carried out according to conventional conditions or conditions recommended by the manufacturer. The reagents or apparatus used were conventional products commercially available without the manufacturer's attention.
As used in this specification and the claims, the terms "comprises" and "comprising," and the like, are intended to specify the presence of stated features, integers, steps, operations, elements, and/or components, which are listed thereafter, but do not preclude the presence or addition of one or more other features, integers, steps, operations, elements, components, and/or groups thereof.
The present embodiments 1-3 provide an additively manufactured ultra-high strength stainless steel made via additive manufacturing using an iron-based alloy powder comprising the following elemental components in mass percent: c:0.1% -0.6%, cr:10% -20%, mn:0.1% -2%, si:0.2% -1.5%, ni:0.5% -10.0%, nb:0.01-0.1%, mo:0.05% -0.6% and the balance of Fe.
In order to further improve the strength and plasticity of the ultra-high strength stainless steel in the preparation process, the additive manufacturing is selective laser melting additive manufacturing. The apparatus used for the selective laser melting is a selective laser melting 3D printing apparatus (HBD 100).
Wherein the laser power of the selective laser melting additive manufacturing is 160-180W; the scanning speed of the selective laser melting additive manufacturing is one of 800mm/s, 850mm/s, 900mm/s, 950mm/s, 1000mm/s, 1050mm/s, 1100mm/s, 1150mm/s or 1200 mm/s; the performance of the selective laser melting additive manufacturing for preparing the ultra-high strength stainless steel is greatly affected by printing parameters, so that the selection of proper parameters is also important; the laser power and scanning speed range provided by the invention are used for preparing the ultra-high strength steel in additive manufacturing, and can further improve the strength and plasticity of the ultra-high strength stainless steel.
The scanning interval of the selective laser melting additive manufacturing is 0.08mm, and the powder spreading thickness of the selective laser melting additive manufacturing is 0.03mm; the scanning distance and the powder spreading thickness can also influence the performance of the ultra-high strength stainless steel prepared by selective laser melting additive manufacturing, and the parameters of the scanning distance and the powder spreading thickness provided by the invention are used for preparing the ultra-high strength steel by additive manufacturing, so that the strength and the plasticity of the ultra-high strength stainless steel can be further improved.
Example 1
An additively manufactured ultra-high strength stainless steel, the ultra-high strength stainless steel being manufactured by additive manufacturing using an iron-based alloy powder, the iron-based alloy powder comprising the following elemental components in percentage by mass: c:0.38%, cr:13%, mn:0.30%, si:0.68%, ni:2.5%, nb:0.04%, mo:0.5%, the balance being Fe.
In this embodiment, the additive manufacturing is selective laser melting additive manufacturing. The apparatus used for the selective laser melting is a selective laser melting 3D printing apparatus (HBD 100). The laser power of the selective laser melting additive manufacturing is 180W, the scanning speed of the selective laser melting additive manufacturing is 900mm/s, the scanning interval of the selective laser melting additive manufacturing is 0.08mm, and the powder paving thickness of the selective laser melting additive manufacturing is 0.03mm.
Example 2
An additively manufactured ultra-high strength stainless steel, the ultra-high strength stainless steel being manufactured by additive manufacturing using an iron-based alloy powder, the iron-based alloy powder comprising the following elemental components in percentage by mass: c:0.25%, cr:16%, mn:0.33%, si:0.70%, ni:4.8%, nb:0.04%, mo:0.5%, the balance being Fe.
In this embodiment, the additive manufacturing is selective laser melting additive manufacturing. The apparatus used for the selective laser melting is a selective laser melting 3D printing apparatus (HBD 100). The laser power of the selective laser melting additive manufacturing is 180W, the scanning speed of the selective laser melting additive manufacturing is 1200mm/s, the scanning interval of the selective laser melting additive manufacturing is 0.08mm, and the powder paving thickness of the selective laser melting additive manufacturing is 0.03mm.
Example 3
An additively manufactured ultra-high strength stainless steel, the ultra-high strength stainless steel being manufactured by additive manufacturing using an iron-based alloy powder, the iron-based alloy powder comprising the following elemental components in percentage by mass: c:0.16%, cr:18%, mn:0.35%, si:0.72%, ni:6.5%, nb:0.03%, mo:0.5%, the balance being Fe.
In this embodiment, the additive manufacturing is selective laser melting additive manufacturing. The apparatus used for the selective laser melting is a selective laser melting 3D printing apparatus (HBD 100). The laser power of the selective laser melting additive manufacturing is 180W, the scanning speed of the selective laser melting additive manufacturing is 900mm/s, the scanning interval of the selective laser melting additive manufacturing is 0.08mm, and the powder paving thickness of the selective laser melting additive manufacturing is 0.03mm.
Comparative example 1
An additively manufactured ultra-high strength stainless steel, the ultra-high strength stainless steel being manufactured by additive manufacturing using an iron-based alloy powder, the iron-based alloy powder comprising the following elemental components in percentage by mass: c:0.05%, cr:8.5%, mn:0.35%, si:0.72%, ni:2.5%, nb:0.03%, mo:0.5%, the balance being Fe.
In this comparative example, the additive manufacturing is selective laser melting additive manufacturing. The apparatus used for the selective laser melting is a selective laser melting 3D printing apparatus (HBD 100). The laser power of the selective laser melting additive manufacturing is 180W, the scanning speed of the selective laser melting additive manufacturing is 900mm/s, the scanning interval of the selective laser melting additive manufacturing is 0.08mm, and the powder paving thickness of the selective laser melting additive manufacturing is 0.03mm. And this comparative example was consistent with the additive manufacturing parameter conditions described above for example 1.
Comparative example 2
An additively manufactured ultra-high strength stainless steel, the ultra-high strength stainless steel being manufactured by additive manufacturing using an iron-based alloy powder, the iron-based alloy powder comprising the following elemental components in percentage by mass: c:0.25%, cr:16%, mn:0.33%, si:0.70%, ni:4.8%, nb:0.04%, mo:0.5%, the balance being Fe.
In this comparative example, the additive manufacturing is selective laser melting additive manufacturing. The apparatus used for the selective laser melting is a selective laser melting 3D printing apparatus (HBD 100). The laser power of the selective laser melting additive manufacturing is 120W, the scanning speed of the selective laser melting additive manufacturing is 2000mm/s, the scanning interval of the selective laser melting additive manufacturing is 0.08mm, and the powder paving thickness of the selective laser melting additive manufacturing is 0.03mm.
Performance test comparative test
Comparative test 1
The ultra-high strength stainless steels of the above examples 1 to 3 and comparative examples 1 to 2 were subjected to mechanical properties (room temperature tensile properties) test, and the test results are shown in Table 1 below. (wherein, the shape and size of the stretched samples in each of examples and comparative examples were prepared according to ASTM E8)
Table 1 mechanical properties of ultra-high strength steels produced by additive manufacturing of examples and comparative examples
| Numbering device | Yield strength (MPa) | Tensile strength (MPa) | Total elongation (%) |
| Example 1 | 456 | 1550 | 19.1 |
| Example 2 | 410 | 1530 | 16.7 |
| Example 3 | 415 | 1525 | 18.5 |
| Comparative example 1 | 784 | 1485 | 3.2 |
| Comparative example 2 | 391 | 1280 | 11.2 |
As can be seen from Table 1, the ultra-high strength stainless steels obtained in examples 1 to 3 of the present invention have excellent tensile resistance and plasticity, wherein the tensile strength is >1500MPa and the elongation is >15%. In particular, the ultra-high strength stainless steel of example 1 has a tensile strength up to 1550MPa and an elongation up to 19.1%. The ultra-high strength steel obtained in comparative example 1 had a very low elongation of only 3.2% although the yield strength and tensile strength were both high. As is clear from comparison, compared with example 1, the additive manufacturing parameter conditions adopted in comparative example 1 are identical to those of comparative example 1, and meanwhile, the components of the iron-based alloy powder are identical, and the difference is only that the proportions of the elements of the components are different, so that the content proportions of the elements in the components have a great influence on the performance of the ultra-high-strength stainless steel manufactured by the additive. The ultra-high strength stainless steel prepared by the iron-based alloy powder in the dosage proportion has the ultra-high strength tensile property and excellent plasticity.
As is apparent from a further detailed comparison of example 1 with comparative example 1, the main difference between the composition of the iron-based powder of example 1 and that of comparative example 1 is the change in the content of C element and Cr element, which both have a stabilizing austenitic effect, and the content of C element and Cr element in comparative example 1 is below the critical range specified in the present invention, so that the microstructure of the ultra-high strength stainless steel after additive manufacturing is greatly changed, i.e. the reduction in the content of stabilizing austenitizing element in the iron-based alloy powder causes the reduction or even disappearance of the austenitic content in the microstructure of the ultra-high strength stainless steel obtained after printing, and in particular, as shown in fig. 2, a comparative graph of the relative distribution of example 1 and comparative example 1 is shown in fig. 2, in which white represents the residual austenite and gray is martensitic. As is clear from the figure, the matrix structure of the ultra-high strength stainless steel obtained in comparative example 1 is a martensitic structure, and although martensite has high strength, plasticity is poor. Since the transformation induced plasticity effect is not sufficiently exhibited by the remarkable reduction of austenite, the ultra-high strength steel obtained in comparative example 1 has a poor elongation although it has a good strength. The proportion of the austenite stabilizing element in the embodiment 1 is proper, so that the microstructure of the ultra-high strength stainless steel obtained by additive manufacturing contains a large amount of residual austenite and martensite microstructure, and the residual austenite can generate a transformation induced plasticity effect through generating transformation to martensite in the stress process of a sample, so that the ultra-high strength steel obtained in the embodiment 1 has high strength and high plasticity, and has excellent comprehensive mechanical properties of strong plasticity. Furthermore, it is necessary to say that: since Cr element can stabilize austenite and improve corrosion resistance of steel, and the content of Cr element in comparative example 1 is reduced, not only the effect of stabilizing austenite is reduced, but also the corrosion resistance of the additive manufactured stainless steel is reduced, therefore, it is necessary to mix austenite stabilizing element C, cr and Ni appropriately to obtain an additive manufactured ultra-high strength stainless steel having a large amount of residual austenite and excellent performance.
As can be seen from comparison of example 2 and comparative example 2, the adoption of the selective laser melting additive manufacturing parameters provided by the invention for preparing the ultra-high strength stainless steel can make the strength and plasticity of the ultra-high strength stainless steel more excellent. The iron-based alloy powder of example 2 and comparative example 2 have the same composition and proportions of the components, the main difference being the additive manufacturing parameters, the specific differences being: comparative example 2 reduced laser power during additive manufacturing, increased scan speed, resulting in reduced energy density of heat input during additive manufacturing, resulting in partial powder undissolved in the region, creating hole defects. Example 2 and comparative example 2 the internal hole defect distribution diagrams of the molded samples for additive manufacturing are shown in fig. 3, and it is understood from fig. 3 that a large number of internal hole defects in the molded samples for additive manufacturing obtained in comparative example 2 impair the overall strength and plasticity, resulting in a significant decrease in strength-plasticity. Whereas example 2 has high density of samples with fewer internal defects in the samples under optimized additive manufacturing preparation parameters, the strength-plasticity of the ultra-high strength stainless steel manufactured by example 2 is more excellent than that of comparative example 2.
In a word, under the condition of proper component proportion and additive manufacturing parameter, the embodiment comparison example has more excellent plastic strengthening performance.
Comparative test 2
The ultra-high strength stainless steel obtained in the embodiment 2 of the invention and the commercial high strength stainless steel powder with the model number of 17-4PH are subjected to tensile stress strain comparison under the same additive manufacturing parameter conditions, and a comparison chart of the obtained stress strain curves is shown in figure 6. As can be seen from the graph, the ultra-high strength steel in example 2 of the present invention has a tensile strength of 1550MPa and an elongation of 19.1%; whereas the tensile strength of the commercial 17-4PH high-strength stainless steel is 980MPa, and the elongation is 11.2%. Therefore, compared with the commercial 17-4PH high-strength stainless steel, the ultra-high-strength stainless steel provided by the invention has obviously improved tensile strength and elongation in a printing state.
Meanwhile, as shown in fig. 1, the iron-based alloy stainless steel powder of the embodiment 2 of the invention has a spherical shape, and has good sphericity, and the particle size of the iron-based alloy stainless steel powder is between 15 and 53 mu m.
Fig. 4 is a scanning electron microscope topography of the ultra-high strength stainless steel of example 2, and fig. 5 is an X-ray diffraction result of the ultra-high strength stainless steel of example 2. As can be seen from fig. 4, the microstructure of the ultra-high strength stainless steel in example 2 is an ultra-fine (1-2 μm) microstructure, whereas the microstructure of the ultra-high strength stainless steel in example 2 is composed of austenite (γ -phase) and martensite (α -phase) phases as can be seen from fig. 5. This ultra-fine duplex structure of austenite and martensite is the root cause of its excellent strong plasticity. The main mechanism of the high-strength plastic is quite different from that of the martensitic 17-4PH high-strength stainless steel adopting precipitation hardening, and the additive manufacturing ultra-high-strength stainless steel of the invention has better strength and plasticity than that of the additive manufacturing 17-4PH high-strength stainless steel (shown in figure 6).
Finally, it should be noted that: these embodiments are merely for illustrating the present invention and do not limit the scope of the present invention. Further, various other changes and modifications will be apparent to those skilled in the art from the foregoing description. It is not necessary here nor is it exhaustive of all embodiments. And obvious variations or modifications thereof are contemplated as falling within the scope of the present invention.
Claims (3)
1. The ultra-high strength stainless steel manufactured by additive manufacturing is manufactured by adopting iron-based alloy powder through additive manufacturing, and is characterized in that: the iron-based alloy powder comprises the following element components in percentage by mass: c:0.38%, cr:13%, mn:0.30%, si:0.68%, ni:2.5%, nb:0.04%, mo:0.5%, the balance being Fe;
the additive manufacturing is selective laser melting additive manufacturing;
the laser power of the selective laser melting additive manufacturing is 160-180W;
the scanning speed of the selective laser melting additive manufacturing is one of 800mm/s, 850mm/s, 900mm/s, 950mm/s, 1000mm/s, 1050mm/s, 1100mm/s, 1150mm/s or 1200 mm/s;
the scanning interval of the selective laser melting additive manufacturing is 0.08mm, and the powder paving thickness of the selective laser melting additive manufacturing is 0.03mm.
2. The ultra-high strength stainless steel manufactured by additive manufacturing is manufactured by adopting iron-based alloy powder through additive manufacturing, and is characterized in that: the iron-based alloy powder comprises the following element components in percentage by mass: c:0.25%, cr:16%, mn:0.33%, si:0.70%, ni:4.8%, nb:0.04%, mo:0.5%, the balance being Fe;
the additive manufacturing is selective laser melting additive manufacturing;
the laser power of the selective laser melting additive manufacturing is 160-180W;
the scanning speed of the selective laser melting additive manufacturing is one of 800mm/s, 850mm/s, 900mm/s, 950mm/s, 1000mm/s, 1050mm/s, 1100mm/s, 1150mm/s or 1200 mm/s;
the scanning interval of the selective laser melting additive manufacturing is 0.08mm, and the powder paving thickness of the selective laser melting additive manufacturing is 0.03mm.
3. An additive manufactured ultra high strength stainless steel according to claim 1 or 2, characterized in that: the particle size of the iron-based alloy powder is between 15 and 53 mu m.
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| WO2019121879A1 (en) * | 2017-12-22 | 2019-06-27 | Voestalpine Böhler Edelstahl Gmbh & Co Kg | Method for the additive manufacturing of an object from a maraging steel powder |
| CN111491750A (en) * | 2018-01-09 | 2020-08-04 | 山阳特殊制钢株式会社 | Stainless steel powder for molding |
| CN113462992A (en) * | 2021-07-05 | 2021-10-01 | 上海交通大学 | Iron-based alloy powder for additive manufacturing, application of iron-based alloy powder and ultrahigh-strength steel for additive manufacturing |
| CN114231842A (en) * | 2021-11-26 | 2022-03-25 | 上海镭镆科技有限公司 | 3D printing stainless steel material and heat treatment method after printing |
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| WO2019121879A1 (en) * | 2017-12-22 | 2019-06-27 | Voestalpine Böhler Edelstahl Gmbh & Co Kg | Method for the additive manufacturing of an object from a maraging steel powder |
| CN111491750A (en) * | 2018-01-09 | 2020-08-04 | 山阳特殊制钢株式会社 | Stainless steel powder for molding |
| CN113462992A (en) * | 2021-07-05 | 2021-10-01 | 上海交通大学 | Iron-based alloy powder for additive manufacturing, application of iron-based alloy powder and ultrahigh-strength steel for additive manufacturing |
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