CN109112425B - Ultra-high strength and high toughness maraging steel and preparation method and application thereof - Google Patents
Ultra-high strength and high toughness maraging steel and preparation method and application thereof Download PDFInfo
- Publication number
- CN109112425B CN109112425B CN201811338298.1A CN201811338298A CN109112425B CN 109112425 B CN109112425 B CN 109112425B CN 201811338298 A CN201811338298 A CN 201811338298A CN 109112425 B CN109112425 B CN 109112425B
- Authority
- CN
- China
- Prior art keywords
- less
- forging
- heat treatment
- maraging steel
- blank
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
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
Abstract
The invention provides a maraging steel with ultrahigh strength and high toughness, which comprises the following chemical components in percentage by mass: 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 less than 0.005%, O less than 0.001%, N less than 0.002%, P less than 0.001%, S less than 0.001%, and the balance of Fe; the total content of C, O, N, P, S is less than 0.01%. The martensite aging steel with ultrahigh strength and high toughness of the invention forms copper-rich phase and Ni3The Ti core-shell structure realizes the composite reinforcement of soft and hard nano particles without losing toughness, the tensile strength is more than 3000Mpa, the yield strength is more than 2700Mpa, the elongation is more than 10 percent, and the requirements of cost reduction and efficiency improvement of consumables such as textile crochet hooks, nail gun firing pins and the like are met.
Description
Technical Field
The invention relates to the technical field of maraging steel, in particular to ultrahigh-strength high-toughness maraging steel and a preparation method and application thereof.
Background
The high-strength low-alloy steel always becomes the preferred material for manufacturing enterprises focusing on high-strength structural members such as textile crochet hooks, firing pins and the like by virtue of the advantage of material cost. The maraging steel is an ultra-high strength steel which takes carbon-free (or micro-carbon) martensite as a matrix and can generate intermetallic compound precipitation hardening during aging, and unlike the traditional high-strength low alloy steel, the maraging steel is strengthened by the dispersion precipitation of the intermetallic compounds without carbon, so that the maraging steel has some unique properties: high strength and toughness, low hardening index, good formability, simple heat treatment process, almost no deformation of maraging steel during heat treatment, and good welding performance. Compared with high-strength low-alloy steel, maraging steel has the advantages of obvious strength and toughness and the like, but cannot be accepted by related enterprises for realizing industrial application.
In the development process of maraging steel, strength and toughness matching and use cost are two core problems influencing the application prospect of maraging steel, on one hand, the strength of maraging steel is improved on the premise of ensuring toughness, the design aims of light weight, energy conservation, emission reduction, safety, environmental protection and the like of products are met, and the method is a key factor determining the application prospect of maraging steel; on the other hand, compared with the common high-strength low-alloy steel, the maraging steel has obvious strength and toughness advantages, but because the maraging steel uses high-content alloy elements such as nickel, cobalt, molybdenum, titanium and the like, the material cost of the maraging steel is higher, and the maraging steel is difficult to popularize in practical application. Therefore, how to fully utilize the performance advantages of the maraging steel and reduce the overall production cost of the structural material is the key influencing the application prospect of the maraging steel.
Disclosure of Invention
In view of the above, the invention aims to provide the maraging steel with ultrahigh strength and high toughness as well as the preparation method and the application thereof, the invention develops the maraging steel with ultrahigh strength and high toughness, the tensile strength of which is more than 3000MPa, the yield strength of which is more than 2700MPa and the elongation of which is more than 10 percent by adding copper element to optimize the proportion of alloy raw materials and assisting double vacuum smelting, continuous forging and continuous heat treatment processes, thereby realizing cost reduction and efficiency improvement of materials of a textile crochet hook and a nail gun firing pin.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides a maraging steel with ultrahigh strength and high toughness, which comprises the following chemical components in percentage by mass: 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 less than 0.005%, O less than 0.001%, N less than 0.002%, P less than 0.001%, S less than 0.001%, and the balance of Fe; the total content of C, O, N, P, S is less than 0.01%.
Preferably, the maraging steel has the following chemical composition components: 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 less than 0.005%, O less than 0.001%, N less than 0.002%, P less than 0.001%, S less than 0.001%, and the balance Fe.
