CN109112425A - A kind of ultrahigh-intensity high-toughness Maraging steel and its preparation method and application - Google Patents
A kind of ultrahigh-intensity high-toughness Maraging steel and its preparation method and application Download PDFInfo
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- CN109112425A CN109112425A CN201811338298.1A CN201811338298A CN109112425A CN 109112425 A CN109112425 A CN 109112425A CN 201811338298 A CN201811338298 A CN 201811338298A CN 109112425 A CN109112425 A CN 109112425A
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- 229910001240 Maraging steel Inorganic materials 0.000 title claims abstract description 74
- 238000002360 preparation method Methods 0.000 title claims description 29
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 32
- 229910052802 copper Inorganic materials 0.000 claims abstract description 28
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 24
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 22
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 22
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 21
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 21
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 21
- 239000000126 substance Substances 0.000 claims abstract description 19
- 239000000203 mixture Substances 0.000 claims abstract description 12
- 238000009941 weaving Methods 0.000 claims abstract description 7
- 238000005242 forging Methods 0.000 claims description 64
- 229910000831 Steel Inorganic materials 0.000 claims description 44
- 239000010959 steel Substances 0.000 claims description 44
- 238000010438 heat treatment Methods 0.000 claims description 38
- 238000011282 treatment Methods 0.000 claims description 33
- 239000002994 raw material Substances 0.000 claims description 22
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 20
- 229910052751 metal Inorganic materials 0.000 claims description 20
- 230000032683 aging Effects 0.000 claims description 18
- 238000000265 homogenisation Methods 0.000 claims description 18
- 229910000734 martensite Inorganic materials 0.000 claims description 17
- 239000002184 metal Substances 0.000 claims description 17
- 238000002844 melting Methods 0.000 claims description 16
- 230000008018 melting Effects 0.000 claims description 16
- 238000012545 processing Methods 0.000 claims description 14
- 238000007670 refining Methods 0.000 claims description 14
- 230000006698 induction Effects 0.000 claims description 12
- 239000007788 liquid Substances 0.000 claims description 10
- 238000004321 preservation Methods 0.000 claims description 8
- 239000010949 copper Substances 0.000 abstract description 35
- 239000000463 material Substances 0.000 abstract description 9
- 239000011258 core-shell material Substances 0.000 abstract description 4
- 239000002105 nanoparticle Substances 0.000 abstract description 3
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 25
- 239000010936 titanium Substances 0.000 description 24
- 238000003483 aging Methods 0.000 description 16
- 238000000034 method Methods 0.000 description 14
- 230000008569 process Effects 0.000 description 11
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 9
- 230000000052 comparative effect Effects 0.000 description 8
- 239000000047 product Substances 0.000 description 8
- 229910052759 nickel Inorganic materials 0.000 description 7
- 238000005728 strengthening Methods 0.000 description 7
- 239000000956 alloy Substances 0.000 description 5
- 230000008901 benefit Effects 0.000 description 5
- 238000005336 cracking Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 239000004615 ingredient Substances 0.000 description 5
- 229910052742 iron Inorganic materials 0.000 description 5
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000012535 impurity Substances 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 238000013461 design Methods 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 238000002156 mixing Methods 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 230000006911 nucleation Effects 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 238000003303 reheating Methods 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 238000010792 warming Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000000280 densification Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000005272 metallurgy Methods 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 229910000510 noble metal Inorganic materials 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 238000000844 transformation Methods 0.000 description 1
- 238000003466 welding Methods 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
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/001—Heat treatment of ferrous alloys containing Ni
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/04—Hardening by cooling below 0 degrees Celsius
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/105—Ferrous alloys, e.g. steel alloys containing cobalt containing Co and Ni
-
- 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
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The present invention provides a kind of Maraging steel of ultrahigh-intensity high-toughness, based on mass content, the chemical composition of the Maraging steel are as follows: Ni:18.0-20.0%, Co:15.0-18.0%, Mo:7.0-8.0%, Ti:1.5-2.5%, Cu:4.0-6.0%, C < 0.005%, O < 0.001%, N < 0.002%, P < 0.001%, S < 0.001%, surplus Fe；The total content < 0.01% of described C, O, N, P, S.Copper-rich phase and Ni are formd in the Maraging steel of ultrahigh-intensity high-toughness of the present invention3Ti core-shell structure, realizes the complex intensifying of soft, hard nanoparticle, and does not lose toughness, its tensile strength > 3000Mpa, yield strength > 2700Mpa, elongation percentage > 10% meet the demand of the weaving consumptive materials cost efficiency such as crochet hook and nailing gun striker.
