CN111961988B - Production process and forging method of medium-carbon non-quenched and tempered steel for automobile expansion fracture connecting rod - Google Patents
Production process and forging method of medium-carbon non-quenched and tempered steel for automobile expansion fracture connecting rod Download PDFInfo
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- CN111961988B CN111961988B CN202010918899.0A CN202010918899A CN111961988B CN 111961988 B CN111961988 B CN 111961988B CN 202010918899 A CN202010918899 A CN 202010918899A CN 111961988 B CN111961988 B CN 111961988B
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 68
- 239000010959 steel Substances 0.000 title claims abstract description 68
- 238000005242 forging Methods 0.000 title claims abstract description 51
- 238000000034 method Methods 0.000 title claims abstract description 43
- 229910052799 carbon Inorganic materials 0.000 title claims abstract description 20
- 238000004519 manufacturing process Methods 0.000 title abstract description 16
- 239000002893 slag Substances 0.000 claims abstract description 46
- 238000001816 cooling Methods 0.000 claims abstract description 26
- 238000007670 refining Methods 0.000 claims abstract description 20
- 238000010583 slow cooling Methods 0.000 claims abstract description 17
- 238000010438 heat treatment Methods 0.000 claims abstract description 16
- 238000009749 continuous casting Methods 0.000 claims abstract description 14
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 claims abstract description 12
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims abstract description 11
- 229910052791 calcium Inorganic materials 0.000 claims abstract description 11
- 239000011575 calcium Substances 0.000 claims abstract description 11
- 238000009489 vacuum treatment Methods 0.000 claims abstract description 11
- 238000005096 rolling process Methods 0.000 claims abstract description 9
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 8
- 239000001301 oxygen Substances 0.000 claims abstract description 8
- 238000010079 rubber tapping Methods 0.000 claims abstract description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 17
- 229910052782 aluminium Inorganic materials 0.000 claims description 14
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 12
- 239000010936 titanium Substances 0.000 claims description 12
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 10
- 238000007664 blowing Methods 0.000 claims description 9
- 238000005266 casting Methods 0.000 claims description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 8
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 claims description 8
- 238000003723 Smelting Methods 0.000 claims description 8
- 229910052681 coesite Inorganic materials 0.000 claims description 7
- 229910052906 cristobalite Inorganic materials 0.000 claims description 7
- 239000000377 silicon dioxide Substances 0.000 claims description 7
- 229910052682 stishovite Inorganic materials 0.000 claims description 7
- 229910052719 titanium Inorganic materials 0.000 claims description 7
- 229910052905 tridymite Inorganic materials 0.000 claims description 7
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 claims description 6
- 238000001514 detection method Methods 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 6
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims description 5
- 229910052786 argon Inorganic materials 0.000 claims description 5
- 229910052593 corundum Inorganic materials 0.000 claims description 5
- 229910052742 iron Inorganic materials 0.000 claims description 5
- 238000002844 melting Methods 0.000 claims description 5
- 230000008018 melting Effects 0.000 claims description 5
- 239000000843 powder Substances 0.000 claims description 5
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 claims description 5
- 229910010271 silicon carbide Inorganic materials 0.000 claims description 5
- 229910001845 yogo sapphire Inorganic materials 0.000 claims description 5
- KKCBUQHMOMHUOY-UHFFFAOYSA-N Na2O Inorganic materials [O-2].[Na+].[Na+] KKCBUQHMOMHUOY-UHFFFAOYSA-N 0.000 claims description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 4
- 229910000272 alkali metal oxide Inorganic materials 0.000 claims description 4
- 239000005997 Calcium carbide Substances 0.000 claims description 3
- 235000008733 Citrus aurantifolia Nutrition 0.000 claims description 3
- 229910000604 Ferrochrome Inorganic materials 0.000 claims description 3
- 229910000519 Ferrosilicon Inorganic materials 0.000 claims description 3
- 229910000720 Silicomanganese Inorganic materials 0.000 claims description 3
- 235000011941 Tilia x europaea Nutrition 0.000 claims description 3
- 239000000378 calcium silicate Substances 0.000 claims description 3
- 229910052918 calcium silicate Inorganic materials 0.000 claims description 3
- OYACROKNLOSFPA-UHFFFAOYSA-N calcium;dioxido(oxo)silane Chemical compound [Ca+2].[O-][Si]([O-])=O OYACROKNLOSFPA-UHFFFAOYSA-N 0.000 claims description 3
- 239000004571 lime Substances 0.000 claims description 3
- 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 claims description 3
- OSMSIOKMMFKNIL-UHFFFAOYSA-N calcium;silicon Chemical compound [Ca]=[Si] OSMSIOKMMFKNIL-UHFFFAOYSA-N 0.000 claims description 2
- 230000006698 induction Effects 0.000 claims description 2
- 238000003825 pressing Methods 0.000 claims description 2
- 229910000859 α-Fe Inorganic materials 0.000 abstract description 18
- 239000000463 material Substances 0.000 abstract description 16
- 238000005520 cutting process Methods 0.000 abstract description 15
- 229910001562 pearlite Inorganic materials 0.000 abstract description 6
- 238000005457 optimization Methods 0.000 abstract description 4