Preferably, the tensile strength of the maraging steel is more than 3000Mpa, the yield strength is more than 2700Mpa, and the elongation is more than 10%.
The invention also provides a preparation method of the maraging steel with ultrahigh strength and high toughness, which comprises the following steps:
(1) sequentially carrying out primary vacuum induction melting and secondary refining on an ultrapure metal raw material under vacuum to obtain a steel ingot;
(2) carrying out homogenization heat treatment on the steel ingot in the step (1);
(3) directly forging the steel ingot subjected to the homogenization heat treatment in the step (2) to obtain a blank;
(4) and (4) carrying out continuous heat treatment on the blank in the step (3), wherein the continuous heat treatment is to directly carry out austenitic aging treatment, cryogenic treatment and aging treatment on the forged blank to obtain the maraging steel with ultrahigh strength and high toughness.
Preferably, the primary vacuum induction melting in the step (1) is carried out in a vacuum induction furnace, the temperature of the primary vacuum induction melting is 1450-1550 ℃, and the vacuum degree is less than 1 × 10-4Pa。
Preferably, the secondary refining in the step (1) is carried out in a vacuum consumable electrode furnace with a vacuum degree of < 1X 10-4Pa。
Preferably, the homogenization heat treatment in the step (2) is specifically: and heating the steel ingot, and then carrying out heat preservation, wherein the heat preservation temperature is 1170-1230 ℃, and the heat preservation time is 24-30 h.
Preferably, the initial forging temperature of the forging in the step (3) is 1100-1200 ℃, and the final forging temperature is not lower than 850 ℃; the deformation of the forging is required to meet the following requirements: the 1 st forging deformation is less than 5%, the 2 nd forging deformation is less than 10%, the 3 rd forging deformation is less than 15%, the total deformation after finish forging is more than or equal to 90%, and the forging ratio is more than 12.
Preferably, the continuous heat treatment in the step (4) is specifically: directly putting the forged blank into a 680-720 ℃ heat treatment furnace, preserving heat for 2-4 h, carrying out austenite aging, and then air-cooling to room temperature; keeping the blank subjected to austenite aging in liquid nitrogen for more than 2h, and cooling the blank to room temperature in air; and (3) preserving the blank treated by the liquid nitrogen in a heat treatment furnace at 480-520 ℃ for 1-3 h, and air-cooling to room temperature.
The invention also provides application of the ultra-high strength and high toughness maraging steel or the ultra-high strength and high toughness maraging steel prepared by the preparation method as a firing pin of a textile crochet hook or a nail gun.
Has the advantages that: the invention provides a maraging steel with ultrahigh strength and high toughness, which comprises the following chemical components in percentage by mass: 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 less than 0.005%, O less than 0.001%, N less than 0.002%, P less than 0.001%, S less than 0.001%, and the balance of Fe; the total content of C, O, N, P, S is less than 0.01%. The invention improves the content of copper element, optimizes the proportion of other noble metals and effectively reduces the cost, and strictly controls the impurity elements in the alloy so as to prevent C, O, N, P, S element from being too high to influence the toughness of the maraging steel.
The invention provides a preparation method of the maraging steel with ultrahigh strength and high toughness, which is characterized in that raw materials are smelted and secondarily refined under vacuum to obtain a steel ingot, and then metal elements in the steel ingot are homogenized through homogenization heat treatment; the invention combines the homogenization heat treatment with the multiple continuous hot forging to ensure that the steel ingot is gradually deformed to obtain the blank; the invention directly carries out the austenitic aging treatment, the cryogenic treatment and the aging treatment on the blank to obtain the maraging steel with ultrahigh strength and high toughness, simplifies the heat treatment process and reduces the total production cost. The invention forms copper-rich phase and Ni in the obtained maraging steel alloy through continuous heat treatment3The Ti core-shell structure realizes the composite strengthening of soft and hard nano particles without losing the toughness of the maraging steel.
The embodiment result shows that the tensile strength of the maraging steel is more than 3000Mpa, the yield strength is more than 2700Mpa, the elongation is more than 10%, the cost reduction and the efficiency improvement are realized, and the requirements of consumables such as a textile crochet hook, a nail gun firing pin and the like are met.
