CN111304517A - High-strength high-yield-ratio non-quenched and tempered steel for automobile engine cracking connecting rod and production method thereof - Google Patents
High-strength high-yield-ratio non-quenched and tempered steel for automobile engine cracking connecting rod and production method thereof Download PDFInfo
- Publication number
- CN111304517A CN111304517A CN202010145323.5A CN202010145323A CN111304517A CN 111304517 A CN111304517 A CN 111304517A CN 202010145323 A CN202010145323 A CN 202010145323A CN 111304517 A CN111304517 A CN 111304517A
- Authority
- CN
- China
- Prior art keywords
- connecting rod
- quenched
- steel
- yield
- automobile engine
- 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.)
- Granted
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 92
- 239000010959 steel Substances 0.000 title claims abstract description 92
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 20
- 238000005336 cracking Methods 0.000 title claims abstract description 17
- 238000005096 rolling process Methods 0.000 claims abstract description 23
- 238000001816 cooling Methods 0.000 claims abstract description 18
- 238000000034 method Methods 0.000 claims abstract description 18
- 230000008569 process Effects 0.000 claims abstract description 15
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 239000002893 slag Substances 0.000 claims description 13
- 238000003756 stirring Methods 0.000 claims description 12
- 238000009749 continuous casting Methods 0.000 claims description 11
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 8
- 238000001514 detection method Methods 0.000 claims description 8
- 238000007670 refining Methods 0.000 claims description 8
- 238000003723 Smelting Methods 0.000 claims description 7
- 229910045601 alloy Inorganic materials 0.000 claims description 7
- 239000000956 alloy Substances 0.000 claims description 7
- 238000010583 slow cooling Methods 0.000 claims description 7
- 238000010438 heat treatment Methods 0.000 claims description 6
- 238000009489 vacuum treatment Methods 0.000 claims description 6
- 229910052786 argon Inorganic materials 0.000 claims description 4
- 238000007599 discharging Methods 0.000 claims description 4
- 238000010079 rubber tapping Methods 0.000 claims description 4
- 238000007664 blowing Methods 0.000 claims description 2
- 239000000203 mixture Substances 0.000 claims 1
- 238000010791 quenching Methods 0.000 claims 1
- 230000000171 quenching effect Effects 0.000 claims 1
- 238000005496 tempering Methods 0.000 claims 1
- 239000000463 material Substances 0.000 abstract description 24
- 239000000126 substance Substances 0.000 abstract description 7
- 239000011572 manganese Substances 0.000 description 23
- 239000010955 niobium Substances 0.000 description 21
- 239000012071 phase Substances 0.000 description 14
- 230000000694 effects Effects 0.000 description 12
- 238000005728 strengthening Methods 0.000 description 12
- 229910052799 carbon Inorganic materials 0.000 description 9
- 229910052758 niobium Inorganic materials 0.000 description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 8
- 229910052757 nitrogen Inorganic materials 0.000 description 8
- 229910052720 vanadium Inorganic materials 0.000 description 8
- 230000009286 beneficial effect Effects 0.000 description 7
- 238000005520 cutting process Methods 0.000 description 7
- 238000005266 casting Methods 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 6
- 230000009466 transformation Effects 0.000 description 6
- 229910052748 manganese Inorganic materials 0.000 description 5
- 230000002829 reductive effect Effects 0.000 description 5
- 238000005204 segregation Methods 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 238000009628 steelmaking Methods 0.000 description 5
- 239000010936 titanium Substances 0.000 description 5
- 229910000859 α-Fe Inorganic materials 0.000 description 5
- 239000002131 composite material Substances 0.000 description 4
- 238000003754 machining Methods 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 238000007667 floating Methods 0.000 description 3
- 238000005242 forging Methods 0.000 description 3
- 230000036961 partial effect Effects 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 229910000616 Ferromanganese Inorganic materials 0.000 description 2
- 229910000954 Medium-carbon steel Inorganic materials 0.000 description 2
- 229910001563 bainite Inorganic materials 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- DALUDRGQOYMVLD-UHFFFAOYSA-N iron manganese Chemical compound [Mn].[Fe] DALUDRGQOYMVLD-UHFFFAOYSA-N 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 241001391944 Commicarpus scandens Species 0.000 description 1
- 229910000915 Free machining steel Inorganic materials 0.000 description 1
- 229910001257 Nb alloy Inorganic materials 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- -1 carburant Substances 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000004134 energy conservation Methods 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 238000007689 inspection Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 230000001050 lubricating effect Effects 0.000 description 1
- 235000013372 meat Nutrition 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- ABLLXXOPOBEPIU-UHFFFAOYSA-N niobium vanadium Chemical compound [V].[Nb] ABLLXXOPOBEPIU-UHFFFAOYSA-N 0.000 description 1
- 238000004806 packaging method and process Methods 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 229910001404 rare earth metal oxide Inorganic materials 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- CADICXFYUNYKGD-UHFFFAOYSA-N sulfanylidenemanganese Chemical compound [Mn]=S CADICXFYUNYKGD-UHFFFAOYSA-N 0.000 description 1
- 150000004763 sulfides Chemical class 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- GFNGCDBZVSLSFT-UHFFFAOYSA-N titanium vanadium Chemical compound [Ti].[V] GFNGCDBZVSLSFT-UHFFFAOYSA-N 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
- 238000005303 weighing 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
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—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
-
- 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
- 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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
Abstract
The invention discloses a high-strength high-yield-ratio non-quenched and tempered steel for a cracking connecting rod of an automobile engine and a production method thereof, wherein the steel comprises the following chemical components in percentage by weight: 0.40-0.50% of C, 0.40-0.60% of Si, 1.00-1.30% of Mn, 0.040-0.060% of S, 0.10-0.20% of V, 0.020-0.035% of Nb, 0.10-0.30% of Cr, 0.10-0.30% of Ni, 0.010-0.020% of N, and the balance of Fe and impurity elements. By the combination of the component proportion and the controlled rolling and cooling process, the mechanical property Rel of the connecting rod material is more than or equal to 850MPa, Rm is more than or equal to 1000MPa, the yield ratio can reach more than 0.84, and the lightweight of an automobile engine is facilitated.