- 230000000052 comparative effect Effects 0.000 description 19
- 230000007547 defect Effects 0.000 description 6
- 230000002159 abnormal effect Effects 0.000 description 5
- 238000003754 machining Methods 0.000 description 5
- 239000000126 substance Substances 0.000 description 5
- 230000009286 beneficial effect Effects 0.000 description 4
- 238000013461 design Methods 0.000 description 4
- 239000011572 manganese Substances 0.000 description 4
- 150000003568 thioethers Chemical class 0.000 description 4
- 238000005422 blasting Methods 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 244000035744 Hura crepitans Species 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 229910001563 bainite Inorganic materials 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 238000004901 spalling Methods 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910000677 High-carbon steel Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 229910001199 N alloy Inorganic materials 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 239000005864 Sulphur Substances 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- SKKMWRVAJNPLFY-UHFFFAOYSA-N azanylidynevanadium Chemical compound [V]#N SKKMWRVAJNPLFY-UHFFFAOYSA-N 0.000 description 1
- 238000010923 batch production Methods 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000007599 discharging Methods 0.000 description 1
- 238000005553 drilling Methods 0.000 description 1
- 238000004134 energy conservation Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000000407 epitaxy Methods 0.000 description 1
- 238000007667 floating Methods 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 230000000977 initiatory effect Effects 0.000 description 1
- 238000007689 inspection Methods 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 239000006247 magnetic powder Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 description 1
- 238000009966 trimming Methods 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/0056—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00 using cored wires
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/04—Removing impurities by adding a treating agent
- C21C7/06—Deoxidising, e.g. killing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/10—Handling in a vacuum
-
- 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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires 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
- C22C33/06—Making ferrous alloys by melting using master 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
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- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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
-
- 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
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Abstract
The invention discloses a production process and a forging method of medium-carbon non-quenched and tempered steel for an automobile expansion fracture connecting rod. Through component optimization, special synthetic slag is added in the electric furnace tapping process, a reasonable slag system is adopted in the refining process to control the alkalinity of final slag to be 2.5-3.5, the oxygen content of molten steel is controlled to be 11-18 ppm, calcium treatment is carried out on the molten steel after VD vacuum treatment, special covering slag is adopted in a crystallizer in the continuous casting process, and a round rod is obtained through rolling. The manufacturing method of the forge piece comprises the steps of blanking, heating and forging the round bar, wherein the heating temperature is controlled to be 1150-1200 ℃, the pre-forging temperature is controlled to be 1100-1130 ℃, and the finish forging temperature is controlled to be 920-960 ℃; after forging, a cooling mode combining strong cooling and slow cooling is adopted, so that a uniform pearlite and ferrite structure is finally obtained, an excellent sulfide morphology is obtained, the cutting performance is improved, and the comprehensive performance characteristics such as high strength, toughness and the like can be obtained, so that the non-quenched and tempered steel material for the high-strength connecting rod is successfully developed.
Description
Technical Field
The invention relates to an automobile expansion-fracture connecting rod and a manufacturing method thereof, in particular to an automobile expansion-fracture connecting rod, a manufacturing method of medium carbon non-quenched and tempered steel used by the automobile expansion-fracture connecting rod and a manufacturing method of a forging piece of the medium carbon non-quenched and tempered steel. In particular to a component design and smelting process of medium carbon non-quenched and tempered steel for an expansion fracture connecting rod and a forging and cooling control process of a forge piece of the medium carbon non-quenched and tempered steel.
Background
The connecting rod is one of the key parts of automobile engine and is formed by connecting a connecting rod body and a connecting rod cover by bolts, the connecting rod connects the piston of the engine with the crankshaft and has the function of converting the linear reciprocating motion of the piston into the rotating motion of the crankshaft.
The connecting rod machining mainly comprises a flat cutting process and an expansion cutting process, the traditional connecting rod flat cutting machining process is complex, the stability of an engine is affected due to machining precision errors, the expansion cutting connecting rod technology well solves the problem, the machining procedures are few, and the production cost of the connecting rod is remarkably reduced.