Detailed Description
The invention provides a maraging steel with ultrahigh strength and high toughness, which comprises the following chemical components in percentage by mass: 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 less than 0.005%, O less than 0.001%, N less than 0.002%, P less than 0.001%, S less than 0.001%, and the balance of Fe; the total content of C, O, N, P, S is less than 0.01%.
The design idea of the invention is as follows: copper element is added into the existing maraging steel system, the mass ratio of other alloy elements in the maraging steel is optimized, and the purpose of reducing the cost is achieved by combining continuous implementation of forging and heat treatment; in the present invention, Cu is an austenite forming element in the maraging steel, lowers the martensite start temperature, and has extremely low solid solubility in martensite, so that it has an extremely high strengthening effect after the aging treatment of the maraging steel, and does not lose toughness. Meanwhile, Cu is preferentially precipitated in the aging treatment process and can be an intermetallic compound Ni3Ti plays a role of nucleation particles to form a copper-rich phase and Ni3The Ti core-shell structure realizes the composite reinforcement of soft and hard nano particles and has higher reinforcement effect. The inventors found that the addition of Cu as a nucleation site should not be too small, and that too small a Cu content and Ni content3Ti is simultaneously separated out, a core-shell structure cannot be formed, and the strengthening effect is not ideal; however, excessive Cu easily causes the 'hot brittleness' cracking phenomenon of the steel in the forging process, and the yield is influenced.
In the present invention, the chemical composition of the maraging steel includes, in mass content, Ni: 18.0-20.0%, preferably 18.5-19.5%, more preferably 19%;
the maraging steel of the invention further comprises, in terms of mass content, Co: 15.0-18.0%, preferably 15.5-16.5%, more preferably 16%;
the maraging steel of the invention further comprises, in terms of mass content, Mo: 7.0-8.0%, preferably 7.0-7.5%, more preferably 7.3%;
the maraging steel of the invention further comprises the following chemical components in percentage by mass: 1.5-2.5%, preferably 1.5-1.8%, more preferably 1.6%;
the maraging steel of the invention further comprises, in terms of mass content, Cu: 4.0-6.0%, preferably 4.0-6.0%, more preferably 5%;
in the invention, the maraging steel is prepared by adopting ultra-pure metal raw materials (Fe, Ni, Co, Cu, Ti and Mo) to obtain the maraging steel with high purity and extremely low impurity, wherein the purity of the ultra-pure metal raw materials is more than 99.99%, and the control of C, O, N, P, S content in the smelting and continuous forging processes of the maraging steel is more facilitated. The source of the ultrapure metal raw material (Fe, Ni, Co, Cu, Ti, Mo) is not particularly limited in the present invention, and commercially available ultrapure metal raw materials known to those skilled in the art may be used.
The invention provides a preparation method of the maraging steel with ultrahigh strength and high toughness, which comprises the following steps:
(1) sequentially carrying out primary vacuum induction melting and secondary refining on an ultrapure metal raw material under vacuum to obtain a steel ingot;
(2) carrying out homogenization heat treatment on the steel ingot in the step (1);
(3) directly forging the steel ingot subjected to the homogenization heat treatment in the step (2) to obtain a blank;
(4) and (4) carrying out continuous heat treatment on the blank in the step (3), wherein the continuous heat treatment is to directly carry out austenitic aging treatment, cryogenic treatment and aging treatment on the forged blank to obtain the maraging steel with ultrahigh strength and high toughness.
The method comprises the step of sequentially carrying out primary vacuum induction melting and secondary refining on an ultra-pure metal raw material under vacuum to obtain a steel ingot.
In the specific embodiment of the invention, the Fe, Ni, Co, Cu, Ti and Mo ultra-pure metal raw materials are preferably firstly proportioned, the proportioning is pre-configured according to the designed preferable dosage range of each metal element, and the loss in the later smelting treatment process is ignored.
