CN114959438A - High-corrosion-resistance high-toughness die steel and preparation method thereof - Google Patents
High-corrosion-resistance high-toughness die steel and preparation method thereof Download PDFInfo
- Publication number
- CN114959438A CN114959438A CN202110193478.0A CN202110193478A CN114959438A CN 114959438 A CN114959438 A CN 114959438A CN 202110193478 A CN202110193478 A CN 202110193478A CN 114959438 A CN114959438 A CN 114959438A
- Authority
- CN
- China
- Prior art keywords
- steel
- die steel
- tempering
- toughness
- corrosion
- 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.)
- Pending
Links
- 239000010959 steel Substances 0.000 title claims abstract description 211
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 207
- 238000002360 preparation method Methods 0.000 title claims abstract description 9
- 238000005260 corrosion Methods 0.000 claims abstract description 18
- 230000007797 corrosion Effects 0.000 claims abstract description 18
- 238000005496 tempering Methods 0.000 claims description 54
- 238000005242 forging Methods 0.000 claims description 43
- 239000002994 raw material Substances 0.000 claims description 35
- 238000001816 cooling Methods 0.000 claims description 31
- 238000000034 method Methods 0.000 claims description 24
- 238000004321 preservation Methods 0.000 claims description 22
- 238000007670 refining Methods 0.000 claims description 21
- 238000010438 heat treatment Methods 0.000 claims description 17
- 230000008569 process Effects 0.000 claims description 17
- 238000000137 annealing Methods 0.000 claims description 16
- 238000009849 vacuum degassing Methods 0.000 claims description 16
- 238000007599 discharging Methods 0.000 claims description 14
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 9
- 229910052750 molybdenum Inorganic materials 0.000 claims description 8
- 239000011733 molybdenum Substances 0.000 claims description 7
- 238000010791 quenching Methods 0.000 claims description 7
- 230000000171 quenching effect Effects 0.000 claims description 7
- 238000007872 degassing Methods 0.000 claims description 6
- 238000004519 manufacturing process Methods 0.000 claims description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 5
- 239000000203 mixture Substances 0.000 claims description 4
- 238000003466 welding Methods 0.000 abstract description 4
- 229910003296 Ni-Mo Inorganic materials 0.000 abstract description 3
- 238000005275 alloying Methods 0.000 abstract description 3
- 239000002131 composite material Substances 0.000 abstract description 3
- 238000012545 processing Methods 0.000 abstract description 3
- 238000003723 Smelting Methods 0.000 description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 10
- 229910052760 oxygen Inorganic materials 0.000 description 10
- 239000002893 slag Substances 0.000 description 10
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 8
- 238000012360 testing method Methods 0.000 description 8
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 6
- 239000001301 oxygen Substances 0.000 description 6
- 239000003795 chemical substances by application Substances 0.000 description 5
- 238000006477 desulfuration reaction Methods 0.000 description 5
- 230000023556 desulfurization Effects 0.000 description 5
- 229910052717 sulfur Inorganic materials 0.000 description 5
- 229910000851 Alloy steel Inorganic materials 0.000 description 4
- 229910001021 Ferroalloy Inorganic materials 0.000 description 4
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 229910052786 argon Inorganic materials 0.000 description 4
- 230000009286 beneficial effect Effects 0.000 description 4
- 230000008859 change Effects 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- 229910052739 hydrogen Inorganic materials 0.000 description 4
- 229910052757 nitrogen Inorganic materials 0.000 description 4
- 238000010079 rubber tapping Methods 0.000 description 4
- 239000011593 sulfur Substances 0.000 description 4
- 230000000903 blocking effect Effects 0.000 description 3
- 239000004615 ingredient Substances 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 238000005034 decoration Methods 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 239000000463 material Substances 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
- 238000005498 polishing Methods 0.000 description 2
- -1 silicon-aluminum-barium-calcium-iron Chemical group 0.000 description 2
- 239000005997 Calcium carbide Substances 0.000 description 1
- OSMSIOKMMFKNIL-UHFFFAOYSA-N calcium;silicon Chemical group [Ca]=[Si] OSMSIOKMMFKNIL-UHFFFAOYSA-N 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000004891 communication Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000003009 desulfurizing effect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 1
- 229910010271 silicon carbide Inorganic materials 0.000 description 1
- CLZWAWBPWVRRGI-UHFFFAOYSA-N tert-butyl 2-[2-[2-[2-[bis[2-[(2-methylpropan-2-yl)oxy]-2-oxoethyl]amino]-5-bromophenoxy]ethoxy]-4-methyl-n-[2-[(2-methylpropan-2-yl)oxy]-2-oxoethyl]anilino]acetate Chemical compound CC1=CC=C(N(CC(=O)OC(C)(C)C)CC(=O)OC(C)(C)C)C(OCCOC=2C(=CC=C(Br)C=2)N(CC(=O)OC(C)(C)C)CC(=O)OC(C)(C)C)=C1 CLZWAWBPWVRRGI-UHFFFAOYSA-N 0.000 description 1
- 150000003568 thioethers Chemical class 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Images
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
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
-
- 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
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention provides high-corrosion-resistance high-toughness die steel and a preparation method thereof, belonging to the technical field of die steel. The high-corrosion-resistance high-toughness die steel comprises the following components in percentage by weight: 0.05-0.2% of C, 0.2-0.6% of Si, 0.4-1.2% of Mn, 10.0-14.0% of Cr, 1.0-2.5% of Mo, 1.5-4.0% of Ni, 0.1-0.5% of V, less than or equal to 0.03% of P, less than or equal to 0.01% of S and the balance of Fe. The hardenability of the die steel is fully improved by Mn-Cr-Ni-Mo composite alloying, the hardness and uniformity of the die steel are ensured, and the ductility, toughness and strength of the die steel are improved; the toughness, corrosion resistance and welding performance of the die steel can be improved by reducing the content of C, and the easy processing performance of the die steel is realized, so that better comprehensive performance is obtained.
Description
Technical Field
The invention relates to the technical field of die steel, in particular to high-corrosion-resistance high-toughness die steel and a preparation method thereof.
Background
The die machining and forming has a series of advantages of high production efficiency, good quality, material saving, low cost and the like, and is widely applied to the fields of household appliances, automobiles, communication and the like. Currently, the more used corrosion-resistant die steels are Mirrax40, S136 and the like. However, the hardness of Mirrax40 and S316 is low, the corrosion resistance is poor, and the impact toughness and the welding performance are to be improved.
Disclosure of Invention
The invention aims to provide the high-corrosion-resistance high-toughness die steel and the preparation method thereof.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides high-corrosion-resistance high-toughness die steel which comprises the following raw materials in percentage by weight: 0.05-0.2% of C, 0.2-0.6% of Si, 0.4-1.2% of Mn, 10.0-14.0% of Cr, 1.0-2.5% of Mo, 1.5-4.0% of Ni, 0.1-0.5% of V, less than or equal to 0.03% of P, less than or equal to 0.01% of S and the balance of Fe.
Preferably, the raw materials comprise: 0.10% of C, 0.25% of Si, 0.6% of Mn, 12% of Cr, 1.5% of Mo, 2.5% of Ni, 0.3% of V, 0.02% of P, 0.01% of S and the balance of Fe.
Preferably, the raw materials comprise: 0.15% of C, 0.4% of Si, 0.8% of Mn, 13% of Cr, 1.8% of Mo, 3.0% of Ni, 0.4% of V, 0.02% of P, 0.01% of S and the balance of Fe.
Preferably, the raw materials comprise: 0.18% of C, 0.5% of Si, 1.0% of Mn, 14% of Cr, 2.3% of Mo, 3.5% of Ni, 0.5% of V, 0.02% of P, 0.01% of S and the balance of Fe.
The invention provides a preparation method of the high-corrosion-resistance high-toughness die steel, which comprises the following steps:
the raw material composition of the high-corrosion-resistance high-toughness die steel is proportioned, and the proportioned raw material is smelted to obtain a billet;
carrying out ladle refining on the steel billet to obtain refined molten steel;
carrying out vacuum degassing and pouring on the refined molten steel to obtain a steel ingot;
carrying out electroslag remelting on the steel ingot to obtain a remelted ingot;
forging the re-melted ingot to obtain forged steel with a target shape and size;
annealing the forged steel to obtain annealed steel;
and (3) carrying out quenching and tempering heat treatment on the annealed steel to obtain the high-corrosion-resistance high-toughness die steel.
Preferably, the annealing temperature is 600-700 ℃, the heat preservation time is not less than 15h, and the furnace is cooled to below 400 ℃ after the heat preservation is finished and then is discharged.
Preferably, the forging process comprises: heating the re-melted ingot to 1180-1250 ℃, preserving heat for not less than 10 hours, then forging, wherein the initial forging temperature is 1150-1180 ℃, the total forging ratio is not less than 6, the final forging temperature is not less than 830 ℃, and air cooling or air cooling is carried out after forging.
Preferably, the thermal refining treatment includes: and (2) preserving the heat of the annealed steel at 840-910 ℃ for more than 10h, discharging the annealed steel from a furnace, performing water cooling or oil cooling until the surface temperature of the annealed steel is below 200 ℃, then loading the annealed steel into a tempering furnace for tempering, wherein the tempering temperature is 450-520 ℃, the single tempering heat preservation time is not less than 20h, the tempering frequency is not less than 2 times, and discharging the annealed steel from the furnace for air cooling or air cooling after the tempering heat preservation is finished.
Preferably, the vacuum degree of vacuum degassing is 50-67 Pa, and the degassing time is more than or equal to 20 min.
Preferably, molybdenum wires are added in the electroslag remelting process for deoxidation.
The invention provides high-corrosion-resistance high-toughness die steel which comprises the following raw materials in percentage by weight: 0.05-0.2% of C, 0.2-0.6% of Si, 0.4-1.2% of Mn, 10.0-14.0% of Cr, 1.0-2.5% of Mo, 1.5-4.0% of Ni, 0.1-0.5% of V, less than or equal to 0.03% of P, less than or equal to 0.01% of S and the balance of Fe.