Description
Technical field
The present invention relates to Maraging steel technical field, in particular to a kind of ultrahigh-intensity high-toughness Maraging steel
And its preparation method and application.
Background technique
Aldecor relies on the advantage of material cost, becomes be absorbed in the high intensity such as weaving crochet hook, striker always
The preferred material of the preparation enterprise of structural member.Maraging steel is energy when timeliness using carbon-free (or micro- carbon) martensite as matrix
The unimach of intermetallic precipitates hardening is generated, different from traditional Aldecor, it does not have to carbon and leans on gold
The disperse educt of compound is strengthened between category, this makes it have some unique performances: high-strength tenacity, low hardenability value, well
Formability, simple heat treatment process, Maraging steel are hardly deformed in heat treatment, have good welding performance.
Compared with Aldecor, although Maraging steel has the advantages such as apparent obdurability, it is unable to get phase always
It closes the approval of enterprise and realizes industrial application.
In the development process of Maraging steel, obdurability matching is to influence Maraging steel application with use cost
Two key problems of prospect, on the one hand, production is catered in the raising that martensite ag(e)ing hardness of steel is realized under the premise of guaranteeing toughness
The design aims such as lightweight, energy-saving and emission-reduction and the safety and environmental protection of product, be the key that determine Maraging steel application prospect because
Element；On the other hand, compared with common Aldecor, although Maraging steel obdurability is with the obvious advantage, due to
It uses the alloying elements such as the nickel of high-content, cobalt, molybdenum, titanium, cause the material cost of Maraging steel higher, it is difficult in reality
It is popularized in the application of border.Therefore, the performance advantage of Maraging steel how is made full use of, and reduces structural material totality
Production cost is the key that influence Maraging steel application prospect.
Summary of the invention
In view of this, it is an object of that present invention to provide a kind of Maraging steel of ultrahigh-intensity high-toughness and its preparation sides
Method and application, the present invention pass through the proportion that copper optimized alloy raw material is added, and are aided with double vacuum metlings, continuous forging and connect
Continuous heat treatment process develops tensile strength greater than 3000MPa, and yield strength is greater than 2700Mpa, and elongation percentage is super greater than 10%
High-intensity and high-tenacity Maraging steel realizes the cost efficiency of weaving crochet hook and nailing gun striker material.
In order to achieve the above-mentioned object of the invention, the present invention the following technical schemes are provided:
The present invention provides a kind of Maraging steel of ultrahigh-intensity high-toughness, based on mass content, the martensite
The chemical composition of aged steel are as follows: Ni:18.0-20.0%, Co:15.0-18.0%, Mo:7.0-8.0%, Ti:1.5-
2.5%, Cu:4.0-6.0%, C < 0.005%, O < 0.001%, N < 0.002%, P < 0.001%, S < 0.001% are remaining
Amount is Fe；The total content < 0.01% of described C, O, N, P, S.
Preferably, the chemical composition of the Maraging steel are as follows: Ni:18.5-19.5%, Co:15.5-
16.5%, Mo:7.0-7.5%, Ti:1.5-1.8%, Cu:5.0-6.0%, C < 0.005%, O < 0.001%, N <
0.002%, P < 0.001%, S < 0.001%, surplus Fe.
Preferably, the tensile strength > 3000Mpa of the Maraging steel, yield strength > 2700Mpa, elongation percentage >
10%.
The present invention also provides the preparation methods of the Maraging steel of above-mentioned ultrahigh-intensity high-toughness, including walk as follows
It is rapid:
(1) superpure metal raw material are successively subjected to first vacuum induction melting and double refining under vacuum, obtain steel
Ingot；
(2) steel ingot in the step (1) is subjected to homogenization heat treatment；
(3) steel ingot after homogenization heat treatment in the step (2) is directly forged, obtains blank；
(4) blank in the step (3) is subjected to continuous heat, the continuous heat is the blank after forging
Austenaging processing, subzero treatment and ageing treatment are directly carried out, the Maraging steel of ultrahigh-intensity high-toughness is obtained.