At present, a series of non-quenched and tempered steels for the fractured connecting rod are developed domestically, the non-quenched and tempered steel with high carbon C70S6 is widely applied, the steel is easy to generate brittle fracture, but still has obvious defects: the yield ratio is low; the fatigue property is lower than that of quenched and tempered steel; the brittle lamellar cementite has high hardness and high content, so that the cutting processability of the steel is poor. The connecting rod belongs to a moving part, and the weight reduction of the moving part is more beneficial to the light weight of an automobile, so along with the development trend of light weight and energy conservation of the automobile, higher requirements are put on the material of the expansion-fracture connecting rod, and the connecting rod material is required to have higher yield ratio so as to fully exert the mechanical property of the material besides ensuring the expansion-fracture performance and the strength. The medium-carbon non-quenched and tempered steel reduces the toughness of a ferrite phase, improves the hardness of the ferrite phase, properly embrittles a prior austenite grain boundary, has the ferrite solid solution strengthening effect of silicon and manganese elements and the precipitation strengthening and structure refining effect of vanadium elements, so that the material has higher strength level and yield ratio, and has excellent high-cycle fatigue performance far higher than that of the high-carbon steel C70S6 for the conventional spalling connecting rod, in addition, the fracture of the medium-carbon non-quenched and tempered steel is in typical brittle fracture, and the deformation before and after spalling is small, so that the processing precision is higher, the performance of an engine is more stable, the medium-carbon non-quenched and tempered steel (such as 36MnVS4) has more excellent cutting performance than the high-carbon C70S6 material, the service life of a cutter in a drilling process can be improved by 30%, and the service life of the cutter in a tapping process is improved by 50%.
In order to improve the strength and toughness of the 36MnVS4 material, enough alloy strengthening elements such as Si, Mn and V need to be added, the increase of the alloy elements can cause the material to be easy to have a banded structure, the austenite stability is poor, and unbalanced structures are easy to appear in the cooling process of rolling and forging, so that the requirement on the cooling process after forging is very high, the cooling strength is not enough, the toughness of the material is not enough, the cooling strength is too high, abnormal structures are easy to appear, the ferrite proportion is increased, and therefore how to develop a connecting rod material with high toughness and capable of preventing the abnormal structures from forming becomes a big difficulty in the industry.
For example, the smelting, rolling and forging processes of the existing and more researched non-quenched and tempered steel 36MnVS4 automobile engine connecting rod have more defects, such as 'analysis of expansion defect of the non-quenched and tempered steel 36MnVS4 automobile engine connecting rod, stretch to the epitaxy and the like', researches find that the 36MnVS4 connecting rod obtained through expansion-fracture simulation research is dispersed in the crack initiation position compared with C70S6, the crack is unstable in expansion, the notch sensitivity is high, the ferrite structure is more, the defect of the expansion-fracture process is increased easily during batch production, the non-quenched and tempered steel 36MnVS4 connecting rod obtained by adopting the blank production process has the defects of uneven fracture, continuous expansion, overlarge fracture deformation and the like, and the cutting performance is poor. In the 'process for controlling ferrite content in the production process of the 36MnVS4 material connecting rod', the limitation on the production process temperature, cooling conditions and the like of the connecting rod casting is adopted, but the volume fraction of the finally obtained ferrite is large, the crystal grains are large, the ferrite content can only be controlled within 32-35%, and the ferrite content is difficult to further reduce. In the non-quenched and tempered steel 36MnVS4, too much ferrite content is not beneficial to the expansion-fracture machining of the connecting rod, so that the proportion of the ferrite can be effectively reduced while the mechanical property of high toughness is ensured, an ideal pearlite and ferrite balanced structure is controlled and obtained, and the good cutting performance is further improved. The design of a connecting rod with light weight, enough rigidity and strength and good cutting processability is particularly important for engines.
Disclosure of Invention
The invention aims to provide an automobile expansion-fracture connecting rod, which can effectively homogenize material structure, obtain an ideal pearlite + ferrite balanced structure, prevent abnormal structures such as bainite and martensite from forming, obtain excellent sulfide morphology, control the ferrite proportion not to exceed 15%, and simultaneously obtain comprehensive performance characteristics such as high strength, toughness, good cutting performance and the like through the optimization design of components and the optimization of smelting, forging and cooling process parameters after forging.
The purpose of the invention is realized by the following technical scheme:
the medium carbon non-quenched and tempered steel for the automobile expansion fracture connecting rod comprises the following components in percentage by weight: 0.34-0.38% of C, 0.65-0.75% of Si, 0.95-1.05% of Mn, less than or equal to 0.020% of P, 0.030-0.045% of S, 0.11-0.14% of Ni, 0.15-0.23% of Cr, 0.008-0.020% of Al, 0.28-0.32% of V, less than or equal to 0.006% of Ti, less than or equal to 0.05% of Mo, 0.015-0.020% of N, and the balance of Fe and inevitable impurities.