According to the invention, the prepared ultrapure metal raw materials are preferably mixed and then placed in a vacuum induction furnace for primary vacuum induction melting, wherein the temperature of the primary vacuum induction melting is preferably 1450-1550 ℃, more preferably 1500-1550 ℃, and further preferably 1550 ℃; the vacuum degree in the vacuum induction furnace is preferably less than 1 x 10-4Pa。
The invention preferably casts the melted molten steel into steel ingots and processes the steel ingots into consumable electrodes, and then carries out secondary refining, the invention adopts a vacuum consumable furnace for secondary refining, and the vacuum degree in the vacuum consumable furnace is preferably less than 1 x 10-4Pa. The invention carries out homogenization heat treatment on the steel ingot obtained after secondary refining. In the invention, the homogenization heat treatment is to heat the steel ingot and then carry out heat preservation, the heat preservation temperature is preferably 1170-1230 ℃, more preferably 1190-1210 ℃, further preferably 1200 ℃, and the heat preservation time is preferably 24-30 h, more preferably 25-27 h, further preferably 26 h. The invention homogenizes the metal elements in the steel ingot through homogenization heat treatment, and eliminates the defects in the casting process.
The steel ingot after the homogenization heat treatment is directly forged to obtain a blank. In the invention, the forging preferably adopts a continuous multiple hot forging process, the continuous multiple hot forging process is to directly forge the blank subjected to the homogenization heat treatment for multiple times at a proper temperature without reheating, the deformation of each forging is gradually increased, and the steel ingot after the forging is finished cannot be lower than a set temperature, and the method specifically comprises the following steps: the initial forging temperature of the steel ingot during forging is preferably 1100-1200 ℃, and the final forging temperature is preferably not lower than 850 ℃; the forging deformation amount preferably satisfies: the 1 st forging deformation is less than 5%, the 2 nd forging deformation is less than 10%, the 3 rd forging deformation is less than 15%, the total deformation after finish forging is more than or equal to 90%, and the forging ratio is more than 12. The invention adopts a mode of directly carrying out continuous hot forging on the blank subjected to the homogenization heat treatment for multiple times, thereby not only preventing the steel ingot from cracking and ensuring the compactness and uniformity of elements in the steel ingot, but also saving secondary heating and reducing the production cost.
According to the invention, the blank obtained by forging is subjected to continuous heat treatment, wherein the continuous heat treatment is to directly perform austenite aging treatment, cryogenic treatment and aging treatment on the forged blank. According to the invention, the blank obtained by forging is preferably directly subjected to the austenite aging treatment without reheating, and then is subjected to the cryogenic treatment and the aging treatment in sequence to obtain the maraging steel with ultrahigh strength and high toughness.
In the specific embodiment of the invention, the temperature of the austenite aging treatment is preferably 680-720 ℃, more preferably 700 ℃, and the time is preferably 2-4 h, more preferably 3 h; the austenitic aging treatment is preferably carried out in a heat treatment furnace.
After the austenitic aging treatment is completed, the invention preferably carries out cryogenic treatment on the treated blank. The blank after the austenite aging treatment is preferably cooled to room temperature by air, and then is subjected to cryogenic treatment; the cryogenic treatment is preferably carried out by placing the blank in liquid nitrogen for more than 2 hours.
After the cryogenic treatment is finished, the invention carries out aging treatment on the treated blank. The blank after the cryogenic treatment is preferably cooled to room temperature by air, and then the aging treatment is carried out; the temperature of the aging treatment is preferably 480-520 ℃, more preferably 500 ℃, and the time is 1-3 hours, more preferably 2 hours.
After the aging treatment is finished, the blank after the aging treatment is preferably cooled to room temperature in air, and the ultra-high strength and high toughness maraging steel is obtained.
The tensile strength of the maraging steel with ultrahigh strength and high toughness is more than 3000Mpa, the yield strength is more than 2700Mpa, and the elongation is more than 10%. In the invention, the key point is to adjust the copper content in the maraging steel and assist the combination of reasonable continuous alternate heat treatment means, and the following points need to be explained: heat of ageing of conventional maraging steelThe treatment is generally to heat to more than 800 ℃ after forging for at least 2h of solution treatment, air-cool to room temperature, then keep for a longer time (more than 5h) in liquid nitrogen to obtain a full martensite matrix, and finally carry out aging heat treatment to obtain the strengthening effect. The final forging temperature is not lower than 850 ℃, and heat treatment at 680-720 ℃ is directly carried out for austenite aging after the final forging, so that the reheating solid solution treatment is omitted, the electric energy and the preparation link are saved, and the purposes of cost reduction and efficiency improvement are achieved; on the other hand, heat treatment at 680-720 ℃ is carried out to carry out austenite aging so as to precipitate intermetallic compounds and copper-rich phases, such as Ni, from austenite3Ti, Cu-rich phase. The austenite alloy content is then reduced, the martensite start transformation point (Ms) and the martensite finish transformation point (Mf) are raised, and the austenite is mostly transformed into martensite upon subsequent cooling. Thus, only a short time of cold treatment is carried out in the age hardening treatment, thereby ensuring that complete martensite transformation is obtained and achieving the dual purposes of martensite strengthening and precipitation strengthening.
