CN114134430A - High-hardenability 35SiMnCrMoB steel for wear-resistant parts of engineering machinery and manufacturing method thereof - Google Patents
High-hardenability 35SiMnCrMoB steel for wear-resistant parts of engineering machinery and manufacturing method thereof Download PDFInfo
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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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- C21—METALLURGY OF IRON
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- C21C1/00—Refining of pig-iron; Cast iron
- C21C1/02—Dephosphorising or desulfurising
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- 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
- C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
- C21C5/28—Manufacture of steel in the converter
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- 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
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- 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
- C21C7/064—Dephosphorising; Desulfurising
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- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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Abstract
The invention relates to high-hardenability 35SiCrMnMoB steel for a wear-resistant part of engineering machinery, which comprises the following chemical components in percentage by weight: 0.32 to 0.38%, Si: 1.20 to 1.50%, Mn: 1.20-1.40%, Cr: 1.00-1.30%, Ti: 0.020-0.050%, B: 0.0010-0.0040%, Mo: 0.20-0.30 percent of Fe, less than or equal to 0.010 percent of S, less than or equal to 0.025 percent of P, less than or equal to 0.20 percent of Cu, less than or equal to 0.020 percent of Al, less than or equal to 0.0060 percent of N, and the balance of Fe and inevitable impurities. The invention discloses a high-hardenability hot-rolled round steel for manufacturing engineering machinery wear-resistant parts subjected to quenching and low-temperature tempering treatment and a manufacturing method thereof, wherein the hardenability of the steel meets the requirement that J25 is more than or equal to 48 HRC. The high silicon design can obviously improve the hardness of the quenched and tempered surface of steel and improve the wear resistance while ensuring the improvement of hardenability.
Description
Technical Field
The invention belongs to the technical field of special steel smelting, and particularly relates to a high-hardenability 35SiMnCrMoB steel for an engineering machinery wear-resistant part and a manufacturing method thereof.
Background
Wear-resistant parts such as excavator teeth and drill rods in engineering machinery are usually made of hot-rolled round steel through forging, and are usually mainly made of common alloy structural steel and carbon steel. In order to meet the severe environment and heavy load in the use of large-scale engineering machinery, the strength of the steel is further improved by adding V, Ti, Nb and the like on the basis of the existing carbon steel or bonding steel, and in recent years, the hardenability is greatly improved by utilizing B, the performance is improved, the cost is greatly reduced, and a large amount of steel containing B is developed.
Patent No. CN201210087346.0 discloses a high-strength wear-resistant steel for engineering machinery and a preparation method thereof. The steel comprises the following components in parts by weight: c: 0.15 to 0.30%, Si: 0.20 to 0.65%, Mn: 1.20-1.60%, S is less than or equal to 0.010%, P is less than or equal to 0.020%, B: 0.0010-0.0040%, Cr: 0.30-1.00%, V: 0.030-0.080%, Al: 0.015 to 0.050%, [ N ]]：80～200×10-6、[H]≤2×10-6、[O]≤40×10-6The balance being Fe and inevitable impurities. The steel can be used for manufacturing mechanical products in the industries of engineering, mining, construction, agriculture, cement production, ports, electric power, metallurgy and the like which require high strength and high wear resistance. But because of this patentThe steel has low contents of C, Si and Cr and low hardenability, and is not enough to meet the requirements of large-specification wear-resistant parts.
Compared with 42CrMo (V) and 40CrNiMo steels which are commonly used for engineering machinery wear-resistant parts, the carbon SiMnCrMoB steel disclosed by the invention has the advantages that the content of Ni and V is eliminated by adding a proper amount of B, the production cost is reduced, the content of Si in the steel is increased to increase the wear-resistant performance of the steel, and the hardenability is further improved, so that the high hardness requirement of the steel for large-specification wear-resistant parts of engineering machinery can be met.
Disclosure of Invention
The invention aims to solve the technical problem of providing the high-hardenability 35SiMnCrMoB steel for the wear-resistant part of the engineering machinery and the manufacturing method thereof, which aim at the prior art, through adding a proper amount of B, the contents of Ni and V are eliminated, the production cost is reduced, the Si content in the steel is improved to increase the wear-resistant performance of the steel, and the hardenability is further improved, so that the high-hardenability requirement of the steel for the wear-resistant part with larger specification of the engineering machinery can be met.
The technical scheme adopted by the invention for solving the problems is as follows: the high-hardenability 35SiMnCrMoB steel for the wear-resistant part of the engineering machinery comprises the following chemical components in percentage by weight: 0.32 to 0.38%, Si: 1.20 to 1.50%, Mn: 1.20-1.40%, Cr: 1.00-1.30%, Ti: 0.020-0.050%, B: 0.0010-0.0040%, Mo: 0.20-0.30 percent of Fe, less than or equal to 0.010 percent of S, less than or equal to 0.025 percent of P, less than or equal to 0.20 percent of Cu, less than or equal to 0.020 percent of Al, and the balance of Fe and inevitable impurities.
The main functions and design basis corresponding to each element of the steel chemical composition are as follows:
c is the most basic element in steel and is also the most economic strengthening element. In order to ensure that the wear-resistant part produced by the steel has higher surface hardness after quenching and tempering and also has good obdurability, the carbon content range of the steel is determined.
Si is one of the most critical elements of the present invention. Si can be used as a deoxidizing element in steel, has a strong solid solution strengthening effect in the steel, can obviously improve the ferrite strength, and can improve the quenching and tempering surface hardness of the steel, thereby improving the wear resistance of the gear. Silicon is a relatively cheap alloy element, and the high-silicon design can properly reduce the addition of other alloy elements, thereby being beneficial to reducing the production cost of materials. The steel material of the invention adopts high silicon design, so the Si content is set to be 1.20-1.50%.
Mn plays a role in solid solution strengthening on steel, and the steel content range is determined by utilizing the characteristics that Mn strongly improves the hardenability of the steel and has low cost.
Cr plays a role in solid solution strengthening on steel, increases hardenability, refines the lamellar spacing of pearlite, and is beneficial to improving the formation proportion of a fine lamellar pearlite structure and the uniformity of a microstructure, so that the strength of the material is effectively improved. The steel content range is determined by using the principle that Cr is matched with Mo to improve the hardenability of the steel and considering the cost.
Mo is a carbide forming element, and can improve the hardenability of the steel, refine crystal grains and improve toughness.
B is a surface active element, boron which is dissolved in austenite in a solid state is adsorbed on a grain boundary to reduce the grain boundary energy, inhibit the proeutectoid ferrite and pearlite nucleation rate, slow down the decomposition of undercooled austenite, delay the transformation of ferrite and improve the hardenability of steel. The hardenability of the steel can be remarkably improved by 1.2 to 2.2 times by adding a trace amount of B (0.0005 to 0.005%) into the steel. According to the existing research results, part of precious alloy elements can be replaced. In order to ensure that the steel has enough effective B, the content of B is controlled to be 0.0010-0.0040 percent in the design of the invention
Ti is both a strong carbide former and a strong nitride former. Ti in the steel is combined with C and N to form TiN or Ti (C, N) particles, and the grain growth can be effectively prevented by pinning the grain boundary, so that the effect of refining the grains is achieved. In the present invention, Ti must be combined with N in the steel to form TiN and play a role of fixing N and keeping B, so that the present invention considers the consumption of Ti by N, O content in the steel and controls the Ti content in the steel to be in the range of 0.020-0.050%.
Generally, P, S is an impurity element and a harmful element, is harmful to the mechanical property and the hot workability of steel, is easy to form defects such as segregation and inclusion, and causes the obvious reduction of plasticity and impact toughness; the content thereof should be minimized. Considering the cost factors of reducing the P content and the S content, the invention controls the P content to be less than or equal to 0.025 percent and the S content to be less than or equal to 0.020 percent.
Al is an element which is very effective in deoxidation, and the main role of Al in the present invention is deoxidation. The reason why Al is controlled to be 0.020% or less is that the Al content is too high and a large amount of brittle inclusions (for example, Al) are formed in the steel2O3Etc.) contamination of molten steel, resulting in a decrease in toughness; in addition, the steel grade of the invention contains high si, and the high content of Al in the steel causes a tendency to graphitize, resulting in deterioration of hot workability of the steel.
The method for manufacturing the high hardenability 35SiMnCrMoB steel for the wear-resistant part of the engineering machinery adopts an electric furnace or a converter for smelting, and then the high hardenability 35SiMnCrMoB steel is subjected to external refining and vacuum degassing treatment, then is poured into a continuous casting billet, and is rolled into a finished product steel after being heated.
Further, the specific production flow of the steel of the invention is as follows: 100t converter-external refining-RH vacuum degassing-390X 510mm continuous casting billet-casting billet reheating rolling into a finished product.
Compared with the prior art, the invention has the advantages that:
the steel type of the invention is different from the CrMo (V) used for the conventional engineering machinery wear-resistant part steel or CrNiMo steel which contains high content of Cr and Mo and contains the noble element V, Ni, the technical means that the B element can strongly improve the hardenability is fully utilized by canceling the noble alloy element V, Ni and adding the B element, the hardenability requirement of the steel used for the large-size wear-resistant part of the engineering machinery is met by improving Si in the steel and combining the influence effect of Mn, Cr and Mo on different depths of the hardenability of the steel, and the hardenability depth of the steel is further improved after the B is added, and meanwhile, the Si content in the steel is improved, so that the part has higher wear resistance, and the steel has higher market competitiveness and popularization value.
The control point in the steel manufacturing method is different from the conventional production process. The content of [ S ] in steel is greatly reduced through KR pretreatment of molten iron, the desulfurization pressure of a converter and a refining furnace is reduced, the [ C ] of a tapping control terminal point of the converter is more than or equal to 0.15 percent, the original [ O ] content in the molten steel can be effectively reduced, the deoxidation and desulfurization effects under the condition of low aluminum of an LF refining process are improved, RH vacuum treatment is different from degassing treatment under high vacuum degree, and is carried out for 8-10 minutes by adopting 133-Pa with moderate vacuum degree, the process cost is reduced while molten steel degassing is ensured, soft argon blowing is kept for more than 10 minutes after vacuum treatment, FeTi line is fed and FeB is fed 5 minutes before a ladle is put on a continuous casting platform, which is different from the conventional process of feeding FeTi line and feeding FeB for fixing N and protecting B before soft argon blowing after degassing, thereby improving the recovery rate of Ti and B and reducing the roller cooling water amount in the rolling process of the internal stress of the rolled piece by 50 percent of that in the rolling of the conventional steel grade.
Detailed Description
The technical solutions of the present invention will be described in more detail with reference to preferred embodiments of the present invention. However, these examples are merely illustrative of the preferred embodiments of the present invention and should not be construed as limiting the scope of the present invention in any way.
Preparing smelting raw materials according to the chemical element composition of the steel, and sequentially adding molten iron pretreated by KR and preferable scrap steel → 100t converter primary smelting → LF furnace refining → RH vacuum degassing → continuous casting 390X510mm continuous casting blank → casting blank high-temperature hot charging or slow cooling after cold charging → casting blank heating → high-pressure water descaling → rolling → bar high-temperature offline slow cooling → finishing and detection-warehousing.
Pretreatment of molten iron
Adding a desulfurizing agent after the ladle is in place, stirring strongly for 10-20 minutes, and treating the [ S ] in the molten iron to be below 0.020%;
smelting in a converter
1) The molten iron in the raw materials fed into the furnace accounts for 90 percent, and the balance is selected high-quality scrap steel;
2) the key point control of the converter smelting and tapping process is as follows: controlling the end point tapping carbon of the converter, wherein the end point of [ C ] is not less than 0.15%, and the content of [ P ] is not more than 0.015%; the steel ladle is partially alloyed, slag-making materials such as synthetic slag and other deoxidizing agents are quantitatively added, and a slag retaining ball is used in the later tapping period to prevent oxidizing slag from falling.
Refining in LF furnace
1) Adding 100-300kg of lime into the LF furnace after the LF furnace is powered on for 10 minutes, adding SiC powder on the surface of the refined slag to perform diffusion deoxidation, and feeding a proper amount of Al wire to enhance precipitation deoxidation of the molten steel, so as to ensure the desulfurization effect to produce high-alkalinity slag (the binary alkalinity is controlled to be 5-7 through calculation of the lime adding amount), and simultaneously, the slag is required to be kept to have good fluidity;
2) refining and taking a 1 st chemical component sample, adjusting si, Cr, Mn and Mo to an internal control lower limit, analyzing a 2 nd sample, finely adjusting all components to enter a target value, and tapping at least 5 minutes after the temperature is qualified; controlling the time to be not less than 40 minutes according to the LF refining time.
RH vacuum degassing and soft argon blowing
1) Controlling the low vacuum degree to be kept for 8-10 minutes under the pressure of 133-660 Pa;
2) and (4) sampling and analyzing after the vacuum is relieved, and hoisting the ladle to the argon blowing position to continue the soft argon blowing for more than or equal to 10 minutes.
3) And (3) calculating the addition amount of FeTi according to the ratio of [ Al ]/[ N ]/[ Ti ] being more than or equal to 2: 1: 4 5 minutes before hoisting the ladle to the continuous casting platform, and adding FeB to adjust [ B ] to the target content.
Continuous Casting
1) Protecting the casting in the whole continuous casting process, and setting the electromagnetic stirring parameters of a crystallizer and a secondary cooling section;
2) the superheat degree target of the continuous casting molten steel is controlled to be 10-25 ℃, the superheat degree of a first furnace is allowed to be 10 ℃ higher than that of a continuous casting furnace, and the pulling speed is controlled to be 0.35-0.55 m/min;
3) the continuous casting blank is hot-fed into a steel rolling heating furnace at the temperature of more than 550 ℃ (if the hot-charging temperature cannot be guaranteed, the continuous casting blank needs to be put into a heat preservation pit in time for slow cooling for more than 24 hours) so as to avoid the generation of reticular cracks on the surface of the casting blank.
Rolling of
1) Heating the continuous casting billet in a heating furnace in a low-oxidizing atmosphere, controlling the temperature of a preheating section at 870 ℃, controlling the heating time of the preheating section to be not less than 1.5 hours, controlling the temperatures of a heating section and a soaking section at 1050-1200 ℃, and preserving heat for 3-4 hours;
2) the initial rolling temperature is 1000-.
3) The steel cooling process comprises the following steps: after the rolling of the steel is finished, the steel is rapidly cooled down on a cooling bed and enters a pit at the temperature of above 650 ℃ for slow cooling to below 200 ℃.
The chemical composition (wt%) of each example of the present invention is shown in table 1.
TABLE 1
| Steel grade | C | Si | Mn | P | S | Cr | Mo | Ti | B | Al | Cu | N |
| Example 1 | 0.35 | 1.30 | 1.31 | 0.015 | 0.002 | 1.22 | 0.24 | 0.035 | 0.0030 | 0.012 | 0.01 | 0.003 |
| Example 2 | 0.33 | 1.45 | 1.38 | 0.012 | 0.001 | 1.25 | 0.27 | 0.035 | 0.0035 | 0.008 | 0.02 | 0.0035 |
| Example 3 | 0.37 | 1.40 | 1.26 | 0.011 | 0.002 | 1.18 | 0.22 | 0.028 | 0.0018 | 0.011 | 0.01 | 0.0028 |
| Example 4 | 0.36 | 1.46 | 1.37 | 0.007 | 0.003 | 1.08 | 0.26 | 0.030 | 0.0027 | 0.015 | 0.01 | 0.0030 |
The results of the hardenability test of the steel materials of the examples are shown in Table 2.
TABLE 2
| Steel grade | Rolled stock specification, mm | J25，HRC | Quenching temperature of DEG C |
| Example 1 | φ150 | 52.5 | 850 |
| Example 2 | φ180 | 50.0 | 850 |
| Examples3 | φ200 | 54.5 | 850 |
| Example 4 | φ195 | 53.5 | 850 |
In addition to the above embodiments, the present invention also includes other embodiments, and any technical solutions formed by equivalent transformation or equivalent replacement should fall within the scope of the claims of the present invention.
Claims (7)
1. The utility model provides a high hardenability 35SiCrMnMoB steel for engineering machine tool wear-resisting part which characterized in that: the steel comprises the following chemical components in percentage by weight: 0.32 to 0.38%, Si: 1.20 to 1.50%, Mn: 1.20-1.40%, Cr: 1.00-1.30%, Ti: 0.020-0.050%, B: 0.0010-0.0040%, Mo: 0.20-0.30 percent of Fe, less than or equal to 0.010 percent of S, less than or equal to 0.025 percent of P, less than or equal to 0.20 percent of Cu, less than or equal to 0.020 percent of Al, and the balance of Fe and inevitable impurities.
2. The high hardenability 35SiCrMnMoB steel for a wear-resistant part of an engineering machine according to claim 1, wherein: the hardenability of the steel meets that J25 is more than or equal to 48 HRC.
3. A method for manufacturing the high hardenability 35SiCrMnMoB steel for a wear-resistant part for construction machinery according to claim 1, characterized in that: the whole manufacturing method is that smelting raw materials are prepared according to the chemical element composition of the steel, molten iron and optimized scrap steel which are pretreated by KR are sequentially added → 100t converter primary smelting → LF furnace refining → RH vacuum degassing → continuous casting 390X510mm continuous casting blank → casting blank is hot-charged at high temperature or cold-charged after slow cooling → casting blank heating → high-pressure water descaling → rolling → bar high-temperature off-line slow cooling → finishing and detection-warehousing.
4. The method for manufacturing a high hardenability 35SiCrMnMoB steel for a wear-resistant part of construction machinery according to claim 3, wherein the method comprises the steps of: the method specifically comprises the following steps:
first, converter smelting
1) The molten iron in the raw materials fed into the furnace accounts for 90 percent, and the balance is selected high-quality scrap steel;
2) the key point control of the converter smelting and tapping process is as follows: controlling the end point tapping carbon of the converter, wherein the end point of [ C ] is not less than 0.15%, and the content of [ P ] is not more than 0.015%; partially alloying the steel ladle, quantitatively adding slag-making materials such as synthetic slag and other deoxidizing agents, and using slag retaining balls to prevent oxidizing slag from falling in the later tapping period;
refining in LF furnace
1) Adding 100-300kg of lime after the LF furnace is powered on for 10 minutes, adding SiC powder on the surface of the refined slag for diffusion deoxidation, and feeding a proper amount of Al wire to enhance the precipitation deoxidation of the molten steel;
2) refining and taking a 1 st chemical component sample, adjusting Si, Cr, Mn and Mo to an internal control lower limit, analyzing a 2 nd sample, finely adjusting all components to enter a target value, and tapping at least 5 minutes after the temperature is qualified; controlling the refining time to be not less than 40 minutes according to the LF refining time;
third, RH vacuum degassing and soft argon blowing
1) Controlling the low vacuum degree to be kept for 8-10 minutes under the pressure of 133-660 Pa;
2) sampling and analyzing after the vacuum is relieved, and hoisting the ladle to an argon blowing position to continue to blow the argon for more than or equal to 10 minutes;
