CN114540720A - High-strength and high-toughness shield tunneling machine blade material and treatment process thereof - Google Patents
High-strength and high-toughness shield tunneling machine blade material and treatment process thereof Download PDFInfo
- Publication number
- CN114540720A CN114540720A CN202210254449.5A CN202210254449A CN114540720A CN 114540720 A CN114540720 A CN 114540720A CN 202210254449 A CN202210254449 A CN 202210254449A CN 114540720 A CN114540720 A CN 114540720A
- Authority
- CN
- China
- Prior art keywords
- blade
- percent
- forging
- furnace
- toughness
- 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
- 239000000463 material Substances 0.000 title claims abstract description 28
- 230000005641 tunneling Effects 0.000 title claims abstract description 15
- 238000000034 method Methods 0.000 title claims abstract description 8
- 238000005242 forging Methods 0.000 claims abstract description 30
- 238000000137 annealing Methods 0.000 claims abstract description 15
- 238000003754 machining Methods 0.000 claims abstract description 13
- 238000010791 quenching Methods 0.000 claims abstract description 6
- 230000000171 quenching effect Effects 0.000 claims abstract description 6
- 238000005496 tempering Methods 0.000 claims abstract description 6
- 238000003723 Smelting Methods 0.000 claims abstract description 5
- 238000010438 heat treatment Methods 0.000 claims description 26
- 238000001816 cooling Methods 0.000 claims description 21
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 claims description 14
- 229910000831 Steel Inorganic materials 0.000 claims description 13
- 239000010959 steel Substances 0.000 claims description 13
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 claims description 7
- 239000003345 natural gas Substances 0.000 claims description 7
- 238000005266 casting Methods 0.000 claims description 4
- 150000003839 salts Chemical class 0.000 claims description 4
- 238000004519 manufacturing process Methods 0.000 abstract description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 abstract description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 abstract description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 abstract description 2
- 229910052799 carbon Inorganic materials 0.000 abstract description 2
- 229910052802 copper Inorganic materials 0.000 abstract description 2
- 239000010949 copper Substances 0.000 abstract description 2
- 238000005516 engineering process Methods 0.000 abstract description 2
- 230000004807 localization Effects 0.000 abstract description 2
- 229910052717 sulfur Inorganic materials 0.000 abstract description 2
- 239000011593 sulfur Substances 0.000 abstract description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 abstract 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 abstract 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 abstract 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 abstract 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 abstract 1
- 229910052804 chromium Inorganic materials 0.000 abstract 1
- 239000011651 chromium Substances 0.000 abstract 1
- 230000000694 effects Effects 0.000 abstract 1
- 229910052742 iron Inorganic materials 0.000 abstract 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 abstract 1
- 229910052750 molybdenum Inorganic materials 0.000 abstract 1
- 239000011733 molybdenum Substances 0.000 abstract 1
- 229910052759 nickel Inorganic materials 0.000 abstract 1
- 229910052758 niobium Inorganic materials 0.000 abstract 1
- 239000010955 niobium Substances 0.000 abstract 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 abstract 1
- 229910052710 silicon Inorganic materials 0.000 abstract 1
- 239000010703 silicon Substances 0.000 abstract 1
- 238000004381 surface treatment Methods 0.000 abstract 1
- 229910052720 vanadium Inorganic materials 0.000 abstract 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 abstract 1
- 238000004458 analytical method Methods 0.000 description 17
- 238000010586 diagram Methods 0.000 description 7
- 229910000734 martensite Inorganic materials 0.000 description 7
- 229910001566 austenite Inorganic materials 0.000 description 6
- 230000005540 biological transmission Effects 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 238000001887 electron backscatter diffraction Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000004321 preservation Methods 0.000 description 3
- 229910019582 Cr V Inorganic materials 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 239000002872 contrast media Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000010438 granite Substances 0.000 description 1
- 238000002354 inductively-coupled plasma atomic emission spectroscopy Methods 0.000 description 1
- HJCCZIABCSDUPE-UHFFFAOYSA-N methyl 2-[4-[[4-methyl-6-(1-methylbenzimidazol-2-yl)-2-propylbenzimidazol-1-yl]methyl]phenyl]benzoate Chemical compound CCCC1=NC2=C(C)C=C(C=3N(C4=CC=CC=C4N=3)C)C=C2N1CC(C=C1)=CC=C1C1=CC=CC=C1C(=O)OC HJCCZIABCSDUPE-UHFFFAOYSA-N 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000005070 sampling Methods 0.000 description 1
- 239000013589 supplement Substances 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 238000004627 transmission electron microscopy Methods 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/22—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for drills; for milling cutters; for machine cutting tools
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/28—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases more than one element being applied in one step
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses a high-strength and high-toughness shield tunneling machine blade material which is composed of carbon, silicon, manganese, sulfur, chromium, vanadium, copper, nickel, molybdenum, niobium and iron elements. The processing technology of the shield machine blade is also disclosed, which is carried out according to the working procedures of electric furnace smelting, primary forging, primary annealing, forming forging, machining, secondary annealing, quenching, primary tempering, finish machining, secondary tempering and surface treatment. The shield machine blade has the remarkable effects that the shield machine blade prepared by adjusting the element components and the dosage and optimizing the manufacturing process has excellent mechanical properties such as yield strength, tensile strength, section shrinkage, impact toughness, hardness and the like, reaches or even exceeds the performance indexes of foreign imported blades, realizes the localization of the high-quality blade of the shield machine and further breaks through foreign technical blockade.
Description
Technical Field
The invention relates to the manufacture of accessories of a shield machine, in particular to a shield machine head cutter and a manufacturing process.
Background
The shield machine is important equipment for urban tunnel tunneling, the mechanization degree of the shield machine is complex, the manufacturing difficulty is high, and related technologies are firmly monopolized by developed countries in the west all the time. Until these years, China gradually makes breakthroughs in each subdivision field of the shield tunneling machine, and breaks through another technical monopoly abroad. The shield machine blade (the structure of which is shown in fig. 1 and fig. 2) is used as a consumable part on the shield machine, the replacement is frequent, the using amount is large, even the price of a single blade is still not good, and the using cost is high.
The shield machine blade has been made a certain achievement in the first place, the performance of the shield machine blade made in China is close to that of the imported shield machine blade, and the shield machine blade can be suitable for most geological conditions in China. However, when a construction unit adopts a shield machine to tunnel in southwest areas of China, the shield machine is influenced by local karst geological environment, and after a domestic blade is installed on a shield machine head, a blade (one blade is thirty or more blades, and the unit price of the domestic blade is about 3 ten thousand yuan/blade) needs to be replaced when the shield machine head tunnels for 40-45 meters; when the granite geological environment is met, the domestic blades cannot be sufficient, Swiss imported blades (the unit price of the Swiss blades is 4-5 ten thousand yuan/piece) must be installed, and one blade needs to be replaced after the tunnel is tunneled for 10 meters generally, so that the tunneling cost is obviously greatly increased.
In order to continuously overcome the above unfavorable situations, researchers urgently need to further improve key technical indexes such as yield strength, tensile strength, impact toughness and wear resistance of the domestic blade, so that the performance of the domestic blade can reach or exceed that of an imported blade, and the technical blockade of the domestic blade in the field of shield machine blades is completely broken through.
Disclosure of Invention
The invention firstly provides a high-strength and high-toughness shield tunneling machine blade material which is characterized by comprising the following elements in percentage by weight: c: 0.45% -0.7%; si: 0.9% -1.2%; mn: 0.3% -0.6%; s: less than or equal to 0.01 percent; cr: 4.0% -6.0%; v: 0.4% -0.8%; cu: 0.08% -0.15%; ni: 0.4% -0.8%; mo: 1.0% -1.6%; nb: 0.2 to 0.4 percent; fe: bal.
Secondly, the invention also provides a treatment process of the high-strength and high-toughness shield machine blade, which is characterized by comprising the following steps of:
step one, smelting in an electric furnace, and casting into a steel ingot with the size of more than 10 inches;
step two, heating to 1150 ℃ for forging, wherein the finish forging temperature is higher than 950 ℃, and obtaining a round billet or a square billet;
step three, annealing the forged steel, keeping the annealing temperature at 850-;
step four, blanking, heating to 1160-1180 ℃, forging the blade forming, controlling the deformation amount of each time during forging to be less than 20%, controlling the finish forging temperature to be 900 ℃, and performing furnace cooling after forging;
step five, machining the forging stock to obtain a blade blank;
sixthly, heating the blade blank to 750 ℃ along with a furnace, preserving heat for 3-4h, cooling along with the furnace, and performing stress relief annealing;
step seven, heating the annealed blade blank to 1020-;
the blade blank has an effective thickness of Lmm, t1 ═ 10min/mm L;
step eight, placing the quenched blade blank in a salt bath furnace, heating to 560-;
t2＝(18-21)s/mm*L；
step nine, performing finish machining on the blade blank;
step ten, after finish machining, performing stress relief tempering;
and step eleven, placing the blade blank into a furnace, introducing natural gas and ammonia gas into the furnace, heating to 580 ℃, preserving heat for more than 8 hours, carrying out S-C-N ternary co-permeation, taking out, and air-cooling to obtain a finished product.
Drawings
FIG. 1 is a schematic structural view of a shield tunneling machine blade;
FIG. 2 is a top view of FIG. 1;
FIG. 3a is a diagram showing the results of an equivalent grain size analysis performed on a test material (d);
FIG. 3b is a distribution diagram of the equivalent grain size obtained by statistics according to FIG. 3 a;
FIG. 4a is a diagram showing the results of grain boundary angle analysis of a test material (iv);
FIG. 4b is a distribution diagram of the grain boundary angle obtained by statistics according to FIG. 4 a;
FIG. 5a is a graph showing the results of the analysis of the ratio of the martensite phase to the austenite phase for the test material (d);
FIG. 5b is a graph showing the ratio of martensite phase to austenite phase according to the statistics of FIG. 5 a;
FIG. 6 is a transmission electron microscope analysis result diagram of a first position selected on the test material IV;
FIG. 7 is a transmission electron microscope analysis result diagram of a second position selected on the test material (R);
FIG. 8 is a transmission electron microscope analysis result diagram of a third position selected on the test material (R).
Detailed Description
The present invention will be further described with reference to the following examples and the accompanying drawings.
Example 1-example 4:
a high-strength and high-toughness blade material of a shield tunneling machine is composed of the following elements in a table 1:
table 1, elemental compositions (weight%/wt%) of examples 1 to 4
| C | Si | Mn | S | Cr | V | Cu | Ni | Mo | Nb | Fe | |
| Example 1 | 0.45 | 0.9 | 0.3 | 0.01 | 4.0 | 0.4 | 0.08 | 0.4 | 1.0 | 0.2 | Bal. |
| Example 2 | 0.7 | 1.2 | 0.6 | 0.01 | 6.0 | 0.8 | 0.15 | 0.8 | 1.6 | 0.4 | Bal. |
| Example 3 | 0.5 | 1.0 | 0.5 | 0.005 | 4.5 | 0.5 | 0.12 | 0.5 | 1.2 | 0.3 | Bal. |
| Example 4 | 0.6 | 1.1 | 0.4 | 0.01 | 5.0 | 0.6 | 0.10 | 0.6 | 1.4 | 0.3 | Bal. |
Example 5:
a treatment process of a shield tunneling machine blade with high strength and toughness is carried out according to the following steps:
step one, respectively smelting molten steel consisting of the elements recorded in the embodiments 1, 2 and 3 by adopting an electric furnace, and casting the molten steel into a steel ingot with the size of more than 10 inches;
step two, heating to 1150 ℃ for forging, wherein the finish forging temperature is higher than 950 ℃, and obtaining a round billet or a square billet;
step three, annealing the forged steel, keeping the annealing temperature at 850-;
step four, blanking, heating to 1160-1180 ℃, forging the blade forming, controlling the deformation amount of each time during forging to be less than 20%, controlling the finish forging temperature to be 900 ℃, and performing furnace cooling after forging;
step five, machining the forging stock to obtain a blade blank;
sixthly, heating the blade blank to 750 ℃ along with a furnace, preserving heat for 3-4h, cooling along with the furnace, and performing stress relief annealing;
seventhly, heating the annealed blade blank to 1020-1080 ℃, then carrying out heat preservation for t1min, and then carrying out oil cooling, wherein the temperature of quenching oil is 50-60 ℃;
the effective thickness of the blade blank is L mm, and the heat preservation time t1 is 10min/mm L;
step eight, placing the quenched blade blank in a salt bath furnace, heating to 560-;
t2＝(18-21)s/mm*L；
step nine, performing finish machining on the blade blank;
step ten, after finish machining, performing stress relief tempering; specifically, heating the blade blank to 250-300 ℃, keeping the temperature for more than 1 hour, taking out and then air-cooling to room temperature;
placing the blade blank in a furnace, introducing natural gas and ammonia gas into the furnace, heating to 580 ℃, preserving heat for more than 8 hours, carrying out S-C-N ternary co-permeation, taking out and air-cooling to obtain a finished product;
in the eleventh step, the flow rate of the natural gas is 1-2m3H, the flow rate of the ammonia gas is 2-3m3/h。
Example 6:
a treatment process of a shield tunneling machine blade with high strength and toughness is carried out according to the following steps:
step one, respectively smelting molten steel consisting of the elements described in examples 1, 2, 3 and 4 by using an electric furnace, and casting into steel ingots with the size of more than 10 inches;
step two, heating to 1150 ℃ for forging, wherein the finish forging temperature is higher than 950 ℃, and obtaining a round billet or a square billet;
step three, annealing the forged steel, keeping the annealing temperature of 865 +/-2 ℃ for 3.5 hours, performing furnace cooling annealing at the speed of 30 ℃ per hour, and cooling the steel to below 500 ℃ and then performing air cooling;
step four, blanking, heating to 1172 +/-1 ℃, forging blade forming, controlling the deformation amount of each time during forging to be less than 20%, controlling the finish forging temperature to be 900 ℃, and performing furnace cooling after forging;
step five, machining the forging stock to obtain a blade blank;
sixthly, heating the blade blank to 750 ℃ along with a furnace, preserving heat for 3.5 hours, cooling along with the furnace, and performing stress relief annealing;
step seven, heating the annealed blade blank to 1050 +/-1 ℃, keeping the temperature for t1min, and then carrying out oil cooling, wherein the temperature of quenching oil is 58 ℃;
the effective thickness of the blade blank is L mm, and the heat preservation time t1 is 10min/mm L;
step eight, placing the quenched blade blank in a salt bath furnace, heating to 570 +/-1 ℃, preserving heat for t2 s, taking out, and then placing in quenching oil again for cooling;
t2＝20s/mm*L；
step nine, performing finish machining on the blade blank;
step ten, heating the finished blade blank to 280 +/-1 ℃, preserving heat for 2 hours, taking out and then air-cooling to room temperature;
eleventh, the blade blank is placed in a furnace, natural gas and ammonia gas are introduced into the furnace, and the flow rate of the natural gas is 1.2m3H, flow rate of the ammonia gas is 2.5m3Heating to 580 ℃ and preserving heat for 8 hours, carrying out S-C-N ternary co-permeation, taking out and air cooling; test blades (i), (ii), (iii) and (iv) were prepared from the molten steels of the elements of examples 1, 2, 3 and 4, respectively.
Performance test:
the test blades (I), (II), (III), (IV) and Swiss imported blade are used as analysis objects, the same test standards are adopted to respectively carry out sampling analysis, and the yield strength sigmas, the tensile strength sigmab, the elongation delta, the section shrinkage psi, the impact toughness Ak, the Vickers hardness HV and other performance indexes of the test materials (I), (II), (III), (IV) and comparison materials (respectively obtained from the test blades (I), (II), (III) and (IV)) and the comparison materials (obtained from the Swiss imported blade) are tested.
Swiss inlet blade element analysis
Adopting an HCS-140 infrared carbon and sulfur analyzer to execute standard GB/T201223-supplement 2006; the ICP-AES emission spectrometer is adopted to perform the GB/T20125-one 2006 standard, and the analysis shows that the element composition of the comparison material is shown in the table 2:
TABLE 2 elemental composition of comparative materials (weight%/wt%)
| C | Si | Mn | S | Cr | V | Cu | Ni | Mo | Fe | |
| Contrast material | 0.6 | 1.09 | 0.33 | 0.01 | 5.02 | 0.91 | 0.09 | 0.12 | 1.24 | Bal. |
Second, mechanical property test results
TABLE 3 mechanical Property test results for test materials and comparative materials
As can be seen from the above table, the yield strength σ s, tensile strength σ b, reduction of area ψ, impact toughness Ak, Vickers hardness HV of the test materials (i), (ii), (iii), and (iv) are superior to those of the comparative materials, and the elongation δ of the test material (iv) is superior to that of the comparative materials.
Three, EBSD and TEM analysis
Performing EBSD analysis on the test material (E), wherein the statistical results of the equivalent grain size analysis are shown in fig. 3a and 3 b; the grain boundary angle analysis statistics are shown in fig. 4a and 4 b; the statistic results of the martensite phase austenite phase ratio analysis are shown in fig. 5a and 5 b; the test material (iv) was analyzed by transmission electron microscopy, and the results are shown in fig. 6, 7, and 8.
EBSD analysis shows that the test material has a compact quenching and tempering structure, a small amount of residual austenite exists in the structure, the residual austenite structure is favorable for improving the toughness of the material, the residual austenite structure is close to six percent, the martensite structure has ninety-four percent, and further transmission electron microscope identification analysis shows that the structure is compact twin crystal martensite and lath martensite, lath martensite is taken as the main part, laths are thin, and nanometer precipitates of titanium and copper exist.
Has the advantages that: according to the technical scheme provided by the invention, by adjusting the element components and the using amount and optimizing the manufacturing process, the manufactured shield machine blade has excellent mechanical properties such as yield strength, tensile strength, reduction of area, impact toughness and hardness, and the like, and reaches or even exceeds the performance indexes of foreign imported blades, so that the localization of the high-quality blade of the shield machine is realized, and the foreign technical blockade is further broken through.
Finally, it should be noted that the above-mentioned description is only a preferred embodiment of the present invention, and those skilled in the art can make various similar representations without departing from the spirit and scope of the present invention.
Claims (4)
1. A high-strength and high-toughness shield tunneling machine blade material is characterized by comprising the following elements in percentage by weight: c: 0.45% -0.7%; si: 0.9% -1.2%; mn: 0.3% -0.6%; s: less than or equal to 0.01 percent; cr: 4.0% -6.0%; v: 0.4% -0.8%; cu: 0.08% -0.15%; ni: 0.4 to 0.8 percent; mo: 1.0% -1.6%; nb: 0.2% -0.4%; the balance of Fe.
2. The high strength and toughness shield tunneling machine blade material according to claim 1, characterized by comprising the following elements in percentage by weight: c: 0.6 percent; si: 1.1 percent; mn: 0.4 percent; s: 0.01 percent; cr: 5.0 percent; v: 0.6 percent; cu: 0.10 percent; ni: 0.6 percent; mo: 1.4 percent; nb: 0.3 percent; the balance of Fe.
3. A treatment process of a shield tunneling machine blade with high strength and toughness is characterized by comprising the following steps:
step one, smelting in an electric furnace, and casting into a steel ingot with the size of more than 10 inches;
step two, heating to 1150 ℃ for forging, wherein the finish forging temperature is higher than 950 ℃, and obtaining a round billet or a square billet;
step three, annealing the forged steel, keeping the annealing temperature at 850-;
step four, blanking, heating to 1160-1180 ℃, forging the blade forming, controlling the deformation amount of each time during forging to be less than 20%, controlling the finish forging temperature to be 900 ℃, and performing furnace cooling after forging;
step five, machining the forging stock to obtain a blade blank;
sixthly, heating the blade blank to 750 ℃ along with a furnace, preserving heat for 3-4h, cooling along with the furnace, and performing stress relief annealing;
seventhly, heating the annealed blade blank to 1020-1080 ℃, preserving heat for t1min, and then carrying out oil cooling, wherein the temperature of quenching oil is 50-60 ℃;
the blade blank has an effective thickness of L mm, t1 ═ 10min/mm L;
step eight, placing the quenched blade blank in a salt bath furnace, heating to 560-;
t2＝(18-21)s/mm*L；
step nine, performing finish machining on the blade blank;
step ten, after finish machining, performing stress relief tempering;
and step eleven, placing the blade blank into a furnace, introducing natural gas and ammonia gas into the furnace, heating to 580 ℃, preserving heat for more than 8 hours, carrying out S-C-N ternary co-permeation, taking out, and air-cooling to obtain a finished product.