The invention also provides application of the ultra-high strength and high toughness maraging steel prepared by the above technical scheme or the ultra-high strength and high toughness maraging steel prepared by the above technical scheme as a textile crochet hook or a firing pin of a nail gun.
The ultra-high strength and high toughness maraging steel provided by the present invention and the method for producing the same will be described in detail with reference to the following examples, but they should not be construed as limiting the scope of the present invention.
Example 1
A preparation method of maraging steel with ultrahigh strength and high toughness comprises the following steps: the method comprises the following steps:
(1) proportioning Fe, Ni, Co, Cu, Ti and Mo ultra-pure metal raw materials, mixing, placing in a vacuum induction furnace for primary vacuum induction melting at the melting temperature of 1550 ℃, casting a steel ingot and processing into a consumable electrode, and carrying out secondary refining in the vacuum consumable furnace;
(2) placing the steel ingot cast after refining in a heat treatment furnace for homogenization heat treatment, heating to 1200 ℃, and preserving heat for 26 hours;
(3) forging the homogenized steel ingot to obtain a blank: the initial forging temperature is 1150 ℃, the 1 st forging deformation of the steel ingot is 4%, the 2 nd forging deformation is 8%, the 3 rd forging deformation is 12%, the total deformation after the final forging is 92%, the final forging temperature is 900 ℃, and the forging ratio is 14.
(4) Carrying out austenite aging treatment on the blank: putting the mixture into a heat treatment furnace at 700 ℃ for heat preservation for 3 hours, and then air-cooling the mixture to room temperature;
carrying out cryogenic treatment on the blank subjected to austenite aging: keeping the mixture in liquid nitrogen for 3 hours, and cooling the mixture to room temperature in air;
and (3) aging the blank treated by the liquid nitrogen: and (3) preserving the heat for 2 hours in a heat treatment furnace at 500 ℃, and air-cooling to room temperature to obtain the maraging steel with ultrahigh strength and high toughness.
The chemical composition (weight percent) of the product prepared in example 1 was measured 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 percent.
The mechanical property is determined to be tensile strength of 3054MPa, yield strength of 2832MPa and elongation of 11.5 percent.
Example 2
The preparation method of the maraging steel with ultrahigh strength and high toughness is the same as that of the maraging steel in example 1, but the raw material proportion is slightly adjusted, and the measured chemical components (weight percentage) of the product prepared in example 2 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 percent.
The mechanical property of the material is measured to be 3014MPa of tensile strength, 2722MPa of yield strength and 10.5 percent of elongation.
Example 3
The preparation method of the maraging steel with ultrahigh strength and high toughness is the same as that of the maraging steel in example 1, but the raw material proportion is slightly adjusted, and the chemical components (weight percentage) of the product prepared in example 3 are measured 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 percent.
The mechanical property is measured to be tensile strength 3025MPa, yield strength 2713MPa, and elongation 10.5%.
Example 4
The preparation method of the maraging steel with ultrahigh strength and high toughness is the same as that of the maraging steel in example 1, but the raw material proportion is slightly adjusted, and the chemical components (weight percentage) of the product prepared in example 4 are measured 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 percent.
The mechanical property is determined to be tensile strength of 3005MPa, yield strength of 2703MPa and elongation of 10.2%.
Example 5
The preparation method of the maraging steel with ultrahigh strength and high toughness is the same as that of the maraging steel in example 1, but the raw material proportion is slightly adjusted, and the measured chemical composition (weight percentage) of the product prepared in example 5 is 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 percent.
The mechanical property is determined to be tensile strength 3033MPa, yield strength 2721MPa, and elongation is 10.1%.