fourthly, continuous casting
1) Protecting the casting in the whole continuous casting process, and setting the electromagnetic stirring parameters of a crystallizer and a secondary cooling section;
2) the superheat degree target of the continuous casting molten steel is controlled to be 10-25 ℃, the superheat degree of a first furnace is allowed to be 10 ℃ higher than that of a continuous casting furnace, and the pulling speed is controlled to be 0.35-0.55 m/min;
fifth, rolling
1) Heating the continuous casting billet in a heating furnace in a low-oxidizing atmosphere, controlling the temperature of a preheating section at 870 ℃, controlling the heating time of the preheating section to be not less than 1.5 hours, controlling the temperatures of a heating section and a soaking section at 1050-1200 ℃, and preserving heat for 3-4 hours;
2) the initial rolling temperature is 1000-;
3) the steel cooling process comprises the following steps: after the rolling of the steel is finished, the steel is rapidly cooled down on a cooling bed and enters a pit at the temperature of above 650 ℃ for slow cooling to below 200 ℃.
5. The method for manufacturing a high hardenability 35SiCrMnMoB steel for a wear-resistant part of construction machinery as claimed in claim 4, wherein: in order to ensure the desulfurization effect of the high-alkalinity slag during LF furnace refining, the binary alkalinity is controlled to be 5-7 through the calculation of the amount of added lime, and meanwhile, the good fluidity of the slag is maintained.
6. The method for manufacturing a high hardenability 35SiCrMnMoB steel for a wear-resistant part of construction machinery as claimed in claim 4, wherein: after finishing RH vacuum degassing and soft argon blowing, calculating the FeTi adding amount according to the ratio of (Al)/(N)/(Ti) being more than or equal to 2: 1: 4 for 5 minutes before hanging and covering on a continuous casting platform, and adding FeB to adjust (B) to the target content.
7. The method for manufacturing a high hardenability 35SiCrMnMoB steel for a wear-resistant part of construction machinery as claimed in claim 4, wherein: when the continuous casting is finished, the continuous casting blank is hot-fed to a steel rolling heating furnace at the temperature of more than 550 ℃, if the hot-charging temperature cannot be guaranteed, a heat preservation pit needs to be put in time for slow cooling for more than 24 hours, so that the generation of reticular cracks on the surface of the casting blank is avoided.
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| CN115323263A (en) * | 2022-06-30 | 2022-11-11 | 江阴兴澄特种钢铁有限公司 | Wear-resistant high-hardenability pinion steel for rear axle reduction gearbox of truck and manufacturing method |
| CN115369334A (en) * | 2022-08-18 | 2022-11-22 | 中天钢铁集团有限公司 | Production method of steel AISI8740H for cutting pick of engineering machinery |
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| CN114959415A (en) * | 2022-05-08 | 2022-08-30 | 江阴兴澄特种钢铁有限公司 | Manufacturing method of microalloyed wind power transmission gear steel |
| CN115323263A (en) * | 2022-06-30 | 2022-11-11 | 江阴兴澄特种钢铁有限公司 | Wear-resistant high-hardenability pinion steel for rear axle reduction gearbox of truck and manufacturing method |
| CN115323263B (en) * | 2022-06-30 | 2024-05-17 | 江阴兴澄特种钢铁有限公司 | Wear-resistant high-hardenability gear steel for rear axle reduction gearbox of truck and manufacturing method |
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| CN115896631A (en) * | 2022-12-09 | 2023-04-04 | 鞍钢矿山机械制造有限公司 | Round steel for rolling ball and ball rolling preparation method |
| CN115896631B (en) * | 2022-12-09 | 2024-04-05 | 鞍钢矿山机械制造有限公司 | Round steel for rolling balls and rolling ball preparation method |
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