A production process of medium carbon non-quenched and tempered steel for an automobile expansion fracture connecting rod comprises the working procedures of electric furnace smelting, LF furnace refining, VD vacuum treatment, continuous casting pouring and rolling, and the process flow comprises the following steps:
(1) smelting in an electric furnace, and improving the molten iron ratio when metal materials are proportioned: adopting 65-75% of blast furnace molten iron and 25-35% of high-quality scrap steel (Cu and Mo in the scrap steel are required to be less than or equal to 0.05%); controlling the end point of the electric furnace: 0.05-0.30% of C and less than or equal to 0.013% of P; adding silicomanganese, ferrosilicon and low titanium ferrochrome (Ti is less than or equal to 0.03%) into a ladle in sequence after tapping 1/3; then adding slag: 400 kg lime/furnace and 400 kg/furnace low-titanium synthetic slag (MgO is less than or equal to 2 percent and Al is calculated according to mass percentage)2O337～43％、H2O≤0.5％、TiO2≤0.10％、CaO42～48％、SiO28-15%) and 80-100 kg of calcium carbide per furnace are used for pre-deoxidation of molten steel;
(2) in the LF refining, firstly electrifying for 5 minutes to melt slag, then performing slag surface deoxidation by using 80-100 kg of aluminum powder per furnace, then adding vanadium-nitrogen alloy to adjust the V content and the N content, performing slag surface deoxidation and slag fluidity adjustment by using silicon carbide according to the slag condition in the whole refining process, controlling the slag alkalinity at the later refining stage to be 2.5-3.5 (CaO/SiO) according to the usage amount of the silicon carbide being 60-120 kg per furnace2) The sulfur content is adjusted by adopting ferro-sulphur at the later stage of refining, the aluminum content is adjusted by feeding an aluminum wire, the Al content of LF refining is controlled to be 0.035-0.045%, the purpose of using aluminum in one step at the early stage is achieved, and the aluminum is prevented from being reused after VD vacuum is finished, so that the generated aluminum deoxidation product is prevented from comingThe oxygen content of the molten steel is controlled to be 11-18 ppm so as to ensure that a proper amount of oxides exist in the molten steel;
(3) controlling VD limit vacuum treatment time for 10-18 min, feeding 50-80 m of calcium silicate wire to each furnace steel after VD vacuum treatment is finished to carry out calcium treatment on sulfide in the molten steel, so that the cutting performance of the material can be improved, the molten steel can be prevented from being polluted by impurities such as aluminum oxide and the like, and carrying out soft argon blowing on the molten steel after the calcium treatment is finished so as to promote the floating of the impurities in the molten steel and control the soft blowing time for 25-45 min;
(4) continuous casting, wherein the superheat degree of molten steel is required to be controlled to be 15-30 ℃, and as the steel contains crack sensitive elements such as S, Cr, Ni and the like, the medium-carbon sulfur-containing steel special-purpose covering slag is adopted for the crystallizer covering slag for ensuring the surface quality of a casting blank, and the physical and chemical performance indexes are designed as follows: SiO 2232±3％、CaO 24±2.5％、Al2O3 6.5±1.5％、FeO≤3.0％、MgO 6.0±1.5％、F-3.5±1.0％、R2O(K2O+Na2O 5.0±1.5％、FC 12±1.5％；CaO/SiO20.75 ± 0.05, melting point: 1260 plus or minus 20 ℃ and 0.66 plus or minus 0.20 of viscosity (Pa.S/1300 ℃), wherein the melting point of the special covering slag is 150 ℃ higher than that of the common covering slag and the viscosity (Pa.S/1300 ℃) is 0.05 higher than that of the common covering slag. Similarly, in order to prevent the surface of the casting blank from generating cracks, slow cooling is carried out after the continuous casting is taken out, the temperature of a slow cooling pit is required to be not lower than 500 ℃, and the slow cooling time is not less than 48 hours;
(5) and heating and rolling the 220 x 260 section continuous casting billet to obtain the round rod with the specification of 60 mm.
The method for manufacturing the forge piece by using the medium-carbon non-quenched and tempered steel for the automobile expansion fracture connecting rod comprises the following steps of blanking, heating, forging (including blank manufacturing, pre-forging, final forging, trimming, punching and shaping), cooling and shot blasting flaw detection:
(1) heating: after blanking, a 60mm round bar is subjected to induction heating, and the designed heating temperature is 1150-1200 ℃;
(2) forging: heating and then forging, controlling the pre-forging temperature to be 1100-1130 ℃, controlling the final forging temperature to be 920-960 ℃, and forging into a connecting rod blank;
(3) and (3) cooling: and (3) blowing air to cool the hot connecting rod blank to 600 +/-10 ℃ on a conveyer belt within 5-8 minutes after forging is finished so as to obtain fine lamellar pearlite and inhibit precipitation of proeutectoid ferrite, controlling the proportion of the ferrite to be less than or equal to 15%, and then moving the connecting rod blank into a sand box from the air-cooled conveyer belt for slow cooling at the cooling rate of 0.03-0.10 ℃/S so as to obtain the connecting rod blank.