It can be seen from examples 1-5 of the present invention that by controlling the ratio of the metal raw materials of Ni, Co, Cu, Ti, and Mo, the maraging steel prepared with the metal elements in the preferred dosage range provided by the technical scheme of the present invention can obtain better toughness performance matching.
Comparative example 1
The preparation method of the maraging steel with ultrahigh strength and high toughness is the same as that of the maraging steel in example 1, but copper is not used as raw materials, other raw materials and the mixture ratio are the same as that of the maraging steel in example 1, and the chemical compositions (weight percentage) of the product prepared in comparative example 1 are measured as follows: 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 percent.
The mechanical property is 2913MPa of tensile strength, 2786MPa of yield strength and 9.2% of elongation.
Comparing example 1 of the present invention with comparative example 1, it can be found that the tensile strength, yield strength and elongation of the maraging steel of example 1 of the present invention are all improved after adding Cu to the maraging steel, and it can be seen that the toughness of the maraging steel can be significantly improved by adding Cu and adjusting the Cu content in the preferred range.
Comparative example 2
The raw materials and the mixture ratio of the maraging steel with ultrahigh strength and high toughness are the same as those in the example 1, except that the forging parameters in the step (3) in the preparation method are adjusted as follows:
(3) forging the homogenized steel ingot to obtain a blank: the initial forging temperature is 1150 ℃, the 1 st forging deformation of the steel ingot is 10%, the 2 nd forging deformation is 15%, and the 3 rd forging deformation is 20%, and the steel billet cracks in the forging process, so that the blank preparation fails.
Comparing example 1 and comparative example 2 of the invention, it can be found that the deformation of the steel ingot in the 1 st to 3 rd forging is not too large in the forging process, otherwise, the cracking phenomenon will occur, and the blank performance will be affected.
Comparative example 3
A preparation method of maraging steel with ultrahigh strength and high toughness comprises the following steps: the method comprises the following steps:
(1) the method comprises the following steps of (1) preparing Fe, Ni, Co, Cu, Ti and Mo metal raw materials with high impurity content without using an ultra-pure metal raw material, mixing, placing in a vacuum induction furnace for primary vacuum induction smelting, casting steel ingots, processing into consumable electrodes, and performing secondary refining in the vacuum consumable furnace;
(2) placing the steel ingot cast after refining in a heat treatment furnace for homogenization heat treatment, heating to 1180 ℃, and preserving heat for 26 hours;
(3) forging the steel ingot after the homogenization heat treatment to obtain a blank: the initial forging temperature is 1120 ℃, the 1 st forging deformation of the steel ingot is 4%, the 2 nd forging deformation is 7%, the 3 rd forging deformation is 14%, the total deformation after final forging is 91%, the final forging temperature is 870 ℃, and the forging ratio is 13.
(4) Carrying out austenite aging treatment on the blank: putting the mixture into a 680 ℃ heat treatment furnace for heat preservation for 3 hours, and then air-cooling the mixture to room temperature;
carrying out cryogenic treatment on the blank subjected to austenite aging: keeping the mixture in liquid nitrogen for 3 hours, and cooling the mixture to room temperature in air;
and (3) aging the blank treated by the liquid nitrogen: and (3) preserving the heat for 2 hours in a heat treatment furnace at 500 ℃, and air-cooling to room temperature to obtain the maraging steel with ultrahigh strength and high toughness.
The chemical composition (weight percent) of the product prepared in comparative example 3 was measured 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 percent.
The mechanical property of the material is measured to be 3012MPa of tensile strength, 2792MPa of yield strength and 6.5 percent of elongation.
Comparing example 1 of the present invention with comparative example 3, it was found that the impurity element C, O, N, P, S was not strictly limited during the melt forging process without controlling the purity of the metal raw material, and the elongation was drastically decreased although the tensile strength could reach 3000 MPa.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.