Description
Technical Field
The invention discloses steel for an automobile engine cracking connecting rod, belongs to the field of non-quenched and tempered steel, and particularly relates to niobium-vanadium composite reinforced non-quenched and tempered steel for the automobile engine cracking connecting rod.
Background
The connecting rod of the automobile engine is one of five key parts in the automobile engine, and transmits the borne piston pressure to the crankshaft to form a moving part together with the piston. The connecting rod is used as a core stress component of the engine and bears strong alternating load, and the quality of the connecting rod directly influences the performance and the reliability of the engine.
The connecting rod machining mainly comprises two processes of cutting and cracking, the traditional connecting rod machining process is complex, the stability of an engine is affected due to machining precision errors, the problem is well solved by the technology of cracking the connecting rod, the machining procedures are few, and the production cost of the connecting rod is remarkably reduced. The expansion-breaking connecting rod technology has special requirements on materials, namely, on the premise of ensuring comprehensive properties such as toughness and the like, the toughness of the connecting rod is limited, namely, the materials are required not to generate large plastic deformation in the expansion-breaking process, so that a fracture presents proper brittle fracture characteristics, the requirement on the roundness of a large-head hole in the subsequent processing procedure is met, and the cutting performance is good.
At present, a series of non-quenched and tempered steels for cracking connecting rods are developed domestically, and the typical steels include 38MnV, 40MnV, 48MnV, C70, C70S6 and the like. The high-carbon non-quenched and tempered steel C70S6 is widely applied at present, and the C70S6 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. In addition, with the development trend of light weight and energy conservation of automobiles, 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.
CN201510332645.X discloses a steel for an automobile engine expansion-fracture connecting rod, wherein the steel for the automobile expansion-fracture connecting rod with high strength, proper brittleness and good cutting processability can be produced by adding 0.15-0.25 wt% of microalloying element V and controlling 0.015-0.025 wt% of N, and other elements are reasonably matched, wherein the strength of the connecting rod is equal to or more than 800MPa, and Rm is equal to or more than 1100 MPa. However, the material has a low yield ratio, and the product performance cannot be effectively utilized, so that the material is not beneficial to light weight.
CN201811175895.7 discloses a non-quenched and tempered steel of a high-strength fractured connecting rod and a continuous casting production process thereof, the strength of a connecting rod material is further improved by adopting titanium-vanadium composite reinforcement, 0.030-0.070 wt% of Ti and 0.25-0.35 wt% of V, and controlling 0.015-0.025% of N, the performance of a connecting rod forging piece can reach Rel not less than 900MPa, Rm not less than 1100MPa, but under the current Ti and N contents, a large-size TiN phase with the diameter of tens of microns can be precipitated in the solidification process, so that the beneficial effect of Ti is reduced, and the fatigue performance of the connecting rod is damaged.
CN201810637610.0 discloses a medium-carbon non-quenched and tempered expansion-broken connecting rod steel and a manufacturing method thereof, wherein the tensile strength Rm of the connecting rod steel can reach 950-1200 MPa, the yield strength is more than or equal to 750MPa, and the yield ratio is more than or equal to 0.73 on the premise of ensuring the expansion-breaking performance of the steel by adding 0.030-0.060% of P, 0.17-0.24% of V and 0.036-0.045% of Nb into the steel. The effect of the P element on the tensile strength of the material is greater than the yield strength, which is not beneficial to the increase of the yield ratio; in addition, the influence of more than 0.20 percent of the V element on the yield ratio is not great, the content of the Nb element in the medium carbon steel reaches more than 0.035 percent, the probability of generating large-particle liquated carbide is increased, the strengthening effect is weakened, the fatigue performance of the product is not facilitated, and in addition, the V, Nb alloy is expensive, so the cost of the product is increased.
CN201410421719.2 discloses free-cutting steel with tensile strength not less than 1200MPa for automobile connecting rods and a production method thereof, the strength of the steel is improved by adding B, the tensile strength is not less than 1200MPa, and the yield strength is not less than 850 MPa; the element B improves the strength of the steel mainly by segregation at grain boundaries, but the ductility of the grain boundary reinforced steel becomes good, which is not beneficial to the increase of the yield ratio of the steel.
CN201510092255.X discloses a high-strength and high-toughness non-quenched and tempered steel suitable for composite forging forming, wherein V is 0.01-0.15%, Nb is 0.005-0.05%, RE is 0.001-0.0075, P is 0.005-0.03%, N is 0.008-0.02%, and Ti is 0.01-0.15%, C content is reduced to 0.25-0.40%, and tensile strength R of a forging ismNot less than 900MPa, yield strength Rp0.2Not less than 750MPa, yield ratio up to 0.85 and above, low strength, difficult rare earth addition in the steel-making process, and difficult floating removal of the generated rare earth oxide, thereby reducing the cleanliness of the steel.
It is known from the above prior art that it is not easy to obtain a material for a connecting rod having a high yield ratio while maintaining high strength. This is because, even if the influence of the elements on the strength is known, the influence of each element on the yield ratio is not clear and there is a different view in the literature. Therefore, the technical problem to be solved by the invention is how to obtain the material for the cracking connecting rod with high strength and high yield ratio.
The method aims to obtain the expansion-fracture connecting rod material with low cost, high strength and high yield ratio, and the yield ratio of the material is further improved by reasonably matching C, N, Nb and V elements while ensuring the performances of expansion fracture, strength and the like required by the connecting rod material.
Disclosure of Invention
The invention relates to a non-quenched and tempered steel for a high-strength high-yield ratio automobile cracking connecting rod, which is characterized in that in order to ensure the strength of the steel and further improve the yield ratio, each element is divided reasonably, and the adopted component design scheme is as follows: the strength of the steel is ensured by reasonably selecting basic elements C, Si, Mn, Cr and Ni; microalloying elements of niobium and vanadium are adopted for composite strengthening, the content of the Nb element is not higher than 0.035%, the content of the V element is controlled to be 0.10-0.20%, the partial Nb element is combined with C, N at high temperature to separate out niobium carbonitride, the effects of increasing dislocation and refining grains can be achieved in the rolling process, so that the yield ratio of the steel is improved, and the rest Nb and V are separated out of strengthening soft-phase ferrite in the subsequent phase transformation process and after phase transformation, so that the yield ratio of the steel is further improved; by matching with a proper rolling and cooling control process, the mechanical property Rel of the connecting rod material is more than or equal to 850MPa, Rm is more than or equal to 1000MPa, and Rel/Rm can reach more than 0.84, so that the lightweight of an automobile engine is facilitated.
The invention relates to a high-strength high-yield-ratio non-quenched and tempered steel for a cracking connecting rod of an automobile engine and a production method, which are characterized in that: the steel comprises the following chemical components in percentage by weight: 0.40-0.50% of C, 0.40-0.60% of Si, 1.00-1.30% of Mn, 0.040-0.060% of S, 0.10-0.20% of V, 0.020-0.035% of Nb, 0.10-0.30% of Cr, 0.10-0.30% of Ni, 0.010-0.020% of N, and the balance of Fe and impurity elements.
C 0.40-0.50％
C: carbon is the element which improves the strength and the cost performance of non-quenched and tempered steel, the amount of ferrite is reduced along with the increase of the content of C, the amount of pearlite is increased, the strength and the hardness of the steel are improved along with the reduction of the plasticity, the toughness and the yield ratio of the steel. The C content is limited to be within the range of 0.40-0.50% by comprehensively considering the performance and the cost of the product.
Si 0.40-0.60％
Si: si can be used as a deoxidizing element in low-aluminum steel, and has high solid solubility in iron and strong solid solution strengthening effect. However, too high Si content deteriorates the hot formability of the bar and affects the surface quality of the forged blank. The Si content is limited to 0.40-0.60%.
Mn 1.00-1.30％
Mn: the ferromanganese alloy has low price, and Mn element mainly exists in a solid solution form in steel, so that the ferromanganese alloy has strong solid solution strengthening effect. In addition, for sulfur-containing non-quenched and tempered steel, the Mn element can be combined with S to form manganese sulfide, thereby inhibiting hot brittleness of the steel, improving cutting performance and reducing tool wear. However, since the Mn content is too high, the pearlite amount increases, the yield ratio decreases, and the bainite structure is promoted, the Mn content is limited to 1.00 to 1.30%.
S 0.040-0.060％
In order to improve the cutting performance, a certain content of S is often added into non-quenched and tempered steel and combined with Mn in the steel to form MnS, so that the effect of a stress concentration source is achieved, the chips of the steel are easy to break in the cutting process, and meanwhile, the effect of lubricating a cutter can be achieved, the cutter abrasion is reduced, and the service life of the cutter is prolonged. However, sulfides are easy to deform and deform into strips in the rolling process, so that the mechanical property of the steel presents directionality, and meanwhile, the S element is a strong segregation element, and a segregation enrichment area is not beneficial to the mechanical property of the steel. The range of the S content of the present invention is defined as 0.040-0.060%.
V 0.10％-0.20％
V: the microalloying element V is an important strengthening element in non-quenched and tempered steel, and is combined with C to form a fine and dispersedly distributed carbide second phase strengthened steel matrix, and the strengthening effect of V is obviously influenced by a rolling process. The content of V is increased, the yield ratio of the steel can be effectively improved, but the content is too high, the action trend and saturation of the V are realized, and the price of the V element is high, so that the performance requirement of the steel is comprehensively considered, and the content of V is limited to 0.10-0.20%.
Nb 0.020-0.035％
The bonding capacity of Nb and C is stronger than V, the precipitation temperature is also higher than V, the crystal grain growth can be inhibited at the conventional heating temperature, dislocation can be fixed and the crystal grain can be refined in the rolling process, so that the yield ratio of the material is improved, in addition, partial solid-dissolved Nb is precipitated and strengthened soft-phase ferrite after subsequent phase transformation and phase transformation, and the yield ratio is further improved. However, the Nb element is a strong segregation element, when the Nb content of the medium carbon steel is over 0.035%, the probability of precipitating primary carbide in a liquid phase is increased, the performance of the steel is not promoted, and alloy waste is caused.
Cr 0.10-0.30
Cr is dissolved in a steel matrix in a solid mode, so that the hardenability can be remarkably improved, and the strength of steel is improved; cr is also a carbide forming element, can form carbide second phase particles in steel to strengthen a steel matrix, and can reduce the diffusion rate of C and inhibit the surface decarburization phenomenon in the heat treatment process. However, if the content is too high, bainite and other structures are generated, and the toughness is lowered, and the Cr content is limited to 0.10 to 0.30%.