The hardenability of the die steel is fully improved by utilizing Mn-Cr-Ni-Mo composite alloying, the hardness and uniformity of the die steel are ensured, and the ductility, toughness and strength of the die steel are improved; the toughness, corrosion resistance and welding performance of the die steel can be improved by reducing the content of C, and the easy processing performance of the die steel is realized, so that better comprehensive performance is obtained.
Drawings
FIG. 1 is a metallographic structure diagram of a high corrosion-resistant high toughness die steel prepared in example 1;
fig. 2 is a graph showing the results of corrosion resistance of the high corrosion-resistant high toughness die steel prepared in example 1, Mirrax40 and S316.
Detailed Description
The invention provides high-corrosion-resistance high-toughness die steel which comprises the following raw materials in percentage by weight: 0.05-0.2% of C, 0.2-0.6% of Si, 0.4-1.2% of Mn, 10.0-14.0% of Cr, 1.0-2.5% of Mo, 1.5-4.0% of Ni, 0.1-0.5% of V, less than or equal to 0.03% of P, less than or equal to 0.01% of S and the balance of Fe.
The raw materials of the high-corrosion-resistance high-toughness die steel comprise, by weight, 0.05-0.2% of C, preferably 0.1-0.17%, and more preferably 0.12-0.15%.
The raw materials of the high-corrosion-resistance high-toughness die steel comprise, by weight, 0.2-0.6% of Si, preferably 0.3-0.5%, and more preferably 0.35-0.45%.
The raw materials of the high-corrosion-resistance high-toughness die steel comprise, by weight, 0.4-1.2% of Mn, preferably 0.5-1.0% of Mn, and more preferably 0.6-0.9% of Mn.
The raw materials of the high-corrosion-resistance high-toughness die steel comprise, by weight, 10.0-14.0% of Cr, preferably 11-13%, and more preferably 11.5-12.5%.
The raw materials of the high-corrosion-resistance high-toughness die steel comprise, by weight, 1.0-2.5% of Mo, preferably 1.3-2.2%, and more preferably 1.5-2.0%.
The raw material of the high-corrosion-resistance high-toughness die steel comprises, by weight, 1.5-4.0% of Ni, preferably 2.0-3.5%, and more preferably 2.5-3.0%.
The raw materials of the high-corrosion-resistance high-toughness die steel comprise 0.1-0.5% of V, preferably 0.2-0.4%, and more preferably 0.25-0.35% in percentage by weight.
The raw materials of the high-corrosion-resistance high-toughness die steel comprise, by weight, not more than 0.03% of P, preferably not more than 0.02%.
The raw materials of the high-corrosion-resistance high-toughness die steel comprise, by weight, not more than 0.01% of S, preferably not more than 0.008%.
The raw materials of the high-corrosion-resistance high-toughness die steel comprise Fe in balance by weight.
The hardenability of the die steel is fully improved by utilizing Mn-Cr-Ni-Mo composite alloying, the hardness and uniformity of the die steel are ensured, and the ductility, toughness and strength of the die steel are improved; the toughness, corrosion resistance and welding performance of the die steel can be improved by reducing the content of C, and the easy processing performance of the die steel is realized, so that better comprehensive performance is obtained.
The invention provides a preparation method of the high-corrosion-resistance high-toughness die steel, which comprises the following steps:
the raw material composition of the high-corrosion-resistance high-toughness die steel is proportioned, and the proportioned raw materials are smelted to obtain a billet;
carrying out ladle refining on the steel billet to obtain refined molten steel;
carrying out vacuum degassing and pouring on the refining molten steel to obtain a steel ingot;
carrying out electroslag remelting on the steel ingot to obtain a remelted ingot;
forging the re-melted ingot to obtain forged steel with a target shape and size;
annealing the forged steel to obtain annealed steel;
and (3) carrying out quenching and tempering heat treatment on the annealed steel to obtain the high-corrosion-resistance high-toughness die steel.
The invention mixes the materials according to the raw material composition of the high-corrosion-resistance high-toughness die steel, and melts the mixed raw materials to obtain the billet.
The invention has no special requirements on the batching process, and the batching process well known in the field can be adopted. The invention preferably adopts scrap steel and ferroalloy raw materials for proportioning, thereby reducing the production cost.
The invention preferably adopts a converter, an electric furnace or an induction furnace for smelting. The invention has no special requirements on the smelting process, and the smelting process well known in the field can be adopted.
After the smelting is finished, the invention preferably carries out slag blocking and adds a deoxidizer to carry out steel tapping to obtain a billet. In the invention, the deoxidizer is preferably one or more of silicon-aluminum-barium-calcium-iron, silicon-calcium core-spun yarn, aluminum wire, aluminum-manganese-iron, steel core aluminum, calcium carbide and silicon carbide. The amount of the deoxidizer used in the present invention is not particularly limited, and may be added in an amount known in the art.
After the steel billet is obtained, the steel billet is subjected to ladle refining to obtain refined molten steel.
In the invention, the ladle refining is preferably used for adjusting the alloy components through LF refining, and adding a deoxidizer and refining slag for deoxidation and desulfurization. The invention uses deoxidizing agent to deoxidize, and uses desulfurizing agent to desulfurize. The invention has no special requirements on the specific type and the dosage of the refining slag, and the S content can be less than or equal to 0.003 percent by adopting the refining slag which is well known in the field. The invention has no special requirements on the type and the dosage of the deoxidizer, and the O content in the refined molten steel after the deoxidizer is added can be less than or equal to 25 ppm. The invention removes the inclusions such as oxides, sulfides and the like existing in the steel by deoxidation and desulfurization, thereby preventing the performance such as toughness, impact energy and the like of the steel from being reduced.
After the refined molten steel is obtained, the invention carries out vacuum degassing and pouring on the refined molten steel to obtain a steel ingot.
In the invention, the vacuum degree of the vacuum degassing is preferably 50-67 Pa, and more preferably 55-65 Pa; the degassing time is preferably 20min or more. The invention preferably employs a VD vacuum degassing apparatus for vacuum degassing. The invention removes gas elements such as N, H, O in molten steel by vacuum degassing. The invention preferably adopts a down-pouring method to pour the molten steel into a required ingot shape to obtain a steel ingot.
After the steel ingot is obtained, the invention carries out electroslag remelting on the steel ingot to obtain a remelted ingot.
According to the invention, molybdenum wires are preferably added in the electroslag remelting process for deoxidation. The addition amount of the deoxidizer is preferably 1-1.5 kg/ton steel ingot, and more preferably 1.2-1.4 kg/ton steel ingot. According to the invention, the oxygen content in the remelted ingot can be further reduced by adding the molybdenum wire, and the oxygen content in the remelted ingot is reduced to 14ppm, so that the content of non-metallic inclusions in a final product is reduced, and the impact energy and polishing performance of the final product are improved. In the present invention, the electroslag remelting is preferably performed under argon protection. The invention further purifies the steel ingot by electroslag remelting, thereby improving the purity of the steel, reducing the sulfur content to be less than 0.002 percent and reducing the oxygen content to be less than 14 ppm.
After obtaining the re-melted ingot, forging the re-melted ingot to obtain the forged steel with the target shape and size.
In the present invention, the forging process preferably includes: heating the re-melted ingot to 1180-1250 ℃, preserving heat for not less than 10 hours, then forging, wherein the initial forging temperature is 1150-1180 ℃, the total forging ratio is not less than 6, the final forging temperature is not less than 830 ℃, and air cooling or air cooling is carried out after forging.
Before forging, the invention keeps the temperature of the re-melted ingot at 1180-1250 ℃, which is beneficial to fully homogenizing the structure. The invention can prevent the forging crack and the crystal grain growth under the condition of ensuring the smooth forging by controlling the initial forging temperature and the final forging temperature.
After the forged steel is obtained, the invention anneals the forged steel to obtain the annealed steel. In the invention, the annealing temperature is preferably 600-700 ℃, and more preferably 620-680 ℃; the heat preservation time is not less than 15h, and more preferably 15-20 h; after the heat preservation is finished, the annealing steel is preferably discharged from the furnace along with the furnace cooling to below 400 ℃ to obtain the annealing steel. In the present invention, the annealing is preferably performed under vacuum conditions. The invention removes the stress after forging by annealing to prevent cracking.
After the annealed steel is obtained, the invention carries out quenching and tempering heat treatment on the annealed steel to obtain the die steel with high corrosion resistance and high toughness.
In the present invention, the quenching and tempering heat treatment preferably includes: and (2) preserving the heat of the annealed steel at 840-910 ℃ for more than 10h, discharging the annealed steel from a furnace, performing water cooling or oil cooling until the surface temperature of the annealed steel is below 200 ℃, then loading the annealed steel into a tempering furnace for tempering, wherein the tempering temperature is 450-520 ℃, the single tempering heat preservation time is not less than 20h, the tempering frequency is not less than 2 times, and discharging the annealed steel from the furnace for air cooling or air cooling after the tempering heat preservation is finished. After the heat preservation of each tempering is finished, the invention is preferably cooled to room temperature, and then the next tempering is carried out.
Further preferably, the annealing steel is kept warm for 10-20 hours at 860-890 ℃. Before tempering, the invention carries out heat preservation, which is beneficial to obtaining better tissue after subsequent tempering.
In the invention, the tempering temperature is preferably 460-500 ℃, and the single tempering time is preferably 15-25 h, and more preferably 18-23 h. In the present invention, the number of annealing is preferably 2 to 3. The invention adopts multiple tempering to be beneficial to fully decomposing martensite and residual austenite to obtain tempered martensite.
The invention obtains good structure by quenching and tempering heat treatment, and ensures that the produced steel has high corrosion resistance and high toughness. In the present invention, the structure after tempering is mainly tempered martensite and contains a small amount of residual austenite.
The high corrosion-resistant and high toughness die steel and the method for manufacturing the same according to the present invention will be described in detail with reference to the following examples, which should not be construed as limiting the scope of the present invention.
Example 1
The raw materials of the high-corrosion-resistance high-toughness die steel comprise 0.10% of C, 0.25% of Si, 0.6% of Mn, 12% of Cr, 1.5% of Mo, 2.5% of Ni, 0.3% of V, 0.02% of P, 0.01% of S and the balance of Fe.
S1, ingredient smelting: smelting the prepared scrap steel and ferroalloy raw materials by using a converter, and tapping by using slag blocking and adding a Ca-Al deoxidizer after the smelting is finished to obtain a steel billet;
s2, ladle refining: adjusting alloy components of the steel billet through LF refining, adding a deoxidizing agent and refining slag for deoxidation and desulfurization, controlling S to be 0.003 percent and O to be less than or equal to 25ppm, and obtaining refined molten steel;
s3, vacuum degassing and pouring: the content of N, H, O gas elements in the refined molten steel is reduced by VD vacuum degassing equipment, the vacuum degree is 60Pa, the degassing time is 20min, and then the molten steel is cast into a required ingot shape by adopting a down-pouring method to obtain a steel ingot;
s4, electroslag remelting: further purifying the steel ingot by an electroslag remelting process, wherein the electroslag remelting is carried out under the protection of argon, and molybdenum wires are added in the remelting process, wherein the adding amount is 1.12 kg/ton, so that the purity of the steel is improved, the sulfur content is reduced to 0.002%, the oxygen content is reduced to 14ppm, and a remelted ingot is obtained;
s5, forging: heating the remelted ingot to 1200 ℃ for heat preservation for 10 hours, keeping the initial forging temperature at 1160 ℃, keeping the total forging ratio at 6, keeping the final forging temperature at 830 ℃, and performing air cooling after forging to obtain forged steel;
s6, annealing: preserving the temperature of the forged steel at 650 ℃ for 15h, then cooling the forged steel to 400 ℃ in a furnace, and discharging the forged steel to obtain annealed steel;
s7, hardening and tempering heat treatment: and (2) preserving the heat of the annealed steel for 10 hours at the temperature of 860 ℃, discharging the annealed steel from the furnace, cooling the annealed steel by water until the surface temperature is 200 ℃, then loading the annealed steel into a tempering furnace for tempering, wherein the tempering temperature is 480 ℃, the single tempering time is 20 hours, the tempering times are 2 times, discharging the annealed steel from the furnace after the tempering and heat preservation are finished, and carrying out air cooling to prepare the high-corrosion-resistance and high-toughness die steel.
Example 2
The raw materials of the high-corrosion-resistance high-toughness die steel comprise the following components: 0.15% of C, 0.4% of Si, 0.8% of Mn, 13% of Cr, 1.8% of Mo, 3.0% of Ni, 0.4% of V, 0.02% of P, 0.01% of S and the balance of Fe.
S1, ingredient smelting: smelting the prepared scrap steel and ferroalloy raw materials by using an electric furnace, and after the smelting is finished, stopping slag and adding a Ca-Al deoxidizer to carry out tapping to obtain a steel billet;
s2, ladle refining: adjusting alloy components of the steel billet through LF refining, adding a deoxidizing agent and refining slag for deoxidation and desulfurization, controlling S to be 0.003 percent and O to be less than or equal to 25ppm, and obtaining refined molten steel;
s3, vacuum degassing and pouring: reducing the content of N, H, O gas elements in the refined molten steel by adopting VD vacuum degassing equipment, wherein the vacuum degree is 50Pa, and the degassing time is 25min, and then pouring the molten steel into a required ingot mold by adopting a down-pouring method to obtain a steel ingot;
s4, electroslag remelting: further purifying the steel ingot through an electroslag remelting process, wherein electroslag remelting is carried out under the protection of argon, and molybdenum wires are added in the remelting process, wherein the addition amount is 1.12 kg/ton, so that the purity of the steel is improved, the sulfur content is reduced to 0.001%, the oxygen content is reduced to 12ppm, and a remelted ingot is obtained;
s5, forging: heating the re-melted ingot to 1180 ℃ for heat preservation, wherein the heat preservation time is 15 hours, the initial forging temperature is 1150 ℃, the total forging ratio is 7, the final forging temperature is 840 ℃, and performing air cooling after forging to obtain forged steel;
s6, annealing: preserving the heat of the forged steel at 600 ℃ for 16h, then cooling the forged steel to 350 ℃ in a furnace, and discharging the forged steel to obtain annealed steel;
s7, hardening and tempering heat treatment: and (2) preserving the heat of the annealed steel at 840 ℃ for 11h, cooling the annealed steel out of the furnace to the surface temperature of 150 ℃, putting the annealed steel into a tempering furnace for tempering, wherein the tempering temperature is 450 ℃, the single tempering time is 22h, the tempering times are 2 times, and discharging the annealed steel out of the furnace after finishing tempering and heat preservation for air cooling to prepare the high-corrosion-resistance and high-toughness die steel.
Example 3
The raw materials of the high-corrosion-resistance high-toughness die steel comprise 0.18 percent of C, 0.5 percent of Si, 1.0 percent of Mn, 14 percent of Cr, 2.3 percent of Mo, 3.5 percent of Ni, 0.5 percent of V, 0.02 percent of P, 0.01 percent of S and the balance of Fe.
S1, ingredient smelting: smelting the prepared scrap steel and ferroalloy raw materials by using an induction furnace, and tapping by using slag blocking and adding a Ca-Al deoxidizer after the smelting is finished to obtain a steel billet;
s2, ladle refining: adjusting alloy components of the steel billet through LF refining, adding a deoxidizing agent and refining slag for deoxidation and desulfurization, controlling S to be 0.002%, and controlling O to be less than or equal to 25ppm, thereby obtaining refined molten steel;
s3, vacuum degassing and pouring: reducing the content of N, H, O gas elements in the refined molten steel by adopting VD vacuum degassing equipment, wherein the vacuum degree is 67Pa, and the degassing time is 30min, and then pouring the molten steel into a required ingot mold by adopting a down-pouring method to obtain a steel ingot;
s4, electroslag remelting: further purifying the steel ingot by an electroslag remelting process, wherein the electroslag remelting is carried out under the protection of argon, and molybdenum wires are added in the remelting process, wherein the adding amount is 1.12 kg/ton, so that the purity of the steel is improved, the sulfur content is reduced to 0.0005%, the oxygen content is reduced to 10ppm, and a remelted ingot is obtained;
s5, forging: heating the re-melted ingot to 1250 ℃ for heat preservation, wherein the heat preservation time is 12 hours, the initial forging temperature is 1180 ℃, the total forging ratio is 8, the final forging temperature is 850 ℃, and air cooling is carried out after forging to obtain forged steel;
s6, annealing: heating the forged steel to 700 ℃, preserving heat for 18 hours, then cooling the forged steel to 200 ℃, discharging the forged steel out of the furnace to obtain annealed steel;
s7, hardening and tempering heat treatment: and (3) keeping the temperature of the annealed steel at 880 ℃ for 15h, discharging the annealed steel from the furnace, cooling the annealed steel by water until the surface temperature is 100 ℃, then loading the annealed steel into a tempering furnace for tempering, wherein the tempering temperature is 520 ℃, the single tempering time is 24h, the tempering times are 2 times, discharging the annealed steel from the furnace after the tempering and heat preservation are finished, and performing air cooling to obtain the high-corrosion-resistance and high-toughness die steel.
Comparative example 1
The only difference from example 1 is that no molybdenum wire was added during electroslag remelting, and the rest is the same as example 1.
And (3) performance testing:
1. metallographic structure observation was performed on the die steel prepared in example 1, and the results are shown in fig. 1. As can be seen from FIG. 1, the die steel prepared by the invention has uniform structure and few non-metallic inclusions.
2. The die steel prepared in example 1 and the existing Mirrax40 and S316 are subjected to corrosion resistance tests by referring to GB/T39534-. As can be seen from fig. 2, the die steel prepared according to the present invention has better corrosion resistance than Mirrax40 and S316.
3. The modulus of elasticity tests were carried out on the die steel prepared in example 1 and the existing Mirrax40 and S316 with reference to GB/T22315-.
TABLE 1 modulus of elasticity of example 1 and the existing Mirrax40 and S316
As can be seen from table 1, the modulus of elasticity of the die steel prepared in example 1 of the present invention is much higher than that of the existing Mirrax40 and S316, and the larger the modulus of elasticity, the less easily the die steel is deformed and the stronger the rigidity, and the greater the hardness.
4. The die steel prepared in example 1 and the existing Mirrax40 were subjected to mechanical property tests with reference to GB/T228.1-2010, and the results are shown in Table 2.
Table 2 mechanical properties of example 1 and the existing Mirrax40
From the results in table 2, it can be seen that the die steel prepared in example 1 of the present invention has a strength equivalent to Mirrax40, and the elongation after fracture and the reduction of area are much higher than Mirrax40, which indicates that the die steel prepared in the present invention has better toughness with good strength.
5. The die steel prepared in example 1 and the existing Mirrax40, S316 were subjected to density testing and the results are shown in table 3.
TABLE 3 Density (in kg/m) of example 1 and the existing Mirrax40 and S316 3 )
| 20℃ | 200℃ | 400℃ | |
| Example 1 | 7680 | 7650 | 7620 |
| Mirrax40 | 7700 | 7660 | 7620 |
| S316 | 7800 | 7750 | 7700 |
As can be seen from Table 3, the die steel prepared by the invention has small density change along with temperature, light weight and small influence by temperature change.
6. The die steel prepared in example 1 and the existing Mirrax40 were subjected to coefficient of thermal expansion tests and the results are shown in table 4.
TABLE 4 thermal expansion coefficients (units:/. degree. C.) for example 1 and conventional Mirrax40 and S316
| 20℃ | 200℃ | 400℃ | |
| Example 1 | 10.8 | 11 | 11.3 |
| Mirrax40 | 10.4 | 10.6 | 11.4 |
| S316 | 10.6 | 11 | 11.4 |
As can be seen from Table 4, compared with other existing die steels, the die steel prepared by the invention has smaller change of thermal expansion coefficient along with temperature change and more stable size under high temperature.
7. The die steel prepared in example 1 and the conventional Mirrax40 were subjected to a thermal conductivity test, and the results are shown in table 5.
TABLE 5 thermal conductivity (unit: W/m ℃ C.) for example 1 and conventional Mirrax40 and S316
| 20℃ | 200℃ | 400℃ | |
| Example 1 | 18 | 20 | 25 |
| Mirrax40 | 17 | 20 | 21 |
| S316 | 16 | 20 | 24 |
As can be seen from Table 5, the hot die steel prepared by the invention has higher heat conductivity coefficient, and when the die is made of steel and used, the die is uniformly heated, so that a product can be better made.
8. The impact energy test is performed on the die steel prepared in example 1 and comparative example 1, the impact energy of example 1 is 224J, the impact energy of comparative document 1 is 146J, the toughness is higher when the impact energy is higher, and the results of example 1 and comparative example 1 show that the addition of molybdenum wires in the electroslag remelting process is beneficial to improving the toughness of the die steel.
From the above results, it is understood that the die steel prepared according to the present invention has high hardness and uniformity, high polishing performance, superior impact toughness, superior hardenability, excellent machining performance, and superior corrosion resistance, compared to the prior art.
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 high-corrosion-resistance high-toughness die steel is characterized by comprising the following raw materials in percentage by weight: 0.05-0.2% of C, 0.2-0.6% of Si, 0.4-1.2% of Mn, 10.0-14.0% of Cr, 1.0-2.5% of Mo, 1.5-4.0% of Ni, 0.1-0.5% of V, less than or equal to 0.03% of P, less than or equal to 0.01% of S and the balance of Fe.
2. The die steel with high corrosion resistance and high toughness as claimed in claim 1, wherein the raw materials comprise: 0.10% of C, 0.25% of Si, 0.6% of Mn, 12% of Cr, 1.5% of Mo, 2.5% of Ni, 0.3% of V, 0.02% of P, 0.01% of S and the balance of Fe.
3. The die steel with high corrosion resistance and high toughness as claimed in claim 1, wherein the raw materials comprise: 0.15% of C, 0.4% of Si, 0.8% of Mn, 13% of Cr, 1.8% of Mo, 3.0% of Ni, 0.4% of V, 0.02% of P, 0.01% of S and the balance of Fe.
4. The high corrosion resistance and high toughness die steel according to claim 1, wherein said raw materials comprise: 0.18% of C, 0.5% of Si, 1.0% of Mn, 14% of Cr, 2.3% of Mo, 3.5% of Ni, 0.5% of V, 0.02% of P, 0.01% of S and the balance of Fe.
5. The method for preparing the high-corrosion-resistance high-toughness die steel of any one of claims 1 to 4, comprising the following steps of:
the high corrosion resistance and high toughness die steel according to any one of claims 1 to 4, wherein the raw material composition is prepared, and the prepared raw material is smelted to obtain a billet;
carrying out ladle refining on the steel billet to obtain refined molten steel;
carrying out vacuum degassing and pouring on the refining molten steel to obtain a steel ingot;
carrying out electroslag remelting on the steel ingot to obtain a remelted ingot;
forging the re-melted ingot to obtain forged steel with a target shape and size;
annealing the forged steel to obtain annealed steel;
and (3) carrying out quenching and tempering heat treatment on the annealed steel to obtain the high-corrosion-resistance high-toughness die steel.
6. The preparation method according to claim 5, wherein the annealing temperature is 600-700 ℃, the heat preservation time is not less than 15h, and the annealing furnace is cooled to below 400 ℃ after the heat preservation is finished and then is taken out of the furnace.
7. The method of manufacturing according to claim 5, wherein the forging process comprises: heating the re-melted ingot to 1180-1250 ℃, preserving heat for not less than 10 hours, then forging, wherein the initial forging temperature is 1150-1180 ℃, the total forging ratio is not less than 6, the final forging temperature is not less than 830 ℃, and air cooling or air cooling is carried out after forging.
8. The production method according to claim 5, wherein the quenching and tempering heat treatment includes: and (2) preserving the heat of the annealed steel at 840-910 ℃ for more than 10h, discharging the annealed steel from a furnace, performing water cooling or oil cooling until the surface temperature of the annealed steel is below 200 ℃, then loading the annealed steel into a tempering furnace for tempering, wherein the tempering temperature is 450-520 ℃, the single tempering heat preservation time is not less than 20h, the tempering frequency is not less than 2 times, and discharging the annealed steel from the furnace for air cooling or air cooling after the tempering heat preservation is finished.
9. The preparation method according to claim 5, wherein the vacuum degree of vacuum degassing is 50-67 Pa, and the degassing time is 20min or more.
10. The method according to claim 5, wherein molybdenum wires are added for deoxidation during the electroslag remelting process.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110193478.0A CN114959438A (en) | 2021-02-20 | 2021-02-20 | High-corrosion-resistance high-toughness die steel and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110193478.0A CN114959438A (en) | 2021-02-20 | 2021-02-20 | High-corrosion-resistance high-toughness die steel and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN114959438A true CN114959438A (en) | 2022-08-30 |
Family
ID=82954510
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202110193478.0A Pending CN114959438A (en) | 2021-02-20 | 2021-02-20 | High-corrosion-resistance high-toughness die steel and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN114959438A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115612935A (en) * | 2022-10-28 | 2023-01-17 | 泰尔重工股份有限公司 | Hot-rolled winding drum high-performance sector plate and manufacturing method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105543653A (en) * | 2015-12-22 | 2016-05-04 | 四川六合锻造股份有限公司 | Plastic die steel with high intensity, high toughness and high corrosion resistance and production method thereof |
| CN110295332A (en) * | 2019-07-05 | 2019-10-01 | 天津钢研海德科技有限公司 | A kind of pre- hard mold steel of the high mirror surface of high tenacity and its manufacturing process |
-
2021
- 2021-02-20 CN CN202110193478.0A patent/CN114959438A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105543653A (en) * | 2015-12-22 | 2016-05-04 | 四川六合锻造股份有限公司 | Plastic die steel with high intensity, high toughness and high corrosion resistance and production method thereof |
| CN110295332A (en) * | 2019-07-05 | 2019-10-01 | 天津钢研海德科技有限公司 | A kind of pre- hard mold steel of the high mirror surface of high tenacity and its manufacturing process |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115612935A (en) * | 2022-10-28 | 2023-01-17 | 泰尔重工股份有限公司 | Hot-rolled winding drum high-performance sector plate and manufacturing method thereof |
| CN115612935B (en) * | 2022-10-28 | 2023-12-19 | 泰尔重工股份有限公司 | High-performance sector plate of hot-rolled winding drum and manufacturing method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN103160729B (en) | Medium-carbon microalloyed steel for engineering machinery caterpillar chain piece and production process thereof | |
| US20210164078A1 (en) | Spring steel having superior fatigue life, and manufacturing method for same | |
| CN110863158B (en) | High-performance Mn-Cr series steel for wind power output gear and production method thereof | |
| CN110295332B (en) | High-toughness high-mirror-surface pre-hardened die steel and manufacturing process thereof | |
| CN111394639B (en) | Manufacturing method of high-wear-resistance gear steel | |
| WO2022022066A1 (en) | Steel board for polar marine engineering and preparation method therefor | |
| CN109652733B (en) | 690 MPa-grade super-thick steel plate and manufacturing method thereof | |
| WO2019080457A1 (en) | Nitrogen-containing microalloying spring steel and preparation method therefor | |
| CN107130172B (en) | 400HBW grades of Brinell hardness whole constrictive type high tenacity easily weld special thick wear-resisting steel plate and its manufacturing method | |
| CN106756509B (en) | A kind of high-temperature alloy structural steel and its Technology for Heating Processing | |
| CN109609729B (en) | Stainless steel plate with 650 MPa-grade yield strength and manufacturing method thereof | |
| CN108588570A (en) | 600 DEG C of medium temperature acid corrosion-resistant pressure vessel steels of one kind and preparation method thereof | |
| CN115612929A (en) | Petroleum casing pipe for heavy oil thermal production well and preparation method thereof | |
| CN105018862A (en) | High-toughness steel plate 140 mm thick and manufacturing method thereof | |
| CN113652609A (en) | Low-cost 42CrMoA round steel and production method thereof | |
| CN114959415A (en) | Manufacturing method of microalloyed wind power transmission gear steel | |
| CN111270169A (en) | Ni-containing alloy steel plate with excellent low-temperature toughness and production method thereof | |
| CN114959438A (en) | High-corrosion-resistance high-toughness die steel and preparation method thereof | |
| CN114635077A (en) | Super austenitic stainless steel and preparation method thereof | |
| CN115094307B (en) | Hot die steel continuous casting round billet for electroslag remelting and production process thereof | |
| CN110983154A (en) | Extra-thick high-toughness 460 MPa-level yield structural steel plate and production method thereof | |
| CN115029631A (en) | High-strength and high-toughness steel for wind power transmission gear and manufacturing method thereof | |
| CN111876679B (en) | Chromium-vanadium hot-rolled steel wire rod and preparation method thereof, and preparation method of steel wire and hand tool | |
| CN109161629A (en) | A kind of LF refining method of spring steel | |
| CN101845594A (en) | Martensitic stainless steel and manufacturing method thereof |
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 | ||
| RJ01 | Rejection of invention patent application after publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20220830 |