(4) Shot blasting and flaw detection: and after the connecting rod blank is cooled to normal temperature, performing shot blasting, magnetic powder flaw detection and physical and chemical performance index detection to obtain the qualified connecting rod blank.
The invention has the beneficial effects that: the automobile expansion-fracture connecting rod forging manufactured by the method has the advantages of good surface quality, high strength, good plasticity, good appearance of sulfide and good free-cutting performance. The invention makes the following efforts:
firstly, carrying out optimization design on components;
secondly, high-quality scrap steel and molten iron are adopted as metal materials, the content of residual elements is strictly controlled, and low-Ti synthetic slag is adopted.
And thirdly, diffusion deoxidation is carried out by using aluminum and silicon carbide in the refining process, the alkalinity of the slag is controlled to be 2.5-3.5, the slag has enough fluidity to adsorb and remove impurities while certain deoxidation capability of the slag is ensured, and oxygen in steel is controlled to be in a proper range, so that the quantity of the impurities in molten steel is controlled, and spindle-shaped sulfide is formed.
Fourthly, calcium treatment is carried out on sulfide in the molten steel after VD vacuum treatment is finished so as to reduce the number of strip-shaped sulfides; the special covering slag is adopted in the continuous casting process to prevent the surface from generating crack defects.
And fifthly, forging at proper heating temperature, pre-forging temperature and final forging temperature, and cooling by combining forced cooling and slow cooling after forging, so that not only can the precipitation of refined pearlite be controlled, but also more fine pearlite structures can be obtained, the tensile strength of the product is improved, and abnormal structures such as martensite are prevented. A microstructure having excellent toughness is obtained.
Through the synergistic efforts, the high-performance low-weight expansion-fracture connecting rod material is successfully designed, the surface quality of the material is good, abnormal structures such as martensite and bainite are effectively controlled, the ferrite proportion is not more than 15%, the sulfide appearance is excellent, the cutting performance is good, and the successful development of the material is beneficial to promoting the lightweight process of automobiles.
Detailed Description
The raw materials and equipment used in the examples are all common raw materials and equipment in the field if not specified; the methods used in the present invention are conventional in the art unless otherwise specified. The following are merely preferred embodiments of the present invention and are not intended to limit the present invention.
According to the chemical composition of the steel 36MnVS4, the following production process steps are adopted:
example 1
(1) Electric furnace smelting
Adopting 75t blast furnace molten iron and 25t high-quality scrap steel to control the end point of the electric furnace: 0.05-0.30% of C, less than or equal to 0.013% of P, adding silicomanganese, ferrosilicon and low titanium ferrochrome (Ti is less than or equal to 0.03%) into a ladle in sequence after tapping 1/3, and then adding slag: 400 kg lime and 400 kg low titanium synthetic slag (MgO less than or equal to 2 percent, Al)2O337～43％、H2O≤0.5％、TiO2≤0.10％、CaO42～48％、SiO28-15%) and 80-100 kg of calcium carbide.
(2) LF refining
The slag surface deoxidation of the slag is carried out by using 80-100 kg of aluminum powder per furnace in the early stage of refining, the deoxidation and the slag fluidity adjustment are carried out by using 60-120 kg of silicon carbide per furnace in the whole refining process, and the slag alkalinity (CaO/SiO) in the later stage of refining is controlled2) 2.5-3.5, feeding an aluminum wire in the later stage of refining to adjust the aluminum content, controlling the Al content of the LF refining to be 0.035-0.045%, and controlling the oxygen content of the molten steel to be 11-18 ppm.
(3) VD vacuum treatment
And controlling the ultimate vacuum treatment time for 10-18 min, feeding 50-80 m of calcium silicon wire into each furnace steel after VD vacuum treatment is finished to carry out calcium treatment on sulfides in the molten steel, and carrying out soft argon blowing on the molten steel after the calcium treatment is finished, wherein the soft argon blowing time is controlled for 25-45 min.
(4) Continuous casting
Controlling the superheat degree of molten steel to be 15-30 ℃, and controlling the crystallizer casting powderThe special casting powder for medium-carbon sulfur-containing steel is adopted, and the physical and chemical performance indexes are designed as follows: SiO 2232±3％、CaO 24±2.5％、Al2O3 6.5±1.5％、FeO≤3.0％、MgO 6.0±1.5％、F-3.5±1.0％、R2O(K2O+Na2O 5.0±1.5％、FC 12±1.5％；CaO/SiO20.75 ± 0.05, melting point: 1260 plus or minus 20 ℃ and 0.66 plus or minus 0.20 of viscosity (Pa.S/1300 ℃), and after continuous casting and billet discharging, pit slow cooling is carried out, wherein the pit feeding temperature is not lower than 500 ℃, and the slow cooling time is not less than 48 hours;
(5) rolling of
And heating the 220 x 260 section continuous casting billet by a heating furnace and then rolling to obtain the round rod with the specification of 60 mm.
(6) Connecting rod blank forging
The method comprises the steps of blanking a round rod, heating at 1150-1200 ℃, forging, controlling the temperature of pre-forging and pressing at 1100-1130 ℃, controlling the temperature of final forging at 920-960 ℃, forging to obtain a connecting rod blank, blowing air to cool the hot connecting rod blank to 600 +/-10 ℃ on a conveyer belt within 5-8 min after forging is finished, carrying out forced cooling, and then moving the connecting rod blank into a sand box from the air-cooled conveyer belt for slow cooling (the cooling rate is 0.03-0.10 ℃/S).
Five batches of round steel are prepared by adopting the process and correspondingly processed into five batches of connecting rod blanks, the specific different conditions are shown in table 1, and other process parameters are the same.
TABLE 1
| Basicity of slag | Controlling the oxygen content (%) | Feeding calcium silicate wire | Forced cooling time | Rate of slow cooling | |
| Example 1 | 2.9 | 0.00153 | 80m | 6min30S | 0.04 |
| Example 2 | 3.0 | 0.00147 | 70m | 6min35S | 0.06 |
| Example 3 | 3.2 | 0.00143 | 60m | 7min13S | 0.05 |
| Example 4 | 2.9 | 0.00156 | 60m | 6min39S | 0.08 |
| Example 5 | 2.7 | 0.00161 | 70m | 6min11S | 0.03 |
Comparative example 1
Comparative example 1 is different from example 1 in that: the special synthetic slag is not added in the electric furnace steel tapping process, and the common synthetic slag (common synthetic slag TiO) is used2Content of 0.5 to 1.0%), and the other operations are the same as in example 1.
Comparative example 2
Comparative example 2 differs from example 1 in that: the crystallizer does not adopt special covering slag, and adopts common covering slag (component SiO of common protection)2 28±3％、CaO 25±2.5％、Al2O3 8±1.5％、FeO≤3.0％、MgO 2.0±0.5％、F-3.5±1.0％、R2O(K2O+Na2O 7.0±1.5％、FC 15±1.5％；CaO/SiO20.80 ± 0.05, melting point: 1110. + -. 20 ℃ and a viscosity (Pa.S/1300 ℃) of 0.61. + -. 0.20, which is 150 ℃ lower than that of the exclusive mold flux, and a viscosity (Pa.S/1300 ℃) of 0.05, and the other operations are the same as those of example 1.
Comparative example 3
Comparative example 3 differs from example 1 in that: the oxygen content was controlled to be less than 11ppm and the procedure in example 1 was otherwise the same.
Comparative example 4
Comparative example 4 is different from example 1 in that: the same procedure as in example 1 was carried out except that the molten steel was not subjected to the calcium treatment.
Comparative example 5
Comparative example 5 differs from example 1 in that: after the connecting rod blank is blown to cool and is off the line, the connecting rod blank does not enter a slow cooling box for slow cooling, and the cooling mode of direct stacking cooling is adopted, and other operations are the same as those in embodiment 1.
Comparative example 6
Comparative example 6 differs from example 1 in that: the hot connecting rod blank is blown on a conveyer belt to be cooled to 600 +/-10 ℃ 12 minutes after the forging is finished, and other operations are the same as the embodiment 1.
(1) The chemical compositions of examples 1 to 5 of the present invention and comparative examples 1 to 6 are as follows (wt%):
TABLE 2
| Item | Number plate | C | Si | Mn | Cr | P | S | Al | Ni | V | O | N | Ti |
| Example 1 | 36MnVS4 | 0.36 | 0.69 | 1.00 | 0.17 | 0.011 | 0.039 | 0.015 | 0.12 | 0.30 | 0.00153 | 0.0173 | 0.0033 |
| Example 2 | 36MnVS4 | 0.35 | 0.70 | 1.01 | 0.19 | 0.012 | 0.039 | 0.014 | 0.11 | 0.30 | 0.00147 | 0.0180 | 0.0029 |
| Example 3 | 36MnVS4 | 0.36 | 0.68 | 0.99 | 0.18 | 0.009 | 0.040 | 0.016 | 0.13 | 0.29 | 0.00143 | 0.0169 | 0.0028 |
| Example 4 | 36MnVS4 | 0.36 | 0.70 | 1.00 | 0.18 | 0.010 | 0.038 | 0.013 | 0.11 | 0.29 | 0.00156 | 0.0175 | 0.0034 |
| Example 5 | 36MnVS4 | 0.35 | 0.69 | 0.98 | 0.17 | 0.011 | 0.041 | 0.012 | 0.12 | 0.30 | 0.00161 | 0.0183 | 0.0031 |
| Comparative example 1 | 36MnVS4 | 0.34 | 0.71 | 0.97 | 0.18 | 0.013 | 0.038 | 0.009 | 0.12 | 0.31 | 0.00179 | 0.0191 | 0.0071 |
| Comparative example 2 | 36MnVS4 | 0.37 | 0.70 | 0.98 | 0.19 | 0.014 | 0.040 | 0.010 | 0.11 | 0.29 | 0.00175 | 0.0185 | 0.0042 |
| Comparative example 3 | 36MnVS4 | 0.36 | 0.68 | 0.99 | 0.17 | 0.012 | 0.036 | 0.008 | 0.13 | 0.31 | 0.00103 | 0.0189 | 0.0045 |
| Comparative example 4 | 36MnVS4 | 0.35 | 0.70 | 1.00 | 0.18 | 0.013 | 0.042 | 0.016 | 0.12 | 0.30 | 0.00176 | 0.0157 | 0.0039 |
| Comparative example 5 | 36MnVS4 | 0.36 | 0.67 | 0.99 | 0.17 | 0.012 | 0.037 | 0.012 | 0.11 | 0.29 | 0.00138 | 0.0171 | 0.0036 |
| Comparative example 6 | 36MnVS4 | 0.36 | 0.69 | 0.99 | 0.17 | 0.013 | 0.038 | 0.011 | 0.12 | 0.29 | 0.00136 | 0.0170 | 0.0038 |
(2) The following table 3 shows the sulfide grades, the sulfide morphology and the service life of the tool:
TABLE 3
The detection standard of the sulfide grade is as follows: the method comprises the steps of measuring the content of non-metallic inclusions in GB/T10561 steel, namely, carrying out microscopic inspection on a standard rating image, selecting a plurality of fields by scanning an electron microscope, then counting the number of sulfides in each field, and then measuring the length-width ratio of each sulfide under the scanning electron microscope. Finally, the number of sulfides with the length/width not more than 3 is counted.
(3) The mechanical property indexes and the service performance comparison conditions of the manufactured connecting rod forging are as follows in the following table 4:
TABLE 4 mechanical Properties of non-quenched and tempered connecting rod
The results show that: by optimally designing the components, adopting special synthetic slag and crystallizer casting powder, controlling the oxygen content to be 11-18 PPM, simultaneously carrying out calcium treatment on the molten steel, adopting reasonable temperature for forging heating, controlling the pre-forging and final forging temperature, and adopting a cooling mode combining air cooling and slow cooling after forging, the successful production of the medium-carbon non-quenched and tempered steel 36MnVS4 for the automobile expansion-broken connecting rod and the forged piece thereof is finally realized, the cutting performance is greatly improved, and the index levels of the strength, the yield ratio and the plastic toughness also reach the international advanced level.
Claims (3)
1. A forging method of medium carbon non-quenched and tempered steel for an automobile expansion fracture connecting rod is characterized by comprising the following steps:
(1) after blanking, the round bar is heated at a proper temperature in an induction heating furnace, and the pre-forging and pressing temperature and the final forging temperature are controlled;
(2) after the forging is finished, a cooling mode combining forced cooling and slow cooling is adopted, and when the connecting rod blank is cooled to normal temperature, flaw detection is carried out to obtain a qualified connecting rod blank;
step (1), controlling the heating temperature to 1150-1200 ℃, controlling the pre-forging temperature to 1100-1130 ℃, and controlling the finish forging temperature to 920-960 ℃;
blowing air to cool the hot connecting rod blank to 600 +/-10 ℃ on a conveyer belt for strong cooling within 5-8 minutes after the forging is finished, and then slowly cooling the connecting rod blank at the cooling rate of 0.03-0.10 ℃/S;
the round bar is prepared by the following method: the method comprises the working procedures of electric furnace smelting, LF furnace refining, VD vacuum treatment, continuous casting pouring and rolling, and comprises the following specific steps:
1) smelting in an electric furnace, wherein 65-75% of blast furnace molten iron and 25-35% of high-quality scrap steel are adopted; controlling the end point C of the electric furnace to be 0.05-0.30% and P to be less than or equal to 0.013%; the tapping 1/3 starts to add silicomanganese, ferrosilicon and low titanium ferrochrome into the ladle in sequence, and then slag and calcium carbide are added for pre-deoxidation of molten steel;
2) electrifying to melt slag firstly in LF refining, then deoxidizing the slag surface of the slag by using aluminum powder, carrying out slag surface deoxidation and slag fluidity adjustment by using silicon carbide according to the slag condition in the refining process, and controlling the slag alkalinity CaO/SiO in the later stage of refining22.5-3.5, feeding an aluminum wire to adjust the aluminum content and controlling the oxygen content of the molten steel to be 11-18 ppm;
(3) controlling VD limit vacuum treatment time for 10-18 min, feeding calcium silicate wire to perform calcium treatment on sulfide and aluminum deoxidation products in molten steel after VD vacuum treatment is finished, and performing soft argon blowing on the molten steel after the calcium treatment is finished, wherein the soft argon blowing time is controlled for 25-45 min;
4) continuous casting, wherein the superheat degree of molten steel is required to be controlled to be 15-30 ℃, the crystallizer casting powder is special medium-carbon sulfur-containing steel casting powder, slow cooling is adopted after continuous casting and billet ejection, the temperature of a slow cooling pit is required to be not lower than 500 ℃, and the slow cooling time is not less than 48 hours;
5) heating and then rolling the continuous casting billet on the section to obtain a round bar with a target component;
the round bar comprises the following components in percentage by weight: 0.34-0.38% of C, 0.65-0.75% of Si, 0.95-1.05% of Mn, less than or equal to 0.020% of P, 0.030-0.045% of S, 0.11-0.14% of Ni, 0.15-0.23% of Cr, 0.008-0.020% of Al, 0.28-0.32% of V, less than or equal to 0.006% of Ti, less than or equal to 0.05% of Mo, 0.015-0.020% of N, and the balance of Fe and inevitable impurities;
the slag charge in the step 1) consists of lime and low-titanium synthetic slag, wherein the low-titanium synthetic slag comprises the following components in percentage by weight: MgO less than or equal to 2 percent and Al2O337～43％、H2O≤0.5％、TiO2 ≤0.10％、CaO 42～48％、SiO2 8～15％；
Step 4) continuous casting crystallizer casting powder with SiO as the component2 32±3％、CaO 24±2.5％、Al2O3 6.5±1.5％、FeO≤3.0％、MgO 6.0±1.5％、F-3.5±1.0％、R2O 5.0±1.5％、FC 12±1.5％、CaO/SiO20.75 + -0.05, melting point 1260 + -20 deg.C, viscosity 0.66 + -0.20 Pa.S at 1300 deg.C, wherein R is2O is K2O and Na2O。
2. The forging method of the medium-carbon non-quenched and tempered steel for the automobile fractured connecting rod according to claim 1, wherein the forging method comprises the following steps: and 2) feeding an aluminum wire to adjust the aluminum content, controlling the Al content of the LF refining to be 0.035-0.045%, and enabling the aluminum to be in place in one step to prevent the VD from being reused after the vacuum is finished.
3. The forging method of the medium-carbon non-quenched and tempered steel for the automobile fractured connecting rod according to claim 1, wherein the forging method comprises the following steps: and 3) feeding 50-80 m of calcium silicon wire into each furnace of steel to perform calcium treatment on the molten steel.
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| CN113522964A (en) * | 2021-07-15 | 2021-10-22 | 承德建龙特殊钢有限公司 | Steel bar for expansion-fracture connecting rod and preparation method thereof |
| CN114178498A (en) * | 2021-10-26 | 2022-03-15 | 南京钢铁股份有限公司 | Special covering slag for non-quenched and tempered steel continuous casting crystallizer and preparation process thereof |
| CN114645208B (en) * | 2022-03-23 | 2023-04-25 | 青海西钢特殊钢科技开发有限公司 | Tellurium-treated non-quenched and tempered steel for connecting rod and production method thereof |
| CN115141976B (en) * | 2022-06-24 | 2023-07-25 | 江苏联峰能源装备有限公司 | Tough microalloyed non-quenched and tempered steel and production process thereof |
| CN115537663B (en) * | 2022-10-13 | 2023-06-02 | 宝武杰富意特殊钢有限公司 | High-silicon high-nitrogen non-quenched and tempered steel and preparation method thereof |
| CN117259662B (en) * | 2023-11-22 | 2024-02-06 | 江苏永钢集团有限公司 | Forging and cooling control process for medium-carbon microalloy non-quenched and tempered expansion connecting rod |
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