Preferably, the first vacuum induction melting in the step (1) carries out in vaccum sensitive stove, the first vacuum
The temperature of induction melting is 1450~1550 DEG C, vacuum degree < 1 × 10-4Pa。
Preferably, the double refining in the step (1) carries out in consumable electrode vacuum furnace, vacuum degree < 1 × 10-4Pa。
Preferably, the homogenization heat treatment in the step (2) specifically: will be kept the temperature after Heating Steel Ingots, the guarantor
The temperature of temperature is 1170~1230 DEG C, and the time of the heat preservation is 24~30h.
Preferably, the first forging temperature forged in the step (3) is 1100~1200 DEG C, and final forging temperature is not less than 850 DEG C；
The deflection of the forging needs to meet: the 1st forging deformation amount < 5%, the 2nd forging deformation amount < 10%, and the 3rd forging becomes
Shape amount < 15%, total deformation >=90% after finish-forging, forging ratio > 12.
Preferably, continuous heat in the step (4) specifically: directly put the blank after forging into 680~720 DEG C
2~4h is kept the temperature in heat-treatment furnace, is carried out austenaging, is then air-cooled to room temperature；By the blank after austenaging in liquid nitrogen
Middle holding 2h or more, is air-cooled to room temperature；By liquid nitrogen, treated that blank keeps the temperature 1~3h in 480~520 DEG C of heat-treatment furnace,
It is air-cooled to room temperature.
It is prepared the present invention also provides the Maraging steel of above-mentioned ultrahigh-intensity high-toughness or using above-mentioned preparation method
Ultrahigh-intensity high-toughness Maraging steel as weaving crochet hook or nailing gun striker application.
The utility model has the advantages that the present invention provides a kind of Maraging steel of ultrahigh-intensity high-toughness, and based on mass content, institute
State the chemical composition of Maraging steel are as follows: Ni:18.0-20.0%, Co:15.0-18.0%, Mo:7.0-8.0%, Ti:
1.5-2.5%, Cu:4.0-6.0%, C < 0.005%, O < 0.001%, N < 0.002%, P < 0.001%, S <
0.001%, surplus Fe；The total content < 0.01% of described C, O, N, P, S.The present invention improves the content of copper and optimization
The proportion of other noble metals, effectively reduces cost, impurity element in strict control alloy of the present invention, with prevent C, O,
N, the excessively high toughness for influencing Maraging steel of P, S element.
The present invention provides the preparation method of the Maraging steel of ultrahigh-intensity high-toughness described in above scheme, the present invention
By raw material, melting and double refining obtain steel ingot under vacuum, then keep steel ingot interior metal element equal by homogenizing heat treatment
It homogenizes；Homogenization heat treatment is combined repeatedly continuous hot forging by the present invention, is deformed steel ingot gradually and is obtained blank, heat of the invention
Forging method can prevent ingot cracking, and obtained blank internal flaw is few, ensure that the compactness of alloy；The present invention is by blank
Austenaging processing, subzero treatment and ageing treatment are directly carried out, the Maraging steel of ultrahigh-intensity high-toughness is obtained, and
And heat treatment process is simplified, reduce total production cost.The Maraging steel that the present invention is made by continuous heat
Copper-rich phase and Ni are formd in alloy3Ti core-shell structure, realizes the complex intensifying of soft, hard nanoparticle, and does not lose martensite
The toughness of aged steel.
Embodiment the result shows that, tensile strength the > 3000Mpa, yield strength > of Maraging steel provided by the invention
2700Mpa, elongation percentage > 10%, the present invention realizes cost efficiency, meets the weaving consumptive materials such as crochet hook and nailing gun striker
Demand.
Specific embodiment
The present invention provides a kind of Maraging steel of ultrahigh-intensity high-toughness, based on mass content, the martensite
The chemical composition of aged steel are as follows: Ni:18.0-20.0%, Co:15.0-18.0%, Mo:7.0-8.0%, Ti:1.5-
2.5%, Cu:4.0-6.0%, C < 0.005%, O < 0.001%, N < 0.002%, P < 0.001%, S < 0.001% are remaining
Amount is Fe；The total content < 0.01% of described C, O, N, P, S.
Design philosophy of the invention are as follows: copper is added in existing Maraging steel system, when optimizing martensite
The quality proportioning for imitating other alloying elements in steel achievees the purpose that cost reduction in conjunction with the continuous implementation of forging, heat treatment；At this
In invention, Cu is austenite former in Maraging steel, martensite start temperature is reduced, in martensite
Solid solubility is minimum, therefore has high strengthening effect after Maraging steel ageing treatment, and do not lose toughness.Together
When, Cu is preferentially precipitated in ageing process, can be intermetallic compound Ni3Ti plays the role of nucleation mass point, is formed rich
Copper phase and Ni3Ti core-shell structure realizes the complex intensifying of " soft ", " hard " nanoparticle, has higher strengthening effect.Inventor
It was found that Cu is as this effect of nucleation mass point, additional amount unsuitable very few, very few Cu content and Ni3Ti is precipitated simultaneously, is unable to shape
At core-shell structure, strengthening effect is undesirable；But it is existing that excessive Cu be easy to cause the steel that " hot-short " cracking occurs in forging process
As influencing lumber recovery.
In the present invention, in terms of mass content, the chemical composition of the Maraging steel includes Ni:18.0-
20.0%, preferably 18.5-19.5%, more preferably 19%；
In terms of mass content, the chemical composition of Maraging steel of the present invention further includes Co:15.0-
18.0%, preferably 15.5-16.5%, more preferably 16%；
In terms of mass content, the chemical composition of Maraging steel of the present invention further includes Mo:7.0-8.0%,
Preferably 7.0-7.5%, more preferably 7.3%；
In terms of mass content, the chemical composition of Maraging steel of the present invention further includes Ti:1.5-2.5%,
Preferably 1.5-1.8%, more preferably 1.6%；
In terms of mass content, the chemical composition of Maraging steel of the present invention further includes Cu:4.0-6.0%,
Preferably 4.0-6.0%, more preferably 5%；
In the present invention, the ingredient of the Maraging steel using superpure metal raw material (Fe, Ni, Co, Cu, Ti,
Mo ingredient) is carried out, to obtain high-purity extremely low impurity Maraging steel, the purity of the superpure metal raw material is all larger than
99.99%, it is more advantageous to the control in the melting of Maraging steel and continuous forging process to C, O, N, P, S content.This
Invention is not particularly limited the source of the superpure metal raw material (Fe, Ni, Co, Cu, Ti, Mo), using art technology
Commercially available superpure metal raw material known to personnel.
The present invention provides the preparation methods of the ultrahigh-intensity high-toughness Maraging steel described in above scheme, including such as
Lower step:
(1) superpure metal raw material are successively subjected to first vacuum induction melting and double refining under vacuum, obtain steel
Ingot；
(2) steel ingot in the step (1) is subjected to homogenization heat treatment；
(3) steel ingot after homogenization heat treatment in the step (2) is directly forged, obtains blank；
(4) blank in the step (3) is subjected to continuous heat, the continuous heat is the blank after forging
Austenaging processing, subzero treatment and ageing treatment are directly carried out, the Maraging steel of ultrahigh-intensity high-toughness is obtained.
Superpure metal raw material are successively carried out first vacuum induction melting and double refining by the present invention under vacuum, are obtained
Steel ingot.
In a specific embodiment of the present invention, preferably first Fe, Ni, Co, Cu, Ti, Mo superpure metal raw material are matched
Material, the ingredient is pre-configured according to the preferred amount ranges of each metallic element of design, during later period metallurgy
Loss ignore.
Configured superpure metal raw material preferably are mixed to be placed in vaccum sensitive stove by the present invention carries out first vacuum
Induction melting, the temperature of the first vacuum induction melting are preferably 1450~1550 DEG C, and more preferably 1500 DEG C~1550 DEG C,
Further preferably 1550 DEG C；The preferred < 1 × 10 of vacuum degree in the vaccum sensitive stove-4Pa。
The present invention preferably by the molten steel teeming after melting and is processed into consutrode, then carries out double refining, this
Invention carries out double refining using consumable electrode vacuum furnace, the preferred < 1 × 10 of vacuum degree in the consumable electrode vacuum furnace-4Pa.The present invention
The steel ingot obtained after double refining is subjected to homogenization heat treatment.In the present invention, the homogenization heat treatment is to add steel ingot
It being kept the temperature after heat, the temperature of the heat preservation is preferably 1170~1230 DEG C, and more preferably 1190~1210 DEG C, further preferably
It is 1200 DEG C, the time of the heat preservation is preferably 24~30h, more preferably 25~27h, further preferably 26h.The present invention is logical
Homogenization heat treatment is crossed, the metallic element inside steel ingot is made to reach homogenization, eliminates defect present in casting process.
The present invention directly forges the steel ingot after homogenization heat treatment, obtains blank.In the present invention, the forging
It is preferred that using continuous several times hot forging process, the continuous several times hot forging process is directly to close the blank after homogenization heat treatment
It is repeatedly forged at suitable temperature, without reheating again, and the deflection forged every time is stepped up, steel after the completion of forging
Ingot cannot be below set temperature, specifically: steel ingot is preferably 1100~1200 DEG C in the first forging temperature of forging, and final forging temperature is preferred
Not less than 850 DEG C；The deflection of the forging preferably satisfies: the 1st forging deformation amount < 5%, the 2nd forging deformation amount <
10%, the 3rd forging deformation amount < 15%, total deformation >=90% after finish-forging, forging ratio > 12.The present invention uses will be uniform
Blank after changing heat treatment directly carries out the mode of the hot forging of continuous several times, can not only prevent steel ingot from cracking, ensure that
The densification of steel ingot inner element and uniform performance, and reheating can be saved, reduce production cost.
The blank that the present invention obtains forging carries out continuous heat, and the continuous heat is that the blank after forging is straight
Tap into the processing of row austenaging, subzero treatment and ageing treatment.The blank that forging obtains preferably directly is carried out Austria by the present invention
Then family name's body ageing treatment successively carries out subzero treatment and ageing treatment, obtains superhigh intensity height without being reheated
The Maraging steel of toughness.
In a specific embodiment of the present invention, the temperature of the austenaging processing is preferably 680~720 DEG C, more excellent
700 DEG C are selected as, the time is preferably 2~4h, more preferably 3h；The austenaging processing carries out preferably in heat-treatment furnace.
After the completion of austenaging processing, preferably by treated, blank carries out subzero treatment to the present invention.The present invention is preferred
By austenaging, treated that blank is air-cooled to room temperature, then carries out subzero treatment again；The subzero treatment is preferably by base
Material is put into holding 2h or more in liquid nitrogen.
After the completion of subzero treatment, by treated, blank carries out ageing treatment to the present invention.The present invention is preferably by subzero treatment
Blank afterwards is air-cooled to room temperature, then carries out ageing treatment again；The temperature of the ageing treatment is preferably 480~520 DEG C, more excellent
500 DEG C are selected as, the time is 1~3h, more preferably 2h.
After the completion of ageing treatment, it is of the invention to get arriving that the blank after ageing treatment is preferably air-cooled to room temperature by the present invention
The Maraging steel of ultrahigh-intensity high-toughness.
The tensile strength > 3000Mpa of ultrahigh-intensity high-toughness Maraging steel described in above scheme of the present invention, surrender
Intensity > 2700Mpa, elongation percentage > 10%.In the present invention, the crucial copper content for being to adjust in Maraging steel and auxiliary
With reasonable continuous alternate heat treatment combination, it should be understood that the aging strengthening model of conventional martensitic aged steel is logical
It is often to be reheated to higher than 800 DEG C progress at least 2h solution treatment after forging, is air-cooled to room temperature, is then kept in liquid nitrogen
Long period (being greater than 5h) just can get full martensitic matrix, finally carries out aging strengthening model again and obtains strengthening effect.And this hair
Bright final forging temperature is not less than 850 DEG C, and 680~720 DEG C of heat treatment is directly carried out after finish-forging and carries out austenaging, is on the one hand saved
It has gone to reheat solution treatment, has saved electric energy and preparation link, achieved the purpose that cost efficiency；On the other hand, 680
~720 DEG C of heat treatments, which carry out austenaging, makes it from compound between precipitating metal in austenite and copper-rich phase, such as Ni3Ti, richness
Cu phase.Then austenitic alloy content reduces, and martensite, which starts transition point (Ms) and martensite, terminates transition point (Mf) rising, with
Austenite is largely converted into martensite when cooling down afterwards.The cold treatment of short period is only carried out in age-hardening processing in this way, i.e.,
It can guarantee and obtain complete martensite transfor mation, reach the dual purpose of martensite strengthening and precipitation strength.
The present invention also provides ultrahigh-intensity high-toughness Maraging steel described in above scheme or above-mentioned technical proposal institutes
State the application of ultrahigh-intensity high-toughness Maraging steel that preparation method is prepared as weaving crochet hook or nailing gun striker.
Below with reference to embodiment to the Maraging steel and preparation method thereof of ultrahigh-intensity high-toughness provided by the invention
It is described in detail, but they cannot be interpreted as limiting the scope of the present invention.
Embodiment 1
A kind of preparation method of the Maraging steel of ultrahigh-intensity high-toughness: it comprises the following steps that
(1) by Fe, Ni, Co, Cu, Ti, Mo superpure metal raw material carry out ingredient, mixing be placed in vaccum sensitive stove into
The first vacuum induction melting of row, smelting temperature are 1550 DEG C, and teeming is simultaneously processed into consutrode, in consumable electrode vacuum furnace into
Row double refining；
(2) steel ingot being cast into after refining is placed in homogenize in heat-treatment furnace and is heat-treated, be warming up to 1200 DEG C, heat preservation
26h；
(3) steel ingot after Homogenization Treatments is carried out forging processing and obtain blank: just forging temperature is 1150 DEG C, steel ingot the 1st
The secondary deflection that forges is 4%, and it is 8% that the 2nd time, which forges deflection, and it is 12% that the 3rd time, which forges deflection, the total deformation after finish-forging
It is 92%, final forging temperature is 900 DEG C, forging ratio 14.
(4) blank is subjected to austenaging processing: puts into 700 DEG C of heat-treatment furnaces and keep the temperature 3h, is then air-cooled to room temperature；
Blank after austenaging is subjected to subzero treatment: keeping 3h in liquid nitrogen, is air-cooled to room temperature；
Liquid nitrogen treated blank is subjected to ageing treatment: keeping the temperature 2h in 500 DEG C of heat-treatment furnaces, is air-cooled to room temperature, obtains
To the Maraging steel of ultrahigh-intensity high-toughness.
Product chemical component (weight percent) prepared by the embodiment 1 measured is as follows: Ni:19.2%, Co:16.3%,
Mo:7.3%, Ti:1.6%, Cu:5.5%, C:0.003%, O:0.0008%, N:0.001%, P:0.0009%, S:
0.0007%.
Its mechanical property is tensile strength 3054MPa, yield strength 2832MPa, elongation percentage 11.5% after measured.
Embodiment 2
A kind of Maraging steel of ultrahigh-intensity high-toughness, preparation method is with embodiment 1, but raw material ratio is slightly
Adjustment, product chemical component (weight percent) prepared by the embodiment 2 measured are as follows: Ni:18.2%, Co:15.7%, Mo:
7.4%, Ti:1.6%, Cu:5.1%, C:0.002%, O:0.0008%, N:0.001%, P:0.0008%, S:0.0006%.
Its mechanical property is tensile strength 3014MPa, yield strength 2722MPa, elongation percentage 10.5% after measured.
Embodiment 3
A kind of Maraging steel of ultrahigh-intensity high-toughness, preparation method is with embodiment 1, but raw material ratio is slightly
Adjustment, product chemical component (weight percent) prepared by the embodiment 3 measured are as follows: Ni:19.0%, Co:17.5%, Mo:
7.2%, Ti:1.5%, Cu:5.2%, C:0.001%, O:0.0008%, N:0.0015%, P:0.0008%, S:
0.0007%.
Its mechanical property is tensile strength 3025MPa, yield strength 2713MPa, elongation percentage 10.5% after measured.
Embodiment 4
A kind of Maraging steel of ultrahigh-intensity high-toughness, preparation method is with embodiment 1, but raw material ratio is slightly
Adjustment, product chemical component (weight percent) prepared by the embodiment 4 measured are as follows: Ni:18.9%, Co:16.1%, Mo:
7.2%, Ti:1.6%, Cu:4.1%, C:0.002%, O:0.0008%, N:0.0016%, P:0.0009%, S:
0.0006%.
Its mechanical property is tensile strength 3005MPa, yield strength 2703MPa, elongation percentage 10.2% after measured.
Embodiment 5
A kind of Maraging steel of ultrahigh-intensity high-toughness, preparation method is with embodiment 1, but raw material ratio is slightly
Adjustment, product chemical component (weight percent) prepared by the embodiment 5 measured are as follows: Ni:18.7%, Co:16.2%, Mo:
7.7%, Ti:2.3%, Cu:5.6%, C:0.001%, O:0.0005%, N:0.0009%, P:0.0008%, S:
0.0005%.
Its mechanical property is tensile strength 3033MPa, yield strength 2721MPa, elongation percentage 10.1% after measured.
By controlling the proportion of Ni, Co, Cu, Ti, Mo raw metal it can be seen from 1-5 of the embodiment of the present invention, in this hair
The Maraging steel that the metallic element in preferred amount ranges that bright technical solution provides is prepared can obtain more preferably
Toughness and tenacity matching.
Comparative example 1
A kind of Maraging steel of ultrahigh-intensity high-toughness, preparation method is with embodiment 1, but its raw material is not used
With embodiment 1, product chemical component (weight percent) prepared by the comparative example 1 measured is as follows for copper, other raw material and proportion:
Ni:19.4%, Co:16.0%, Mo:7.2%, Ti:1.7%, C:0.004%, O:0.0009%, N:0.001%, P:
0.0008%, S:0.0005%.
Its mechanical property is tensile strength 2913MPa, yield strength 2786MPa, elongation percentage 9.2%.
The comparison embodiment of the present invention 1 and comparative example 1 can find that Cu is added in the embodiment of the present invention 1 in Maraging steel
Afterwards, tensile strength, yield strength and elongation percentage have promotion, it is seen then that the present invention is added copper and adjusts preferred scope
Cu content can be obviously improved the obdurability of Maraging steel.
Comparative example 2
A kind of Maraging steel of ultrahigh-intensity high-toughness, raw material and same as Example 1, the difference of proportion
It is, the forging parameter adjustment of step in preparation method (3) is as follows:
(3) steel ingot after Homogenization Treatments is carried out forging processing and obtain blank: just forging temperature is 1150 DEG C, steel ingot the 1st
The secondary deflection that forges is 10%, and it is 15% that the 2nd time, which forges deflection, and it is 20% that the 3rd time, which forges deflection, steel billet in forging process
There is cracking phenomena, leads to blank preparation failure.
The comparison embodiment of the present invention 1 and comparative example 2 can find that it is unsuitable to forge deflection steel ingot the 1-3 times in forging process
It is excessive, it otherwise will will appear cracking phenomena, and influence blank performance.
Comparative example 3
A kind of preparation method of the Maraging steel of ultrahigh-intensity high-toughness: it comprises the following steps that
(1) superpure metal raw material is not used, higher Fe, Ni, Co, Cu, Ti, Mo raw material metal of impurity content is carried out
Ingredient, mixing, which is placed in vaccum sensitive stove, carries out first vacuum induction melting, and teeming is simultaneously processed into consutrode, in vacuum
Double refining is carried out in self-consuming furnace；
(2) steel ingot being cast into after refining is placed in homogenize in heat-treatment furnace and is heat-treated, be warming up to 1180 DEG C, heat preservation
26h；
(3) steel ingot after homogenization heat treatment is carried out forging processing and obtains blank: just forging temperature is 1120 DEG C, steel ingot the
It is 4% that 1 time, which forges deflection, and it is 7% that the 2nd time, which forges deflection, and it is 14% that the 3rd time, which forges deflection, the total deformation after finish-forging
Amount is 91%, and final forging temperature is 870 DEG C, forging ratio 13.
(4) blank is subjected to austenaging processing: puts into 680 DEG C of heat-treatment furnaces and keep the temperature 3h, is then air-cooled to room temperature；
Blank after austenaging is subjected to subzero treatment: keeping 3h in liquid nitrogen, is air-cooled to room temperature；
Liquid nitrogen treated blank is subjected to ageing treatment: keeping the temperature 2h in 500 DEG C of heat-treatment furnaces, is air-cooled to room temperature, obtains
To the Maraging steel of ultrahigh-intensity high-toughness.
Product chemical component (weight percent) prepared by the comparative example 3 measured is as follows: Ni:19.1%, Co:15.7%,
Mo:7.3%, Ti:1.7%, Cu:5.4%, C:0.01%, O:0.003%, N:0.02%, P:0.005%, S:0.005%.
Its mechanical property is tensile strength 3012MPa, yield strength 2792MPa, elongation percentage 6.5% after measured.
The comparison embodiment of the present invention 1 and comparative example 3 can be found, if not controlling the purity of raw metal, the mistake of melting forging
Impurity element C, O, N, P, S cannot get stringent limitation in journey, although tensile strength can reach 3000MPa, elongation percentage is sharply
Decline.
The above is only a preferred embodiment of the present invention, it is noted that for the ordinary skill people of the art
For member, various improvements and modifications may be made without departing from the principle of the present invention, these improvements and modifications are also answered
It is considered as protection scope of the present invention.
Claims (10)
1. a kind of Maraging steel of ultrahigh-intensity high-toughness, which is characterized in that based on mass content, the martensite ag(e)ing
The chemical composition of steel are as follows: Ni:18.0-20.0%, Co:15.0-18.0%, Mo:7.0-8.0%, Ti:1.5-2.5%,
Cu:4.0-6.0%, C < 0.005%, O < 0.001%, N < 0.002%, P < 0.001%, S < 0.001%, surplus Fe；
The total content < 0.01% of described C, O, N, P, S.
2. the Maraging steel of ultrahigh-intensity high-toughness according to claim 1, which is characterized in that when the martensite
Imitate the chemical composition of steel are as follows: Ni:18.5-19.5%, Co:15.5-16.5%, Mo:7.0-7.5%, Ti:1.5-1.8%,
Cu:5.0-6.0%, C < 0.005%, O < 0.001%, N < 0.002%, P < 0.001%, S < 0.001%, surplus Fe.
3. the Maraging steel of ultrahigh-intensity high-toughness according to claim 1 or 2, which is characterized in that the geneva
The tensile strength > 3000Mpa of body aged steel, yield strength > 2700Mpa, elongation percentage > 10%.
4. the preparation method of the Maraging steel of ultrahigh-intensity high-toughness described in claims 1 to 3 any one, feature exist
In including the following steps:
(1) superpure metal raw material are successively subjected to first vacuum induction melting and double refining under vacuum, obtain steel ingot；
(2) steel ingot in the step (1) is subjected to homogenization heat treatment；
(3) steel ingot after homogenization heat treatment in the step (2) is directly forged, obtains blank；
(4) blank in the step (3) is subjected to continuous heat, the continuous heat is that the blank after forging is direct
Austenaging processing, subzero treatment and ageing treatment are carried out, the Maraging steel of ultrahigh-intensity high-toughness is obtained.
5. the preparation method according to claim 4, which is characterized in that the first vacuum induction melting in the step (1)
It is carried out in vaccum sensitive stove, the temperature of the first vacuum induction melting is 1450~1550 DEG C, vacuum degree < 1 × 10-4Pa。
6. the preparation method according to claim 4, which is characterized in that double refining in the step (1) vacuum from
It is carried out in consumption furnace, vacuum degree < 1 × 10-4Pa。
7. the preparation method according to claim 4, which is characterized in that the homogenization heat treatment in the step (2) is specific
Are as follows: it will be kept the temperature after Heating Steel Ingots, the temperature of the heat preservation is 1170~1230 DEG C, and the time of the heat preservation is 24~30h.
8. the preparation method according to claim 4, which is characterized in that the first forging temperature of forging is in the step (3)
1100~1200 DEG C, final forging temperature is not less than 850 DEG C；The deflection of the forging needs to meet: the 1st forging deformation amount < 5%,
2nd forging deformation amount < 10%, the 3rd forging deformation amount < 15%, total deformation >=90% after finish-forging, forging ratio >
12。
9. the preparation method according to claim 4, which is characterized in that continuous heat in the step (4) specifically: will
Blank after forging directly puts 2~4h of heat preservation in 680~720 DEG C of heat-treatment furnaces into, carries out austenaging, is then air-cooled to room
Temperature；Blank after austenaging is kept into 2h or more in liquid nitrogen, is air-cooled to room temperature；By liquid nitrogen treated blank 480
1~3h is kept the temperature in~520 DEG C of heat-treatment furnace, is air-cooled to room temperature.
10. the Maraging steel or claim 4~9 times of ultrahigh-intensity high-toughness described in claims 1 to 3 any one
The Maraging steel of the ultrahigh-intensity high-toughness of the preparation method preparation of meaning one is as weaving crochet hook or nailing gun striker
Application.
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| CN113755677A (en) * | 2021-08-30 | 2021-12-07 | 中国科学院金属研究所 | Ultra-high strength and high toughness maraging steel with superfine substructure and preparation method thereof |
| CN115369332A (en) * | 2022-08-24 | 2022-11-22 | 中航上大高温合金材料股份有限公司 | Maraging ultrahigh-strength steel and preparation method thereof |
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