4. The process for treating the high-toughness shield tunneling machine blade according to claim 3, wherein: in the eleventh step, the flow rate of the natural gas is 1-2m3H, the flow rate of the ammonia gas is 2-3m3/h。
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210254449.5A CN114540720A (en) | 2022-03-15 | 2022-03-15 | High-strength and high-toughness shield tunneling machine blade material and treatment process thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210254449.5A CN114540720A (en) | 2022-03-15 | 2022-03-15 | High-strength and high-toughness shield tunneling machine blade material and treatment process thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN114540720A true CN114540720A (en) | 2022-05-27 |
Family
ID=81664485
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210254449.5A Pending CN114540720A (en) | 2022-03-15 | 2022-03-15 | High-strength and high-toughness shield tunneling machine blade material and treatment process thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN114540720A (en) |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1648276A (en) * | 2004-01-26 | 2005-08-03 | 大同特殊钢株式会社 | Alloy tool steel |
| CN102517502A (en) * | 2012-01-16 | 2012-06-27 | 株洲钻石钻掘工具有限公司 | Disk-shaped roller cutter ring and manufacture method thereof |
| CN104640654A (en) * | 2012-08-20 | 2015-05-20 | 日立金属株式会社 | Method for cutting cold work tool steel, and method for producing cold-working die material |
-
2022
- 2022-03-15 CN CN202210254449.5A patent/CN114540720A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1648276A (en) * | 2004-01-26 | 2005-08-03 | 大同特殊钢株式会社 | Alloy tool steel |
| CN102517502A (en) * | 2012-01-16 | 2012-06-27 | 株洲钻石钻掘工具有限公司 | Disk-shaped roller cutter ring and manufacture method thereof |
| CN104640654A (en) * | 2012-08-20 | 2015-05-20 | 日立金属株式会社 | Method for cutting cold work tool steel, and method for producing cold-working die material |
Non-Patent Citations (2)
| Title |
|---|
| 李奇等: "《模具材料及热处理（第2版）》", 31 August 2009, 北京理工大学出版社 * |
| 胡怡等: "全断面隧道掘进机盘形滚刀用钢5Cr5MoSiV的研制", 《特殊钢》 * |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109628836B (en) | High-strength anti-seismic fire-resistant steel for building structure and preparation method thereof | |
| US20040238079A1 (en) | Stainless-steel pipe for oil well and process for producing the same | |
| KR100469671B1 (en) | Quenched and tempered steel wire with superior characteristics of cold forging | |
| EP3150735B1 (en) | Hot work tool material and method for manufacturing hot work tool | |
| CN107779746B (en) | Ultra-fine grain alloy steel with ultrahigh strength, high toughness, corrosion resistance, oxidation resistance and preparation method thereof | |
| EP4261320A1 (en) | High-strength and toughness free-cutting non-quenched and tempered round steel and manufacturing method therefor | |
| WO2018182480A1 (en) | Hot work tool steel | |
| CN109735777B (en) | Anti-oxidation hot-work die steel and preparation method thereof | |
| EP2889390B1 (en) | Highly strong, highly tough and highly corrosion-resistant martensitic stainless steel | |
| CN109112423A (en) | Special thick alloy-steel plate of a kind of superior low-temperature toughness and preparation method thereof | |
| WO2010074017A1 (en) | Steel tempering method | |
| EP3173500B1 (en) | Hot-working tool material, method for manufacturing hot-working tool, and hot-working tool | |
| CN113930692A (en) | High-homogenization super-thick steel plate for advanced pressurized water reactor nuclear power station and manufacturing method thereof | |
| CN116516130B (en) | Cr-Mo-V hot work die steel with high hardness and high impact toughness and preparation method thereof | |
| EP3263730B1 (en) | Hot-working tool and manufacturing method therefor | |
| US20240141465A1 (en) | Martensittc steel and method of manufacturing a martensitic steel | |
| KR20140087279A (en) | A cold-work tool steel with excellent hardness and impact toughness | |
| CN114540720A (en) | High-strength and high-toughness shield tunneling machine blade material and treatment process thereof | |
| CN116103472A (en) | Heat treatment process for improving low-temperature toughness of low-carbon high-strength martensitic stainless steel | |
| CN108690938B (en) | Gradient-strengthened maraging steel firing pin and preparation method thereof | |
| CN111321349B (en) | 130mm containment nuclear power steel and continuous casting billet low-compression-ratio manufacturing method thereof | |
| CN116837276A (en) | High-strength high-hardenability steel part and manufacturing method thereof | |
| CN114635075A (en) | High-strength high-ductility and toughness blade material | |
| CN116397160B (en) | Low-carbon steel and preparation method thereof | |
| JP2000212699A (en) | Tool steel excellent in weldability and machinability and die using the same |
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 |
Application publication date: 20220527 |
|
| RJ01 | Rejection of invention patent application after publication |