Ni 0.10-0.30％
Ni is a non-carbide forming element, is mainly dissolved in a steel matrix in a solid solution manner to achieve the effect of solid solution strengthening, and meanwhile, the stability of austenite can be improved, and the hardenability of steel is remarkably improved. Also, too high Ni content more easily causes non-equilibrium structure in the steel, decreasing the toughness of the steel. The Ni content of the present invention is limited to 0.10 to 0.30%.
N 0.010-0.020％
N is an important strengthening element in non-quenched and tempered steel and can be combined with micro-alloying elements Nb and V to form second phase particles, so that on one hand, austenite grain boundaries can be pinned, grain growth is inhibited, and on the other hand, a precipitation strengthening effect is achieved. However, if the N content is too high, it is disadvantageous in steel making, and the cast slab may have bubbles and pores. The content of N in the invention is controlled to be 0.010-0.020%.
The production process of the high-strength high-yield-ratio non-quenched and tempered steel for the automobile engine cracking connecting rod comprises the following steps: electric furnace/converter smelting, LF refining, VD/RH vacuum treatment, continuous casting, slow cooling, inspection, heating by a heating furnace, controlled rolling, cooling, ultrasonic and magnetic flux leakage flaw detection, packaging, weighing and warehousing.
Wherein during electric furnace/converter smelting, the initial smelting end point C is controlled to be more than or equal to 0.08 percent, molten steel is prevented from being oxidized, and slag is strictly forbidden to be discharged; a deoxidizer, an alloy, a recarburizer and slag charge are added in sequence during the tapping process;
during LF refining, component fine adjustment is carried out, the reducing atmosphere in the furnace is kept, the alkalinity of furnace slag is controlled to be 2.0-3.0, argon is blown from the bottom to stir, the temperature and the components are uniform, non-metallic inclusions in steel are promoted to float upwards and be removed, and the purity of molten steel is ensured; and controlling the Mn content at the LF end point, and reserving proper allowance for adjusting the Mn and N contents after vacuum.
Vacuum treatment process, ensuring high vacuum (less than or equal to 67Pa) time to be more than or equal to 10min, feeding N-Mn line and S line according to detection components after breaking empty; the soft blowing time is controlled to be more than 15 minutes.
The continuous casting adopts crystallizer electromagnetic stirring and tail end detection stirring to control the macrostructure and component segregation of the continuous casting billet, and the secondary cooling adopts a weak cooling mode; and after continuous casting and billet discharging, putting the cast slab into a pit, covering the cast slab and slowly cooling, wherein the temperature of the cast slab in the pit is more than or equal to 450 ℃, and the slow cooling time is selected according to the size of the cast slab.
In the controlled rolling process, the initial rolling temperature is controlled to be 1080-.
The invention has the beneficial effects that:
the invention relates to a high-strength high-yield-ratio non-quenched and tempered steel for an automobile engine cracking connecting rod and a production method thereof, which aim at the yield ratio to carry out reasonable component design while ensuring the strength and the toughness of a connecting rod product, and except for reasonable matching of basic elements, the yield ratio of the steel is further improved by adding Nb and V elements and reasonably designing the content of the Nb and V elements: as for automobile parts, the higher the yield ratio, the higher the material utilization rate, and the more beneficial to the light weight of the automobile. According to the invention, the second phase is precipitated from partial Nb at high temperature, so that the effects of increasing dislocation, refining crystal grains and precipitation strengthening are achieved, the yield ratio of the material is improved, the precipitation strengthening effect is better compared with other microalloying elements such as Ti, large-size liquid phase titanium nitride is not generated, and the fatigue strength of the product is further ensured; in addition, the V element and the residual Nb element are separated out in the phase transformation process from austenite to ferrite and after phase transformation, the strength of soft-phase ferrite is improved, and the yield ratio of the product is further improved. Besides the component proportion, the mechanical property of the connecting rod material is finally ensured to meet the requirement of the expansion-broken connecting rod by combining a rolling and cooling control process, Rel is more than or equal to 850MPa, Rm is more than or equal to 1000MPa, Rel/Rm reaches more than 0.84, and the lightweight automobile engine is facilitated.
Drawings
FIG. 1 is a diagram of a fracture of a connecting rod blank made of the connecting rod material produced in the embodiment 1.
Detailed Description
The present invention is further illustrated with reference to the following specific examples, but the scope of the present invention is not limited to the following examples. Specific conditions not specified in the following examples are not particularly limited to conventional conditions, and those skilled in the art can flexibly select the conditions according to actual circumstances. The materials (such as carburant, slag, etc.) or instruments used are not indicated by manufacturers, and are all conventional products which can be obtained by commercial purchase.
Example 1:
a high-strength high-yield-ratio non-quenched and tempered steel for a cracking connecting rod of an automobile engine and a production method thereof are disclosed, wherein the steel comprises the following chemical components in percentage by weight: 0.45 percent of C, 0.56 percent of Si, 1.23 percent of Mn, 0.049 percent of S, 0.15 percent of V, 0.029 percent of Nb0.20 percent of Cr, 0.13 percent of Ni, 0.016 percent of N, and the balance of Fe and impurity elements.
The initial smelting end point C is 0.20 percent, molten steel is prevented from being oxidized, and slag is strictly prevented from being discharged; a deoxidizer, an alloy, a recarburizer and slag charge are added in sequence during the tapping process; fine adjustment of components is carried out in LF refining, the reducing atmosphere in a furnace is kept, the alkalinity of slag is 2.5, argon is blown from the bottom for stirring, the temperature and the components are uniform, the floating removal of non-metallic inclusions in steel is promoted, and the purity of molten steel is ensured; the Mn content at the LF end point is 1.08%, and a proper margin is reserved for adjusting the Mn and N contents after vacuum.
Vacuum treatment, wherein the high vacuum (less than or equal to 67Pa) time is 12min, and N-Mn lines and S lines are fed according to detection components after the vacuum is broken; soft blow time 20 minutes.
Electromagnetic stirring of a crystallizer and tail end detection stirring are adopted in continuous casting, and a weak cooling mode is adopted in secondary cooling, wherein the specific water amount is 0.20L/kg; the section of the casting blank is 220mm by 260mm, the casting blank is put into a pit and covered with a cover for slow cooling after being continuously cast and discharged, the temperature of the casting blank in the pit is 510 ℃, and the slow cooling time is 38 hours.
The initial rolling temperature is 1130 ℃, the final rolling temperature is 920 ℃, and air cooling is carried out after rolling is finished.
FIG. 1 is a diagram of a fracture of a connecting rod blank made of the connecting rod material produced in example 1, and it is seen from the fracture diagram that the fracture of the produced material is flat and has no meat drop or burr.
Example 2:
a high-strength high-yield-ratio non-quenched and tempered steel for a cracking connecting rod of an automobile engine and a production method thereof are disclosed, wherein the steel comprises the following chemical components in percentage by weight: 0.47% of C, 0.54% of Si, 1.25% of Mn, 0.047% of S, 0.14% of V, 0.030% of Nb0.030% of Cr, 0.21% of Ni, 0.016% of N, and the balance of Fe and impurity elements.
The initial smelting end point C is 0.21 percent, molten steel is prevented from being oxidized, and slag discharging is strictly forbidden; a deoxidizer, an alloy, a recarburizer and slag charge are added in sequence during the tapping process; fine adjustment of components is carried out in LF refining, the reducing atmosphere in a furnace is kept, the alkalinity of slag is 2.3, argon is blown from the bottom for stirring, the temperature and the components are uniform, the floating removal of non-metallic inclusions in steel is promoted, and the purity of molten steel is ensured; the Mn content at the LF end point is 1.08%, and a proper margin is reserved for adjusting the Mn and N contents after vacuum.
Vacuum treatment, wherein the high vacuum (less than or equal to 67Pa) time is 13min, and N-Mn lines and S lines are fed according to detection components after the vacuum breaking; soft blow time 25 minutes.
Electromagnetic stirring of a crystallizer and tail end detection stirring are adopted in continuous casting, and a weak cooling mode is adopted in secondary cooling, wherein the specific water amount is 0.20L/kg; the section of the casting blank is 220mm by 260mm, the casting blank is put into a pit and covered with a cover for slow cooling after continuous casting and discharging, the temperature of the casting blank in the pit is 530 ℃, and the slow cooling time is 40 hours.
The initial rolling temperature is 1120 ℃, the final rolling temperature is 925 ℃, and the air cooling is carried out after the rolling is finished.
To further illustrate the synergistic relationship between the components of the present invention, specific comparative examples are as follows:
comparative example 1:
the chemical components by weight percentage are as follows: 0.35% of C, 0.50% of Si, 1.21% of Mn, 0.045% of S, 0.15% of V, 0.025% of Nb, 0.21% of Cr, 0.15% of Ni, 0.016% of N, and the balance of Fe and impurity elements.
The steel making process and the steel rolling process are the same as those of example 2.
Comparative example 2:
the chemical components by weight percentage are as follows: 0.47% of C, 0.31% of Si, 0.91% of Mn, 0.050% of S, 0.10% of V, 0.18% of Cr, 0.20% of Ni, 0.015% of N, and the balance of Fe and impurity elements.
The steel making process and the steel rolling process are the same as in comparative example 1.
Comparative example 3:
the chemical components by weight percentage are as follows: 0.38% of C, 0.69% of Si, 1.48% of Mn, 0.047% of S, 0.11% of V, 0.21% of Cr, 0.15% of Ni, 0.016% of N, and the balance of Fe and impurity elements.
The steel making process and the steel rolling process are the same as in comparative example 1.
TABLE 1 examples mechanical properties (normalized state) of rolled stock
The above embodiments are preferred embodiments of the present invention, but the present invention is not limited to the above embodiments. Obvious improvements, changes and modifications to some technical features in the foregoing embodiments can be made by those skilled in the art without departing from the technical idea of the present invention, and the technical scope of the present invention is not limited to the contents of the specification, but must be determined from the scope of the claims.
Claims (9)
1. The utility model provides a non-quenching and tempering steel of high strength high yield ratio for automobile engine rises disconnected connecting rod which characterized in that: the steel comprises, by weight, 0.40-0.50% of C, 0.40-0.60% of Si, 1.00-1.30% of Mn, 0.040-0.060% of S, 0.10-0.20% of V, 0.020-0.035% of Nb, 0.10-0.30% of Cr, 0.10-0.30% of Ni, 0.010-0.020% of N, and the balance of Fe and impurity elements.
2. The high-strength high-yield-ratio non-quenched and tempered steel for the pop-up connecting rod of the automobile engine as claimed in claim 1, wherein Rel of the non-quenched and tempered steel is not less than 850MPa, Rm of the non-quenched and tempered steel is not less than 1000MPa, and the yield ratio of the non-quenched and tempered steel is more than 0.84.
3. The production method of the non-quenched and tempered steel with high strength and high yield ratio for the automobile engine cracking connecting rod as recited in claim 2, wherein the production process comprises the following steps: smelting in an electric furnace or a converter, LF refining, VD or RH vacuum treatment, continuous casting, slow cooling, heating in a heating furnace, controlled rolling and cooling.
4. The method for producing a high-strength high-yield-ratio non-quenched and tempered steel for an automobile engine cracking connecting rod as claimed in claim 3, wherein the initial smelting end point C is controlled to be not less than 0.08%, molten steel is prevented from being oxidized, and slag is prevented from being discharged strictly; and a deoxidizer, an alloy, a recarburizer and slag charge are added in sequence during the tapping process.
5. The method for producing a high-strength high-yield-ratio non-quenched and tempered steel for an automobile engine pop-up connecting rod as claimed in claim 3, wherein the composition is finely adjusted during LF refining, the reducing atmosphere in the furnace is maintained, the basicity of the slag is controlled to be 2.0-3.0, and argon is blown from the bottom for stirring; controlling the Mn content of the LF end point to be less than 1.00 percent.
6. The method for producing a high-strength high-yield-ratio non-quenched and tempered steel for an automobile engine pop-up connecting rod as claimed in claim 3, wherein the vacuum treatment process is performed for a high vacuum time of 10min or more, and after breaking the air, N-Mn lines and S lines are fed according to the detected components; the soft blowing time is controlled to be more than 15 minutes.
7. The method for producing a high-strength high-yield-ratio non-quenched and tempered steel for an automobile engine pop-up connecting rod as claimed in claim 3, wherein continuous casting employs crystallizer electromagnetic stirring + end detection stirring, and secondary cooling employs a weak cooling manner; and after continuous casting and billet discharging, putting the cast ingot into a pit, covering the cast ingot, and slowly cooling the cast ingot.
8. The method for producing a high-strength high-yield-ratio non-quenched and tempered steel for an automobile engine pop-up connecting rod as claimed in claim 7, wherein the pit entry temperature is not less than 450 ℃.
9. The method for producing a high-strength high-yield-ratio non-quenched and tempered steel for an automobile engine pop-up connecting rod as claimed in claim 3, wherein the initial rolling temperature is controlled to 1080-1180 ℃, the final rolling temperature is controlled to 850-950 ℃, and air cooling is performed after the rolling is completed.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010145323.5A CN111304517B (en) | 2020-03-05 | 2020-03-05 | High-strength high-yield-ratio non-quenched and tempered steel for automobile engine cracking connecting rod and production method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010145323.5A CN111304517B (en) | 2020-03-05 | 2020-03-05 | High-strength high-yield-ratio non-quenched and tempered steel for automobile engine cracking connecting rod and production method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN111304517A true CN111304517A (en) | 2020-06-19 |
| CN111304517B CN111304517B (en) | 2021-04-30 |
Family
ID=71145316
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010145323.5A Active CN111304517B (en) | 2020-03-05 | 2020-03-05 | High-strength high-yield-ratio non-quenched and tempered steel for automobile engine cracking connecting rod and production method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111304517B (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111876682A (en) * | 2020-07-22 | 2020-11-03 | 中国重汽集团济南动力有限公司 | High-strength non-quenched and tempered steel connecting rod for heavy-duty automobile and manufacturing method thereof |
| CN111961988A (en) * | 2020-09-04 | 2020-11-20 | 中天钢铁集团有限公司 | Production process and forging method of medium-carbon non-quenched and tempered steel for automobile expansion fracture connecting rod |
| CN114058943A (en) * | 2021-09-14 | 2022-02-18 | 武汉钢铁有限公司 | Microalloyed steel and manufacturing method thereof |
| CN114592157A (en) * | 2022-03-16 | 2022-06-07 | 宝武杰富意特殊钢有限公司 | Nb-containing non-quenched and tempered steel and preparation method thereof |
| CN114752849A (en) * | 2021-01-12 | 2022-07-15 | 宝山钢铁股份有限公司 | High-strength and high-toughness free-cutting non-quenched and tempered round steel and manufacturing method thereof |
| CN115058655A (en) * | 2022-06-29 | 2022-09-16 | 马鞍山钢铁股份有限公司 | Non-quenched and tempered steel for Nb microalloying medium-carbon expansion-broken connecting rod, expansion-broken connecting rod produced by using non-quenched and tempered steel and forging-controlled cooling process |
| CN115074629A (en) * | 2022-06-29 | 2022-09-20 | 马鞍山钢铁股份有限公司 | Non-quenched and tempered steel for Nb-Ti-V composite reinforced high-carbon expansion-fracture connecting rod, expansion-fracture connecting rod produced from non-quenched and tempered steel and forging and cooling control process |
| CN115125447A (en) * | 2022-06-29 | 2022-09-30 | 马鞍山钢铁股份有限公司 | Non-quenched and tempered steel for Nb-V composite reinforced high-carbon fractured connecting rod, produced fractured connecting rod and forging and cooling control process |
Citations (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004346415A (en) * | 2003-05-26 | 2004-12-09 | Nippon Steel Corp | Ultrahigh-temperature hot-forged non-heat-treated parts and manufacturing method therefor |
| JP2008127595A (en) * | 2006-11-17 | 2008-06-05 | Kobe Steel Ltd | High strength hot forged non-heat treated steel having excellent fatigue limit ratio and toughness |
| JP2008274393A (en) * | 2007-03-30 | 2008-11-13 | Daido Steel Co Ltd | Manufacturing method of high-strength, high-toughness ferrite/pearlite non-heat-treated steel forging part |
| CN102220546A (en) * | 2011-06-30 | 2011-10-19 | 首钢总公司 | B-containing medium-carbon non-quenched and tempered steel and production method thereof |
| CN104254626A (en) * | 2013-04-30 | 2014-12-31 | 新日铁住金株式会社 | Untempered steel material |
| CN104651753A (en) * | 2014-11-28 | 2015-05-27 | 南京钢铁股份有限公司 | Non-quenched and tempered steel for heavy truck balance shaft and manufacturing method thereof |
| CN105463318A (en) * | 2015-11-27 | 2016-04-06 | 北大方正集团有限公司 | Non-quenched and non-tempered steel, production method of non-quenched and non-tempered steel and cracking connecting rod manufactured through non-quenched and non-tempered steel |
| CN107587076A (en) * | 2017-09-19 | 2018-01-16 | 北京科技大学 | The production method of bent axle major diameter ferrite+pearlite type non-hardened and tempered steel bar |
| CN109252097A (en) * | 2018-10-10 | 2019-01-22 | 江阴兴澄特种钢铁有限公司 | A kind of non-hardened and tempered steel and its continuous casting manufacturing technique of high intensity fractured connecting rod |
| CN109666856A (en) * | 2018-12-29 | 2019-04-23 | 江苏利淮钢铁有限公司 | A kind of high-strength tenacity semiaxis non-hardened and tempered steel and its production method instead of 42CrMo quenched and tempered steel |
| CN110184527A (en) * | 2018-05-31 | 2019-08-30 | 江阴兴澄特种钢铁有限公司 | It is a kind of for making the high intensity levels non-hardened and tempered steel bar and its manufacturing method of engine rocker |
| CN110592476A (en) * | 2019-09-16 | 2019-12-20 | 宝鸡新利达汽车零部件有限公司 | Non-quenched and tempered round steel for direct cutting and method for manufacturing truck pin shaft by using same |
| CN110616363A (en) * | 2018-06-20 | 2019-12-27 | 宝山钢铁股份有限公司 | Medium-carbon non-quenched and tempered expansion-fracture connecting rod steel and manufacturing method thereof |
-
2020
- 2020-03-05 CN CN202010145323.5A patent/CN111304517B/en active Active
Patent Citations (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004346415A (en) * | 2003-05-26 | 2004-12-09 | Nippon Steel Corp | Ultrahigh-temperature hot-forged non-heat-treated parts and manufacturing method therefor |
| JP2008127595A (en) * | 2006-11-17 | 2008-06-05 | Kobe Steel Ltd | High strength hot forged non-heat treated steel having excellent fatigue limit ratio and toughness |
| JP2008274393A (en) * | 2007-03-30 | 2008-11-13 | Daido Steel Co Ltd | Manufacturing method of high-strength, high-toughness ferrite/pearlite non-heat-treated steel forging part |
| CN102220546A (en) * | 2011-06-30 | 2011-10-19 | 首钢总公司 | B-containing medium-carbon non-quenched and tempered steel and production method thereof |
| CN104254626A (en) * | 2013-04-30 | 2014-12-31 | 新日铁住金株式会社 | Untempered steel material |
| CN104651753A (en) * | 2014-11-28 | 2015-05-27 | 南京钢铁股份有限公司 | Non-quenched and tempered steel for heavy truck balance shaft and manufacturing method thereof |
| CN105463318A (en) * | 2015-11-27 | 2016-04-06 | 北大方正集团有限公司 | Non-quenched and non-tempered steel, production method of non-quenched and non-tempered steel and cracking connecting rod manufactured through non-quenched and non-tempered steel |
| CN107587076A (en) * | 2017-09-19 | 2018-01-16 | 北京科技大学 | The production method of bent axle major diameter ferrite+pearlite type non-hardened and tempered steel bar |
| CN110184527A (en) * | 2018-05-31 | 2019-08-30 | 江阴兴澄特种钢铁有限公司 | It is a kind of for making the high intensity levels non-hardened and tempered steel bar and its manufacturing method of engine rocker |
| CN110616363A (en) * | 2018-06-20 | 2019-12-27 | 宝山钢铁股份有限公司 | Medium-carbon non-quenched and tempered expansion-fracture connecting rod steel and manufacturing method thereof |
| CN109252097A (en) * | 2018-10-10 | 2019-01-22 | 江阴兴澄特种钢铁有限公司 | A kind of non-hardened and tempered steel and its continuous casting manufacturing technique of high intensity fractured connecting rod |
| CN109666856A (en) * | 2018-12-29 | 2019-04-23 | 江苏利淮钢铁有限公司 | A kind of high-strength tenacity semiaxis non-hardened and tempered steel and its production method instead of 42CrMo quenched and tempered steel |
| CN110592476A (en) * | 2019-09-16 | 2019-12-20 | 宝鸡新利达汽车零部件有限公司 | Non-quenched and tempered round steel for direct cutting and method for manufacturing truck pin shaft by using same |
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111876682A (en) * | 2020-07-22 | 2020-11-03 | 中国重汽集团济南动力有限公司 | High-strength non-quenched and tempered steel connecting rod for heavy-duty automobile and manufacturing method thereof |
| CN111961988A (en) * | 2020-09-04 | 2020-11-20 | 中天钢铁集团有限公司 | Production process and forging method of medium-carbon non-quenched and tempered steel for automobile expansion fracture connecting rod |
| CN111961988B (en) * | 2020-09-04 | 2021-11-02 | 中天钢铁集团有限公司 | Production process and forging method of medium-carbon non-quenched and tempered steel for automobile expansion fracture connecting rod |
| WO2022152158A1 (en) * | 2021-01-12 | 2022-07-21 | 宝山钢铁股份有限公司 | High-strength and toughness free-cutting non-quenched and tempered round steel and manufacturing method therefor |
| CN114752849B (en) * | 2021-01-12 | 2023-09-12 | 宝山钢铁股份有限公司 | High-strength and high-toughness free-cutting non-quenched and tempered round steel and manufacturing method thereof |
| CN114752849A (en) * | 2021-01-12 | 2022-07-15 | 宝山钢铁股份有限公司 | High-strength and high-toughness free-cutting non-quenched and tempered round steel and manufacturing method thereof |
| CN114058943A (en) * | 2021-09-14 | 2022-02-18 | 武汉钢铁有限公司 | Microalloyed steel and manufacturing method thereof |
| CN114592157A (en) * | 2022-03-16 | 2022-06-07 | 宝武杰富意特殊钢有限公司 | Nb-containing non-quenched and tempered steel and preparation method thereof |
| CN115058655A (en) * | 2022-06-29 | 2022-09-16 | 马鞍山钢铁股份有限公司 | Non-quenched and tempered steel for Nb microalloying medium-carbon expansion-broken connecting rod, expansion-broken connecting rod produced by using non-quenched and tempered steel and forging-controlled cooling process |
| CN115074629A (en) * | 2022-06-29 | 2022-09-20 | 马鞍山钢铁股份有限公司 | Non-quenched and tempered steel for Nb-Ti-V composite reinforced high-carbon expansion-fracture connecting rod, expansion-fracture connecting rod produced from non-quenched and tempered steel and forging and cooling control process |
| CN115125447A (en) * | 2022-06-29 | 2022-09-30 | 马鞍山钢铁股份有限公司 | Non-quenched and tempered steel for Nb-V composite reinforced high-carbon fractured connecting rod, produced fractured connecting rod and forging and cooling control process |
| CN115058655B (en) * | 2022-06-29 | 2023-08-11 | 马鞍山钢铁股份有限公司 | Non-quenched and tempered steel for Nb microalloyed medium-carbon expansion-break connecting rod, expansion-break connecting rod produced by non-quenched and tempered steel, and forging and cooling control process of non-quenched and tempered steel |
| CN115074629B (en) * | 2022-06-29 | 2023-08-11 | 马鞍山钢铁股份有限公司 | Non-quenched and tempered steel for Nb-Ti-V composite reinforced high-carbon expansion-break connecting rod, production expansion-break connecting rod thereof and forging and cooling control process |
| CN115125447B (en) * | 2022-06-29 | 2023-08-15 | 马鞍山钢铁股份有限公司 | Non-quenched and tempered steel for Nb-V composite reinforced high-carbon expansion connecting rod, expansion connecting rod produced by non-quenched and tempered steel, and forging and cooling control process |
Also Published As
| Publication number | Publication date |
|---|---|
| CN111304517B (en) | 2021-04-30 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN111304517B (en) | High-strength high-yield-ratio non-quenched and tempered steel for automobile engine cracking connecting rod and production method thereof | |
| CN109234508B (en) | Medium-carbon steel wire rod with high strength and high plasticity and production method thereof | |
| CN109252097B (en) | Non-quenched and tempered steel of high-strength expansion-fracture connecting rod and continuous casting production process thereof | |
| CN108998615B (en) | 600MPa grade ocean engineering structural steel with excellent wear resistance and production method thereof | |
| CN107619995A (en) | A kind of major diameter engineering mechanical hydraulic oil cylinder piston rod round steel and its manufacture method | |
| CN107904492A (en) | A kind of low silicon high-carbon-chromium bearing steel and its hot rolling production method | |
| CN111286670B (en) | Medium-carbon non-quenched and tempered steel and preparation process thereof, and connecting rod and preparation process thereof | |
| CN108950432B (en) | Manufacturing method of high-strength and high-toughness low-alloy wear-resistant steel | |
| CN110846580B (en) | high-Mo high-performance Mn-Cr series steel for wind power output gear and production method thereof | |
| CN113293336A (en) | Preparation method of rare earth non-quenched and tempered free-cutting hot-rolled round steel with yield strength of 500MPa | |
| CN110629114A (en) | Low-cost high-strength high-toughness bridge steel and preparation method thereof | |
| CN109735765B (en) | Large-sized, ultra-fine grain, high-strength and high-toughness spring steel and production method thereof | |
| CN113430458B (en) | Ultrahigh-strength steel plate with yield strength of more than 1040MPa and manufacturing method thereof | |
| CN108677084B (en) | Production method of low-inclusion clean steel | |
| CN114941101B (en) | Steel for bearing shaft of automobile engine and production method thereof | |
| CN111575578B (en) | Hot-rolled chain plate steel strip with excellent wear resistance and manufacturing method thereof | |
| CN111155022B (en) | 390 MPa-grade polar region hull structural steel with low-temperature toughness and preparation method thereof | |
| CN115584441A (en) | Hot-rolled coil for hydrogen transmission pipeline with 245 MPa-level yield strength and production method thereof | |
| JP2006274373A (en) | Steel for high strength screw having excellent toughness and cold workability and method for producing high strength screw | |
| CN112143970B (en) | High-strength high-toughness non-quenched and tempered front axle steel and production method thereof | |
| CN113604745A (en) | High-sulfur free-cutting tool steel bar and preparation method thereof | |
| CN113564460A (en) | Low-cost MnNb series acid-resistant pipeline steel hot-rolled plate coil without Cu, Cr, Ni, Mo and V and manufacturing method thereof | |
| WO2019029533A1 (en) | Cast steel, preparation method for cast steel and use of cast steel | |
| CN115679223B (en) | High-yield-ratio cold-rolled DH980 steel and preparation method thereof | |
| CN115449704B (en) | New energy automobile hub bearing steel and production 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 | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |