CN116837273A - Spray formed precipitation hardening high speed steel - Google Patents
Spray formed precipitation hardening high speed steel Download PDFInfo
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- CN116837273A CN116837273A CN202111436960.9A CN202111436960A CN116837273A CN 116837273 A CN116837273 A CN 116837273A CN 202111436960 A CN202111436960 A CN 202111436960A CN 116837273 A CN116837273 A CN 116837273A
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- 229910000997 High-speed steel Inorganic materials 0.000 title claims abstract description 59
- 238000004881 precipitation hardening Methods 0.000 title claims abstract description 50
- 239000007921 spray Substances 0.000 title claims description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 28
- 229910052742 iron Inorganic materials 0.000 claims abstract description 18
- 239000000126 substance Substances 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910000765 intermetallic Inorganic materials 0.000 claims abstract description 6
- 238000009718 spray deposition Methods 0.000 claims description 18
- 239000002245 particle Substances 0.000 claims description 6
- 238000001556 precipitation Methods 0.000 claims description 5
- 229910045601 alloy Inorganic materials 0.000 abstract description 20
- 239000000956 alloy Substances 0.000 abstract description 20
- 239000011159 matrix material Substances 0.000 abstract description 7
- 239000006104 solid solution Substances 0.000 abstract description 7
- 238000005204 segregation Methods 0.000 abstract description 2
- 229910000831 Steel Inorganic materials 0.000 description 44
- 239000010959 steel Substances 0.000 description 44
- 238000000034 method Methods 0.000 description 22
- 230000008569 process Effects 0.000 description 19
- 238000010438 heat treatment Methods 0.000 description 17
- 239000000203 mixture Substances 0.000 description 10
- 238000005496 tempering Methods 0.000 description 10
- 230000032683 aging Effects 0.000 description 9
- 238000000151 deposition Methods 0.000 description 9
- 230000008021 deposition Effects 0.000 description 8
- 238000002347 injection Methods 0.000 description 8
- 239000007924 injection Substances 0.000 description 8
- 238000004663 powder metallurgy Methods 0.000 description 8
- 238000002360 preparation method Methods 0.000 description 8
- 238000005242 forging Methods 0.000 description 7
- 239000007789 gas Substances 0.000 description 7
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 6
- 238000001816 cooling Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 230000001681 protective effect Effects 0.000 description 5
- 238000004458 analytical method Methods 0.000 description 4
- 238000000137 annealing Methods 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 238000004321 preservation Methods 0.000 description 4
- 239000002893 slag Substances 0.000 description 4
- 239000012298 atmosphere Substances 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000011261 inert gas Substances 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 229910052757 nitrogen Inorganic materials 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 238000004220 aggregation Methods 0.000 description 2
- 230000002776 aggregation Effects 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 238000000889 atomisation Methods 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 238000001540 jet deposition Methods 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 239000003921 oil Substances 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 238000003756 stirring Methods 0.000 description 2
- 229910052721 tungsten Inorganic materials 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 229910000760 Hardened steel Inorganic materials 0.000 description 1
- 229910000846 In alloy Inorganic materials 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- 241001085205 Prenanthella exigua Species 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- ZMIGMASIKSOYAM-UHFFFAOYSA-N cerium Chemical compound [Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce] ZMIGMASIKSOYAM-UHFFFAOYSA-N 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000006731 degradation reaction Methods 0.000 description 1
- 238000005137 deposition process Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000012938 design process Methods 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 238000007599 discharging Methods 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 238000001746 injection moulding Methods 0.000 description 1
- 238000011068 loading method Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 239000012299 nitrogen atmosphere Substances 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 239000010937 tungsten Substances 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/115—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by spraying molten metal, i.e. spray sintering, spray casting
-
- 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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
-
- 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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- 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
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
- B22F2003/248—Thermal after-treatment
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
Abstract
A spray-formed precipitation hardening high-speed steel comprises the following chemical components in percentage by mass: si:0.5% -1.2%; co:10.0% -25.0%; ce:0.01% -0.1%; w:0% -5.0%; mo:15.0% -25.0%; (mo+w/2): 15.0% -27.0%; the balance being iron and impurities. The spray-formed precipitation hardening high-speed steel prepared by the invention has a uniform microstructure, mainly comprises an iron-based cubic solid solution matrix and a mu phase of intermetallic compound (IMC for short) in the matrix, wherein the mu phase is (Fe, co) 7 (Mo+W/2) 6 Type (2). The segregation of alloy elements is restrained in a small range, the mu phase is small in size and uniform in distribution, and the wear resistance and the grindability are well influenced.
Description
Technical Field
The invention relates to novel high-speed steel, in particular to spray forming precipitation hardening high-speed steel.
Background
Precipitation hardening steel is a carbon-free iron-based martensitic precipitation hardening tool alloy, which has been classified as high speed steel because of its properties (hardness, strength, toughness), uses, and major elements that are the same as high speed steel. But is greatly different from the conventional high-speed steel in terms of phase composition, structural transformation and heat treatment characteristics.
Because the content of C in the components of the precipitation hardening steel is low, carbide precipitation is basically avoided, the structure is mainly an iron-based matrix and intermetallic compounds (i.e. IMCs) of Fe-Co-Mo-W, and the hardening effect is caused by IMC particles precipitated in the aging process. The precipitation hardening high-speed steel has good grindability, tempering softening resistance and dimensional stability.
At present, precipitation hardening steel is prepared by adopting a powder metallurgy process, so that the problem of element segregation can be solved, and a uniform tissue structure is obtained.
Disclosure of Invention
In view of this, the present invention provides a spray formed precipitation hardened high speed steel having good texture and excellent properties.
In order to achieve the above purpose, the technical scheme of the invention is realized as follows:
a spray formed precipitation hardening high speed steel, characterized in that the steel comprises the following chemical components in mass percent:
Si：0.5％-1.2％；
Co：10.0％-25.0％；
Ce：0.01％-0.1％；
W：0％-5.0％；
Mo：15.0％-25.0％；
(Mo+W/2)：15.0％-27.0％；
the balance of iron and impurities;
and, intermetallic compound (i.e., IMC phase) in the spray-formed high-speed steel is μ phase, and the μ phase is of the type (Fe, co) 7 (Mo+W/2) 6 。
According to the invention, through the design of alloy components, precipitation of mu phase of precipitation hardening high-speed steel under the spray forming process is promoted, so that tempering softening resistance and toughness of the steel are improved.
As a limitation of the above manner, the spray-formed precipitation hardening high-speed steel comprises the following chemical components in mass percent:
Si：0.5％-1.0％；
Co：10.0％-22.0％；
Ce：0.01％-0.08％；
W：0％-3.0％；
Mo：15％-23.0％；
(Mo+W/2)：15.0％-24.0％；
the balance being iron and impurities.
In order to achieve better comprehensive performance, each chemical component in the spray forming precipitation hardening high-speed steel is controlled within a required range.
Further, at least 80% of the volume fraction of the mu phase has a size of 1.5 μm or less and the largest dimension of the mu phase does not exceed 7.5. Mu.m.
Further, the volume fraction of the μ phase is 12-20%.
The invention also provides a preparation method for preparing the spray forming precipitation hardening high-speed steel, and the preparation method comprises the following steps:
s1. preparing precipitation hardening molten steel according to the chemical composition requirement and transferring to a ladle;
s1.1. maintaining the superheat degree of molten steel by heating covering slag covered on the upper surface of molten steel in a ladle; introducing inert gas into the bottom of the ladle to stir molten steel;
s1.2, flowing molten steel into a preheated tundish through a flow guide pipe at the bottom of a ladle at a stable flow rate, and applying protective slag to the upper surface of the molten steel when the molten steel enters the lower end surface of the flow guide pipe buried in the tundish;
s1.3. continuously compensating and heating the tundish, and maintaining the superheat degree of molten steel;
s1.4, atomizing and depositing the molten steel by adopting inert gas after the molten steel enters an injection and deposition chamber from a tundish, and completing injection and deposition under the stable outlet pressure to obtain an injection and deposition ingot; maintaining stable temperature and flow of molten steel in the spray deposition process, slowly descending the spray deposition receiving disc while horizontally rotating, and keeping the descending speed of the spray deposition receiving disc and the growth speed of the spray deposition ingot to ensure that the height of the upper end surface of the spray deposition ingot is constant; controlling the gas inlet flow and the gas outlet flow, and keeping the inert gas protective atmosphere of the jet deposition chamber;
and s1.5, transferring the spray deposited ingot to a protective atmosphere furnace for annealing or directly transferring to a hot forging and cogging process link.
S2, forging and opening the blank
Homogenizing by a chamber furnace, discharging, and forging and cogging the spray deposited ingot by adopting a plurality of fires and small deformation to obtain the precipitation hardening high-speed steel bar.
s3. heat treatment
Carrying out solid solution aging treatment on the bar, keeping the solid solution temperature at 1170-1190 ℃, and carrying out oil cooling after 30min of heat preservation; then aging treatment is carried out, the aging temperature is 600-650 ℃, a box-type resistance furnace is adopted for heat preservation for 3 hours, and then air cooling is carried out.
The bar material obtained by the preparation method has uniform composition structure and fine mu phase, can obtain excellent mechanical properties, particularly high red hardness and better toughness, has the hardness of 64HRC after solution aging treatment, has no notch impact toughness of more than 10J, and can meet the application requirements of different types. The precipitation hardening high-speed steel is prepared by adopting a spray forming process, the preparation cost is lower than that of a powder metallurgy process, the integral cost of the alloy is reduced, and the process flow is simplified.
Drawings
The accompanying drawings, which are included to provide a further understanding of the invention and are incorporated in and constitute a part of this specification, illustrate embodiments of the invention and together with the description serve to explain the invention. In the drawings:
FIG. 1 is a microstructure of precipitation hardening high-speed steel prepared in example 1 of the present invention;
FIG. 2 is a microstructure of precipitation hardening high-speed steel prepared in example 2 of the present invention;
FIG. 3 is a microstructure of precipitation hardening high-speed steel prepared in example 4 of the present invention;
FIG. 4 is a microstructure of precipitation hardening high-speed steel prepared in example 5 of the present invention;
FIG. 5 is a microstructure of precipitation hardening high-speed steel prepared in example 6 of the present invention;
FIG. 6 is a microstructure of the high-speed steel of the electroslag process prepared in comparative example A of the present invention;
FIG. 7 is a microstructure of the powder metallurgy high-speed steel prepared in comparative example B of the present invention;
FIG. 8 is a comparative chart of tempering resistance according to examples 1 to 9 of the present invention
Detailed Description
It should be noted that, without conflict, the embodiments of the present invention and features of the embodiments may be combined with each other.
The invention will be described in detail below with reference to the drawings in connection with embodiments.
The invention relates to spray-formed precipitation hardening high-speed steel, which comprises the following chemical components in percentage by mass: si:0.5% -1.2%; co:10.0% -25.0%; ce:0.01% -0.1%; w:0% -5.0%; mo:15% -23.0%; (mo+w/2): 15.0% -27.0%; the balance being iron and impurities.
Meanwhile, intermetallic compounds (i.e., IMC phases) in the spray-formed high-speed steel are μ phases, and the μ phases are of the type (Fe, co) 7 (Mo+W/2) 6 Wherein the volume fraction of the mu phase is 12-20%, and at least 80% of the volume fraction of the mu phase has a mu phase size of 1.5 μm or less and the largest dimension of the mu phase is not more than 7.5 μm.
Specifically, the effect of Co in the precipitation hardening high-speed steel of the present invention is to form a solid solution in the matrix to make the alloy a martensitic steel, thereby improving the hardness and strength of the ferritic alloy by one step, and the increase in Co (cobalt) content, which is in the range of 10.0% to 25.0%, preferably 10.0% to 22.0%, suitably reduces the toughness of the steel.
The W (tungsten) has high melting point, increases the strength and tempering stability of the steel, increases the high-temperature creep resistance and increases the tempering softening resistance of the steel, so that the steel has less surface layer temperature rise and hardness drop in the processing and using processes, and the W element content range is 0% -5.0%, preferably 0% -3.0% in the invention.
Mo (molybdenum) acts on W in the same manner, and can completely replace W, and is lower in price than W. On the other hand, the higher the Mo content, the higher the initial precipitation temperature of the mu phase, and the larger the granularity of the mu phase, the Mo element content in the present invention is in the range of 15.0% to 25.0%, preferably 15.0% to 23.0%.
Ce (cerium) is added in the refining stage, can react with oxygen, sulfur and the like in molten steel to generate compounds, is discharged from the molten steel as impurities, and can play roles in deoxidation, desulfurization and modification.
Si (silicon) is not a carbide forming element but is used as a deoxidizer and matrix strengthening element to improve the strength and hardness of steel, but Si is excessive to lower the plasticity and toughness of the matrix, and the Si content of the present invention is controlled to be 0.5% to 1.2%, and preferably 0.5% to 1%.
Based on the above description, it can be found that the precipitation hardening high-speed steel of the present invention comprises, as preferable in mass%, the following chemical components: si:0.5% -1.0%; co:10.0% -22.0%; ce:0.01% -0.08%; w:0% -3.0%; mo:15% -23.0%; (mo+w/2): 15.0% -24.0%; the balance being iron and impurities. The precipitation hardening high-speed steel of the present invention, which is composed of the above components, can achieve an ideal structure and excellent properties to meet the demands.
Secondly, the present invention also relates to a method for preparing the precipitation hardening high-speed steel as above, which is easy to be segregated to cause performance degradation due to slow solidification speed when prepared by adopting a conventional ingot casting or electroslag process. The powder metallurgy process is long in flow and high in cost, and on the premise of ensuring that the components of the prepared precipitation hardening high-speed steel ingot are uniform in structure, fine in mu phase and high in purity, the spray forming process is adopted to replace the powder metallurgy process for preparing the steel ingot, and the required bar product is obtained through forging.
Specifically, the preparation method of the invention specifically comprises the following steps:
s1. the precipitation hardening steel liquid of the invention is filled into a spray forming smelting ladle, and the loading weight of the steel liquid is 3.5 tons;
s1.1. electrifying and heating the covering slag covered on the upper surface of the molten steel in the steel ladle by adopting a graphite electrode, introducing argon into the bottom of the steel ladle to stir the molten steel, and opening a molten steel guide pipe when the superheat degree of the molten steel reaches 100-150 ℃;
s1.2, flowing molten steel into a tundish preheated to 1200 ℃ through a flow guide pipe at the bottom of a ladle at the flow rate of 100Kg/min, and applying covering slag when the molten steel enters the tundish and is buried at the lower end face of the flow guide pipe;
s1.3. continuously compensating and heating the tundish in the spray deposition process, and maintaining the superheat degree of molten steel at 100-150 ℃;
s1.4, the molten steel enters a jet deposition chamber through the bottom of the tundish, a gas jet valve is opened, nitrogen is adopted as a gas medium for atomization deposition, the purity of the nitrogen is more than or equal to 99.999%, the oxygen content is less than or equal to 2ppm, and the outlet pressure of a gas nozzle is 1.0MPa; the molten steel is crushed into semi-solidified molten drops under the effect of nitrogen injection, the semi-solidified molten drops are mixed with gas to form an atomization cone, the molten drops fly to an injection deposition receiving disc to slowly descend and horizontally rotate at the same time, and the descending speed of the injection deposition receiving disc and the growth speed of an injection deposition ingot are kept to be constant so that the height of the upper end face of the injection deposition ingot is kept constant; before and after the start of spray deposition, continuously maintaining protective nitrogen atmosphere in the spray deposition chamber, and controlling gas inlet and outlet flow in the deposition process;
s1.5, obtaining single ingot with the weight of more than 3 tons and the size phi of 550mm after spray deposition, transferring the spray deposited ingot to a protective atmosphere furnace for annealing, and then cooling along with the furnace.
S2, forging and opening the blank
And forging and opening the spray deposition ingot by adopting multiple fires with small deformation, wherein each deformation is 5-20mm, each heating temperature is 1170-1200 ℃, heating is carried out for 400min, the total number of fires is 4, tube annealing is carried out in time after the ingot is opened, and the annealing temperature is 870-890 ℃, so that the precipitation hardening high-speed steel bar is finally obtained.
s3. heat treatment
Carrying out solid solution aging treatment on the bar, keeping the solid solution temperature at 1170-1190 ℃, and carrying out oil cooling after 30min of heat preservation; then aging treatment is carried out, the aging temperature is 600-650 ℃, a box-type resistance furnace is adopted for heat preservation for 3 hours, and then air cooling is carried out.
The spray-formed precipitation hardening high-speed steel of the present invention and the preparation thereof will be further described below with specific preparation examples and comparative examples, and corresponding performance tests.
The mu-phase granularity and the volume fraction of the spray-formed precipitation hardening high-speed steel, the heat treatment hardness, the tempering softening resistance and the impact toughness are verified, wherein the mu-phase granularity and the volume fraction are analyzed based on tissue images obtained by a scanning electron microscope, and the heat treatment hardness, the tempering softening resistance and the impact toughness are respectively tested by referring to GB/T230.1 and GB/T229.
Seven precipitation hardening high-speed steels having different compositions in total were obtained by the above-described production methods in examples 1 to 7, and compared with cast forging tool steels (alloy a) and powder metallurgy tool steels (alloy B), the results were as follows:
table 1 composition comparison:
the "-" in the table indicates that the element is not contained, or the element content is little to no analysis.
Microstructure analysis
FIGS. 1 to 5 are schematic diagrams of microstructures of examples 1, 2, 4, 5 and 6, respectively, of the precipitation-hardened steel rods prepared, FIG. 6 is a schematic diagram of the microstructure of alloy A, and FIG. 7 is a schematic diagram of the microstructure of alloy B
It is apparent that the off-white hardened phase of fig. 1-5 is dispersed in the matrix, which can significantly improve the wear resistance, toughness and service life of the material. Two precipitated phases are included in fig. 6 and 7, one of which is bright white and has a large size, and the other of which is off-white and has a small size.
The high speed steels produced in examples 1 to 7 after heat treatment were compared with the content of precipitated phases, particle size, composition in alloy A, B:
TABLE 2 content of precipitated phases and chemical composition
"-" in the table indicates: the element is not contained or the element content is little and not analyzed.
As can be seen from Table 2, in examples 1 to 7, the detected IMC was mainly a μ phase, of the type (Fe, co) 7 (Mo+W/2) 6 The main component is Fe, co, mo, W and a small amount of alloy elements such as Si. In alloys A and B, the detected strengthening phase is mainly of two major types, one is VC type carbide, the components are mainly C, V, cr and Fe, the other is Cr-rich carbide, the type is (Cr, fe) C type carbide, the components are mainly C, V, cr and Fe, and a small amount of Mo is contained.
The precipitation hardening high-speed steel has the volume fraction of mu phase reaching 12% -20%, fine granularity, most mu phase granularity smaller than 1.5 mu m and maximum size not larger than 7 mu m, and the precipitated phases have fine size and large dispersity, and meanwhile, the mu phase high-temperature aggregation resistance is higher than that of carbide, so that the material has better service life.
The VC-type carbide in the alloy B prepared by adopting the powder metallurgy process is the finest, but the (Cr, fe) C-type carbide with a large quantity and a size range of 4-7 mu m also exists in the structure. Although the largest size of VC type carbide in the A alloy by electroslag remelting process is smaller than that of mu phase in the precipitation hardening high-speed steel example of the invention, the (Cr, fe) C type carbide with larger quantity and size range of 5-9 mu m exists in the structure.
(II) Heat treatment hardness and impact toughness analysis
In order to verify the influence of a heat treatment system on the performance of the precipitation hardening high-speed steel prepared by the method, heat treatment processes with different solid solution temperatures and aging temperatures are set for carrying out heat treatment on the prepared bar.
The high-speed steels and alloys A, B obtained in examples 1 to 7 were heat-treated, and the following hardness and impact toughness comparisons were obtained as shown in table 3.
Table 3: comparison of mechanical Properties
As can be seen from Table 3, the hardness of the spray-formed precipitation-hardenable high-speed steel of the present invention was 64HRC or more, the impact toughness value of the non-defective sample was 10.0J or more, and the measured value satisfies the toughness requirement in the application field although the impact toughness of the precipitation-hardenable high-speed steel of the present invention is relatively low, so that the precipitation-hardenable high-speed steel of the present invention is particularly suitable for use in the case of less impact load operation.
(III) tempering softening resistance analysis
The high-speed steels and alloys A, B obtained in examples 1 to 7 were compared for temper softening resistance, the heat treatment process used is shown in Table 4, and the temper softening resistance results are shown in FIG. 8.
TABLE 4 tempering softening resistant process
As can be seen from fig. 8, the precipitation hardening steel of the present invention exhibits more excellent temper softening resistance.
In addition, the precipitation hardening steel of the present invention is prepared under the above-mentioned implementation conditions due to the limitation of the statistical image analysis software of the number of precipitated phase particles, and the size of the individual μ phase may exist in the structure exceeding the maximum size, but the number thereof is very small, and thus has no substantial influence on the toughness and other mechanical properties of the precipitation hardening steel, and thus may be disregarded. In addition, many smaller mu phases of particles cannot be identified by analysis software, and the statistics of volume fraction and granularity are only used as comparison.
The invention adopts specific alloy component design and injection molding process to prepare, has high intermetallic compound mu phase content, fine granularity and high dispersity, and has higher high-temperature aggregation resistance than carbide, so that the material has better toughness and longer service life, can meet different application requirements, and can be used for manufacturing (1) cutters for cutting difficult-to-process materials at high speed; (2) high-precision measuring tool; (3) thin and thin blade cutters.
In summary, the spray-formed precipitation hardening high-speed steel of the present invention has excellent mechanical properties, particularly excellent temper softening resistance. Because of the alloy composition characteristics, the alloy composition is different from the traditional high-speed steel strengthening mechanism, so that the tempering softening resistance of the alloy composition is better than that of the traditional high-speed steel and other tool steels, and the precipitation hardening high-speed steel has the characteristics of high efficiency and low cost compared with the powder metallurgy process due to the low preparation cost, and has good practicability.
The foregoing description of the preferred embodiments of the invention is not intended to be limiting, but rather is intended to cover all modifications, equivalents, alternatives, and improvements that fall within the spirit and scope of the invention.
Claims (6)
1. The spray forming precipitation hardening high-speed steel is characterized by comprising the following chemical components in percentage by mass:
Si：0.5％-1.2％；
Co：10.0％-25.0％；
W：0％-5.0％；
Ce：0.01％-0.1％；
Mo：15.0％-25.0％；
(Mo+W/2)：15.0％-27.0％；
the balance of iron and impurities;
and, the intermetallic compound in the spray-formed precipitation hardening high-speed steel is a mu phase, and the type of the mu phase is (Fe, co) 7 (Mo+W/2) 6 。
2. The spray-formed precipitation hardening high-speed steel according to claim 1, wherein the chemical components thereof comprise, in mass percent:
Si：0.5％-1.0％；
Co：10.0％-22.0％；
W：0％-3.0％；
Ce：0.01％-0.08％；
Mo：15％-23.0％；
(Mo+W/2)：15.0％-24.0％；
the balance being iron and impurities.
3. The spray-formed precipitation hardening high-speed steel according to claim 1 or 2, characterized in that: at least 80% of the volume fraction of the mu phase has a particle size of 1.5 mu m or less.
4. The spray-formed precipitation hardening high-speed steel according to claim 1 or 2, characterized in that: the maximum particle size of the μ phase is no more than 7.5 μm.
5. The spray-formed precipitation hardening high-speed steel according to claim 1 or 2, characterized in that: the volume fraction of the mu phase in the spray formed precipitation hardened high speed steel is 12-20%.
6. The spray-formed precipitation hardening high-speed steel according to claim 1 or 2, characterized in that: the hardness of the spray-formed precipitation hardening high-speed steel is more than 64HRC, and the impact toughness value of an unoccupied sample is more than 10.0J.
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