Claims (10)
1. The ultra-high strength and high toughness maraging steel is characterized by comprising the following chemical components in percentage by mass: 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 less than 0.005%, O less than 0.001%, N less than 0.002%, P less than 0.001%, S less than 0.001%, and the balance of Fe; the total content of C, O, N, P, S is less than 0.01 percent;
the preparation method of the maraging steel with ultrahigh strength and high toughness comprises the following steps:
(1) sequentially carrying out primary vacuum induction melting and secondary refining on an ultrapure metal raw material under vacuum to obtain a steel ingot;
(2) carrying out homogenization heat treatment on the steel ingot in the step (1);
(3) directly forging the steel ingot subjected to the homogenization heat treatment in the step (2) to obtain a blank;
(4) performing continuous heat treatment on the blank in the step (3), wherein the continuous heat treatment is to directly perform austenitic aging treatment, cryogenic treatment and aging treatment on the forged blank to obtain the maraging steel with ultrahigh strength and high toughness;
the deformation of the forging is required to meet the following requirements: the 1 st forging deformation is less than 5%, the 2 nd forging deformation is less than 10%, the 3 rd forging deformation is less than 15%, and the total deformation after finish forging is more than or equal to 90%.
2. An ultra-high strength and high toughness maraging steel according to claim 1, having a chemical composition comprising: 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 less than 0.005%, O less than 0.001%, N less than 0.002%, P less than 0.001%, S less than 0.001%, and the balance Fe.
3. An ultra-high strength and high toughness maraging steel according to claim 1 or 2, having a tensile strength > 3000MPa, a yield strength > 2700MPa and an elongation > 10%.
4. The method for preparing the ultra-high strength and high toughness maraging steel as recited in any one of claims 1 to 3, comprising the steps of:
(1) sequentially carrying out primary vacuum induction melting and secondary refining on an ultrapure metal raw material under vacuum to obtain a steel ingot;
(2) carrying out homogenization heat treatment on the steel ingot in the step (1);
(3) directly forging the steel ingot subjected to the homogenization heat treatment in the step (2) to obtain a blank;
(4) performing continuous heat treatment on the blank in the step (3), wherein the continuous heat treatment is to directly perform austenitic aging treatment, cryogenic treatment and aging treatment on the forged blank to obtain the maraging steel with ultrahigh strength and high toughness;
the deformation of the forging is required to meet the following requirements: the 1 st forging deformation is less than 5%, the 2 nd forging deformation is less than 10%, the 3 rd forging deformation is less than 15%, and the total deformation after finish forging is more than or equal to 90%.
5. The manufacturing method according to claim 4, wherein the primary vacuum induction melting in the step (1) is performed in a vacuum induction furnace, the temperature of the primary vacuum induction melting is 1450-1550 ℃, and the degree of vacuum is < 1 x 10-4Pa。
6. The production method according to claim 4, wherein the secondary refining in the step (1) is carried out in a vacuum consumable electrode furnace with a degree of vacuum < 1X 10-4Pa。
7. The preparation method according to claim 4, wherein the homogenization heat treatment in step (2) is specifically: and heating the steel ingot, and then carrying out heat preservation, wherein the heat preservation temperature is 1170-1230 ℃, and the heat preservation time is 24-30 h.
8. The preparation method according to claim 4, wherein the forging in the step (3) is performed at an initial forging temperature of 1100-1200 ℃ and a final forging temperature of not less than 850 ℃; the forging ratio of the forging is more than 12.
9. The preparation method according to claim 4, wherein the continuous heat treatment in the step (4) is specifically: directly putting the forged blank into a 680-720 ℃ heat treatment furnace, preserving heat for 2-4 h, carrying out austenite aging, and then air-cooling to room temperature; keeping the blank subjected to austenite aging in liquid nitrogen for more than 2h, and cooling the blank to room temperature in air; and (3) preserving the blank treated by the liquid nitrogen in a heat treatment furnace at 480-520 ℃ for 1-3 h, and air-cooling to room temperature.
10. Use of the ultra-high strength and high toughness maraging steel as defined in any one of claims 1 to 3 or as prepared by the method as defined in any one of claims 4 to 9 as a firing pin for textile crochet hooks or nail guns.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811338298.1A CN109112425B (en) | 2018-11-12 | 2018-11-12 | Ultra-high strength and high toughness maraging steel and preparation method and application thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811338298.1A CN109112425B (en) | 2018-11-12 | 2018-11-12 | Ultra-high strength and high toughness maraging steel and preparation method and application thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN109112425A CN109112425A (en) | 2019-01-01 |
| CN109112425B true CN109112425B (en) | 2020-06-05 |
Family
ID=64853913
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201811338298.1A Active CN109112425B (en) | 2018-11-12 | 2018-11-12 | Ultra-high strength and high toughness maraging steel and preparation method and application thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109112425B (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111054924A (en) * | 2019-12-13 | 2020-04-24 | 上海镭镆科技有限公司 | Heat treatment method for 3D printed stainless steel material |
| CN112251684B (en) * | 2020-09-29 | 2022-02-15 | 中国科学院金属研究所 | Micro-nanocrystalline maraging steel and preparation method thereof |
| 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 |
| CN115369332B (en) * | 2022-08-24 | 2023-07-14 | 中航上大高温合金材料股份有限公司 | Maraging ultrahigh-strength steel and preparation method thereof |
| CN116875915A (en) * | 2023-06-12 | 2023-10-13 | 华为技术有限公司 | Maraging steel, method for producing maraging steel, and electronic device |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5939497B2 (en) * | 1977-03-30 | 1984-09-25 | 大同特殊鋼株式会社 | Maraging steel with excellent delayed fracture resistance |
| JPS62174350A (en) * | 1986-01-27 | 1987-07-31 | Kobe Steel Ltd | Maraging steel |
| CN106756583A (en) * | 2015-11-25 | 2017-05-31 | 中国科学院金属研究所 | A kind of ultra-high-strength/tenacity Maraging steel and its preparation method and application |
| CN107974642A (en) * | 2017-01-17 | 2018-05-01 | 上海落日新材料科技有限公司 | A kind of cutter precipitation-hardening stainless steel and its manufacture method |
| CN108690938B (en) * | 2017-04-06 | 2019-12-27 | 中国科学院金属研究所 | Gradient-strengthened maraging steel firing pin and preparation method thereof |
-
2018
- 2018-11-12 CN CN201811338298.1A patent/CN109112425B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN109112425A (en) | 2019-01-01 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109112425B (en) | Ultra-high strength and high toughness maraging steel and preparation method and application thereof | |
| CN103949805B (en) | A kind of method preparing nickel-base alloy bare welding filler metal | |
| CN101538686B (en) | Martensite precipitation hardening stainless steel for structural member and manufacturing method thereof | |
| CN108220766B (en) | Cr-V hot work die steel and preparation method thereof | |
| KR20150103276A (en) | 700MPa High Strength Hot Rolling Q and P Steel and Manufacturing Method Thereof | |
| CN104120368B (en) | A kind of automobile frame high intensity austenitic stainless steel and its manufacturing method | |
| CN109097682B (en) | High-strength refractory steel bar and preparation method thereof | |
| CN109609840B (en) | Alloy structural steel 27SiMn with thickness of 180-200 mm and production process thereof | |
| CN112222572A (en) | Gas shielded welding wire steel and production method thereof | |
| CN103882344A (en) | Vanadium, chromium and molybdenum added steel plate and production method thereof | |
| CN105499843A (en) | Preparation method of nickel-based alloy welding wires | |
| CN103540859B (en) | High heat-resistant stainless steel coffee pot material and preparation method thereof | |
| CN103962747A (en) | Nickel base alloy welding wire with diameter smaller than 3 mm | |
| CN103962755A (en) | Method for preparing nickel base alloy welding wire with diameter smaller than 3 mm | |
| CN103805909A (en) | Preparation method of austenitic hot-work die steel | |
| CN101985719A (en) | Composite additive for smelting high heat input welding low-alloy steel and using method thereof | |
| CN116005078A (en) | Manufacturing method of lamellar heterogeneous structure high-strength steel | |
| CN103725923A (en) | Aluminum-reinforced nickel-based alloy and manufacturing method thereof | |
| CN103962756B (en) | Cr28Ni48W5 nickel-base alloy is made the method for welding wire | |
| CN103949801A (en) | Welding wire | |
| CN102644025B (en) | High-strength and high-toughness steel plate and preparation method thereof | |
| CN111363970B (en) | Nickel-free LPG (liquefied Petroleum gas) steel plate for ship and manufacturing method thereof | |
| TWI683908B (en) | Method for manufacturing austenite nickel-based alloy plate | |
| CN115821171A (en) | Trace B element-doped modified high-strength high-plasticity multi-component alloy, and preparation method and application thereof | |
| CN114934162A (en) | Thermal deformation method of high-alloy martensitic stainless steel and stainless steel |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |