WO2017120987A1 - 用于制造轴承的钢材、对其进行热处理的方法和成型件 - Google Patents

用于制造轴承的钢材、对其进行热处理的方法和成型件 Download PDF

Info

Publication number
WO2017120987A1
WO2017120987A1 PCT/CN2016/072301 CN2016072301W WO2017120987A1 WO 2017120987 A1 WO2017120987 A1 WO 2017120987A1 CN 2016072301 W CN2016072301 W CN 2016072301W WO 2017120987 A1 WO2017120987 A1 WO 2017120987A1
Authority
WO
WIPO (PCT)
Prior art keywords
steel
bearing
steel material
less
transformation
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.)
Ceased
Application number
PCT/CN2016/072301
Other languages
English (en)
French (fr)
Inventor
易红亮
庞佳琛
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Northeastern University China
Original Assignee
Northeastern University China
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Northeastern University China filed Critical Northeastern University China
Publication of WO2017120987A1 publication Critical patent/WO2017120987A1/zh
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/30—Parts of ball or roller bearings
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/30—Parts of ball or roller bearings
    • F16C33/58—Raceways; Race rings
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to the field of metal materials, in particular to a steel material.
  • the invention also relates to a method of heat treating such a steel material.
  • the invention also relates to a molded part.
  • the function of the bearing is to support the mechanical rotating body, reduce the friction coefficient during its movement, and ensure its rotation accuracy.
  • bearings that can withstand high speed, high load, high temperature, low temperature and low noise are often needed. This requires bearing steels with high dimensional stability, high hardness, high strength, excellent rolling contact fatigue properties, and wear resistance.
  • GCr15 bearing steel is a commonly used high hardness bearing steel having a carbon content of between 0.95% and 1.05% by weight. After quenching heat treatment, the quenched hardness of GCr15 bearing steel ranges from 61 HRC to 64 HRC. Hardness values after tempering range from 58 HRC to 62 HRC.
  • GCr15 bearing steel In the preparation process of GCr15 bearing steel, after quenching martensite transformation, tempering is carried out to decompose the retained austenite as much as possible, in order to avoid martensite transformation of retained austenite under external force. As a result, the bearing size changes. Thus, typically at room temperature, GCr15 bearing steel contains less than 3% by volume of retained austenite. Such a small amount of retained austenite makes the bearing susceptible to cracks when subjected to a large external force, and even directly causes bearing damage. This severely limits the range of use of bearings made from GCr15 bearing steel.
  • the present invention proposes a steel material for manufacturing a bearing.
  • This steel contains more Carbon and aluminum.
  • the molded part or bearing obtained by using this steel material and passing through the heat treatment method of the present invention contains more martensite and more retained austenite, which gives the molded part or bearing a high hardness.
  • most of these retained austenites do not undergo martensitic transformation under the action of external forces, thereby ensuring that the dimensions of the molded part or bearing are constant, and these retained austenite can effectively inhibit the component or The bearing is cracked or cracked due to external force.
  • a steel material for manufacturing a bearing comprises 1.22-1.6% C, 0.5-2% Cr, 4-8% Al, 0.11-1.5% Mn, and 0.7 weight or less of Si, and the balance is Fe and impurities. .
  • the bearing for manufacturing a bearing of the present invention contains 4-8% aluminum, which increases the carbon content to 1.22-1.6%, but there is still no reticulated carbide inside the steel, and the steel structure is relatively uniform. During the subsequent heat treatment, the good texture distribution of the steel is inherited, resulting in a very uniform microstructure and properties of the heat-treated molded part.
  • the aluminum in the steel increases the martensitic transformation temperature of the steel, which counteracts the decrease in the martensitic transformation temperature caused by the higher carbon content of the steel.
  • the steel of the present invention still has more martensite after heat treatment, which makes the bearing prepared from the steel of the present invention have a very high hardness.
  • the Mars body contains more carbon and will also result in a very high hardness of the bearings produced.
  • the final molded part prepared from the steel of the present invention contains more retained austenite than the prior art GCr15 bearing steel and other types of bearing steel. These retained austenites inhibit cracking and expansion of the brittle martensite (or molded part) when the molded part is subjected to an external force.
  • the retained austenite may have a carbon content of from 2% to 5% by weight. Residual austenite of the final molded part prepared from the steel of the present invention compared to prior art GCr15 bearing steels and other types of bearing steels (the bearing steels having a carbon content of at most 1.9% by weight) The carbon content will be higher, making it very stable and will not undergo martensitic transformation.
  • the stable retained austenite hardly undergoes martensite transformation during use, so the dimensional change of the molded part or bearing under the force condition is not Often small.
  • the retained austenite contains more carbon and also inhibits austenite decomposition, which also results in a larger amount of retained austenite in the final shaped part prepared from the steel of the present invention.
  • a conventional GCr15 bearing steel has a density of about 7.86 g/cm 3
  • a steel material of the present invention, Fe-1.25C-1.5Cr-5Al that is, a C content of about 1.25% by weight, and a Cr content of The density of about 1.5%, the Al content of about 5%, and the balance of Fe and impurities
  • Fe-1.25C-1.5Cr-5Al that is, a C content of about 1.25% by weight, and a Cr content of The density of about 1.5%, the Al content of about 5%, and the balance of Fe and impurities
  • steel material used to make the bearing of the present invention may be ingot, bar, wire, tube or any other suitable shape.
  • the steel further includes at least one of the group consisting of: 1.0% or less by weight of Mo; 1.0% or less of W; 0.05% or less of Ti; and 0.2% or less of Nb. 0.2% or less of Zr; 0.2% or less of V; 2.0% or less of Cu; and 4.0% or less of Ni.
  • a method of heat-treating the above-described steel material for manufacturing a bearing comprises the following steps: step 1: martensitic transformation of the steel; step 2: bain transformation of the steel after martensitic transformation; and step 3: cooling to room temperature.
  • the heat treatment method of the present invention it is not necessary to completely remove the retained austenite, but a part of the retained austenite is retained.
  • a bainite transformation that is, a low-temperature heat treatment for reheating after martensitic transformation
  • a bainite transformation that is, a low-temperature heat treatment for reheating after martensitic transformation
  • Al also inhibits the conversion of carbon into carbides, but causes excess carbon generated during the bainite transformation to enter the retained austenite. Al also causes excess carbon in the martensite to enter the retained austenite. This increases the carbon content of the retained austenite, which inhibits the austenite from undergoing a bainite transformation, so that a greater amount of retained austenite is present in the final shaped part prepared from the steel of the invention.
  • Bainite grows on the retained austenite, which cuts the retained austenite into a very fine residual austenite structure, which also helps to improve the stability of the retained austenite.
  • the stability of this high-carbon and fine retained austenite is very good, even under the action of external forces, the high-carbon retained austenite Martensite transformation does not occur.
  • the high toughness of austenite in the steel inhibits the crack propagation of the molded part when subjected to an external force.
  • the martensite transformation in the first step, is heated at a temperature of from 800 ° C to 950 ° C for a period of from 10 minutes to 300 minutes.
  • the cooling step of the martensitic transformation in step one, is a temperature cooled between room temperature and minus 196 ° C, and the cooling time is from 0.5 minutes to 300 minutes.
  • room temperature is understood to mean a temperature between 18 ° C and 27 ° C, preferably between 20 ° C and 25 ° C.
  • the bainite transformation is heated at a temperature of from 150 ° C to 250 ° C for a period of from 6 hours to 240 hours, preferably from 6 hours to 140 hours.
  • the retained austenite in the steel has a large thermodynamic driving force for the bainite transformation.
  • the atomic diffusion rate is very slow, which makes the bainite transformation practically difficult to occur.
  • the heating temperature of 150 ° C to 250 ° C causes the atomic diffusion rate to be greatly increased, so that the retained austenite can smoothly undergo bainite transformation.
  • the bainite transformation has a holding time of 6 hours to 240 hours, which contributes to the full bainite transformation to increase the carbon content in the retained austenite.
  • the holding time is less than 6 hours, the bainite transformation is not sufficiently ensured, and the carbon content in the retained austenite is not satisfactory.
  • the cooling step of the martensitic transformation may be performed using ice water mixture cooling, liquid nitrogen cooling, or any other suitable cooling means.
  • a protective gas is used to prevent oxidation of the steel during heating and holding of the steel.
  • the shielding gas is an inert gas or nitrogen.
  • a molded article obtained by heat-treating a steel material for manufacturing a bearing described above by heat-treating the steel material as described above.
  • the microstructure of the molded part in terms of volume content includes: 4% to 10% of retained austenite, 80% to 90% of martensite, and 5% or less of carbide, the balance being bainite and impurities. As described above, a certain amount of retained austenite contributes to suppressing crack propagation of the molded article.
  • the retained austenite comprises from 2% to 5.5% carbon by weight.
  • the retained austenite has such a high carbon content that it contributes to the stability of retained austenite and prevents martensite transformation.
  • the retained austenite has a size of from 10 nanometers to 500 nanometers, more preferably from 10 nanometers to 50 nanometers.
  • the morphology of the retained austenite is generally membranous. This also helps to improve the molded part Mechanical properties.
  • the molded part has a hardness between 64 HRC and 69 HRC and a plane fracture toughness between 16 MPa.m 1/2 and 28 MPa.m 1/2 .
  • the plane fracture toughness is used to characterize the ability of the molded part to resist crack propagation and fracture under the action of external force and to absorb deformation energy. The higher the plane fracture toughness, the better the ability of the molded part to hinder crack propagation.
  • the molded part is any one or more of the group consisting of a ferrule of the bearing, an outer ring, an inner ring, a rolling body, and a cage.
  • An advantage of the present invention over the prior art is that the steel of the present invention contains more carbon and aluminum.
  • the molded part prepared by using the steel of the present invention contains more martensite and more retained austenite, and the retained austenite is also very stable, so that the molded part has a very high hardness and is also subjected to an external impact. No cracks will occur.
  • Figure 1 is a photomicrograph of a sample 1-1 according to the present invention.
  • Figure 2 is a photomicrograph of a sample 2-1 according to the present invention.
  • Figure 3 is a photomicrograph of a sample 3-1 according to the present invention.
  • Figure 4 is a photomicrograph of a sample 4-1 according to the present invention.
  • Figure 5 is a photograph of the microstructure of Sample 5-1 according to the present invention.
  • Carbon is the cheapest strengthening element, which can increase the hardness of steel by means of interstitial solid solution and dispersion strengthening.
  • the carbon content is less than 1.22%, in the austenitizing process, after the cementite is completely dissolved, some ferrite remains after the austenite, which lowers the hardness of the steel and deteriorates the toughness of the steel; The carbon content is not conducive to increasing the hardness of martensite.
  • the carbon content is higher than 1.6%, carbon tends to increase the tendency to form reticulated carbides, and the steel and the bearings made of the steel deteriorate the bearing performance due to tissue inhomogeneity caused by tissue inheritance. Therefore, the carbon content ranges from 1.22-1.6%. In this range, in the austenitizing process There is no ferrite remaining, and the carbides can only be dispersed, rather than forming network carbides. This dispersed carbide can effectively increase the hardness and strength of the steel.
  • Aluminum is an important element in the steel of the present invention.
  • Aluminum is a lightweight element with a very low density, close to 1/3 of iron. Therefore, by using aluminum to replace iron, the density of the steel can be reduced, thereby achieving the purpose of reducing the weight.
  • increasing the carbon content in martensite is the most economical and practical method to increase the hardness of steel, but the increase in carbon content leads to a decrease in the martensitic transformation temperature, thereby reducing the martensite volume fraction obtained by quenching heat treatment. Further, the hardness of the material is lowered, so simply increasing the carbon content does not increase the hardness of the bearing steel.
  • aluminum increases the martensitic transformation temperature point, so that the addition of aluminum ensures that the martensite transformation temperature of the steel remains substantially unchanged, thereby increasing the content of martensite. It does not decrease, so that the steel of the present invention can be ensured to have a high hardness after heat treatment.
  • the low-temperature heat treatment process i.e., the bainite transformation process of the present invention
  • aluminum can inhibit the conversion of carbon into cementite or carbide.
  • carbon is enriched in austenite during the bainite transformation, so that the carbon content in the retained austenite is greatly increased.
  • the high carbon content of austenite in turn inhibits the austenite-forming bainite transformation.
  • Al allows the steel of the present invention to be made into a product containing a relatively large amount of retained austenite and a high retained carbon content of retained austenite.
  • ultra-fine retained austenite structure can be obtained by bainite transformation, and the addition of aluminum can also increase the bainite transformation speed, which is beneficial to shorten the time of bainite transformation. If the aluminum content is too low, the above effects cannot be sufficiently achieved, so the lower limit of aluminum is 4%. More than 8% of aluminum forms brittle Fe-Al alloy compounds in steel, which deteriorates material properties. Therefore, the upper limit of aluminum is 8%.
  • Chromium improves hardenability and corrosion resistance and is an important alloying element of the steel of the present invention. Chromium improves the hardenability of steel. Chromium can form high-hardness chromium carbides in bearing steel or form chrome-rich cementite to improve the properties of carbides in bearing steels, improve the hardness and rolling contact fatigue properties of bearing steels. Too low a chromium content does not initiate sufficient of the above effects, so the lower limit of the chromium content is 0.5%.
  • chromium content will reduce the eutectoid carbon content of steel and increase the tendency to form reticulated carbides; excessive chromium content will lower the martensitic transformation temperature and lower the martensite fraction, while lowering the martensite content and lowering martensite Hardness, thus resulting in a decrease in the hardness of the steel.
  • too high a chromium content will significantly increase the brittle transition temperature of the steel. Therefore, the upper limit of the chromium content is 2%.
  • Manganese can improve the hardenability of steel. However, manganese reduces the eutectoid carbon content of steel and increases the tendency to form reticulated carbides; high manganese content lowers martensitic transformation temperature and lowers martensite fraction, while lowering martensite The content lowers the martensite hardness, thus causing a decrease in the hardness of the steel. In addition, too high a manganese content will significantly increase the brittle transition temperature of the steel, and the heat sensitivity of the steel and the tendency to form cracks will also increase. In the steelmaking process, the molten steel contains a certain amount of manganese, so the content of manganese is limited to 0.1-1.5%.
  • silicon increases the heat sensitivity, cracking and decarburization tendency of the steel.
  • the molten steel in the steel making process contains Si, and controlling the Si content to a lower level leads to an increase in cost. Therefore, the content of silicon is controlled to be less than or equal to 0.7%.
  • Mo and W improve the hardenability of steel, which can effectively increase the strength of steel, and is also a carbide forming element, which contributes to the formation of high hardness carbides and improves the hardness of steel.
  • the content is more than 1.0%, the hardness of the steel cannot be further increased, and the cost is increased.
  • Ti, Nb, Zr and V can refine the grain of the steel and increase the strength. Too low a content of Ti, Nb, Zr, and V does not function, and more than 0.2% increases unnecessary cost.
  • Cu can increase strength, especially atmospheric corrosion. However, if the content of Cu is more than 2.0%, the workability may be deteriorated, for example, the hot rolling process may form a liquid phase to cause cracking, and may also cause unnecessary cost increase. Ni can increase the strength of steel and maintain good plasticity and toughness. If the concentration of Ni is more than 4.0%, there is an increase in cost.
  • Table 1 shows the composition of some steels according to the invention, with the balance being iron and impurities.
  • the eutectoid carbon content of the steel is also listed in Table 1. Further, the sample 6 in Table 1 is the composition and the eutectoid carbon content of the prior art GCr15.
  • a plurality of small samples were prepared for the samples 1, 2, 3, 4 and 5 in Table 1, respectively, and heat treatment was performed to characterize the mechanical properties of the small samples after heat treatment, as shown in Table 2.
  • the hardness of the GCr15 bearing steel in the prior art is about 62HRC, and the plane fracture toughness is about 16.9 MPa.m 1/2 .
  • the molded article of the present invention has better overall mechanical properties than the prior art GCr15 bearing steel.
  • the compressive strength of these samples was tested to be between 3,200 MPa and 3,500 MPa. It can thus be seen that the molded part according to the invention has a very good pressure resistance.
  • Table 3 shows the volume content of the microstructure of a plurality of small samples.
  • Figs. 1 to 5 show the microstructures of the heat-treated small samples 1-1, 2-1, 3-1, 4-1 and 5-1, respectively.
  • reference numeral ⁇ ' is martensite
  • ⁇ b is bainite
  • ⁇ is retained austenite
  • ⁇ is cementite.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • General Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Rolling Contact Bearings (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

一种用于制造轴承的钢材，其包括以重量含量计1.22-1.6％的C、0.5-2％的Cr、4-8％的Al、0.1-1.5％的Mn以及小于等于0.7％的Si，余量为Fe和杂质。热处理先经过马氏体相变再进行贝氏体相变，冷却至室温，经过该热处理之后的成型件或轴承含有较多的马氏体和较多的残余奥氏体。

Description

用于制造轴承的钢材、对其进行热处理的方法和成型件
相关申请的交叉引用
本申请要求享有于2016年1月15日提交的名称为“用于制造轴承的钢材、对其进行热处理的方法和成型件”的中国专利申请CN201610027568.1的优先权，该申请的全部内容通过引用并入本文中。
技术领域
本发明涉及金属材料领域，特别涉及一种钢材。本发明还涉及对这种钢材进行热处理的方法。本发明还涉及一种成型件。
背景技术
轴承作为机械设备中的重要零件，其功能是支撑机械旋转体，降低其运动过程中的摩擦系数，并保证其回转精度。随着科技的发展，在一些特种设备中，往往需要能承受高转速、高负荷、高温、低温并且低噪音的轴承。这要求轴承钢具有高的尺寸稳定性、高硬度、高强度、优异的滚动接触疲劳性能以及耐磨性。
在现有技术中，GCr15轴承钢是常用的高硬度轴承钢，其碳含量在0.95％到1.05％重量之间。在淬火热处理后，GCr15轴承钢的淬火态硬度范围在61HRC到64HRC之间。回火后的硬度值范围在58HRC到62HRC之间。
GCr15轴承钢在制备过程中，在进行淬火发生马氏体相变后，再进行回火以尽量使残余奥氏体分解，这是为了避免残余奥氏体在外力作用下发生马氏体相变而导致轴承尺寸发生变化。由此，通常在室温下，GCr15轴承钢仅含有不到3％体积的残余奥氏体。如此少的残余奥氏体使得轴承在受到较大的外力时，极易产生裂纹，甚至直接导致轴承损坏。这严重限制了由GCr15轴承钢制备的轴承的使用范围。
发明内容
针对上述问题，本发明提出了一种用于制造轴承的钢材。这种钢材含有较多 的碳和铝。使用这种钢材并经过本发明的热处理方法之后得到的成型件或轴承含有较多的马氏体和较多的残余奥氏体，这使得成型件或轴承具有高的硬度。此外，绝大部分的这些残余奥氏体在外力作用下不会发生马氏体相变，由此可确保该成型件或轴承的尺寸不变，并且这些残余奥氏体可以有效地抑制构件或轴承由于受到外力作用而产生裂纹或裂纹扩展。
根据本发明的第一方面，提供了一种用于制造轴承的钢材。以重量含量计，这种钢材包括1.22-1.6％的C、0.5-2％的Cr、4-8％的Al、0.11-1.5％的Mn以及小于等于0.7重量的Si，余量为Fe和杂质。
与GCr15轴承钢的碳含量(GCr15轴承钢的共析碳含量为约0.5wt.％)或铁碳热平衡二元相图中的共析钢的碳含量相比，本发明的用于制造轴承的钢材含有4-8％的铝，使得碳的含量被提高到1.22-1.6％，但是在钢材内部仍然不存在网状碳化物，钢材的组织也较为均匀。在随后的热处理过程中，钢材的良好的组织分布方式会遗传下去，从而使得热处理后的成型件的组织和性能非常均匀。
在热处理过程中，钢材中的铝提高钢材的马氏体相变温度，这抵消了由钢材的较高的碳含量导致的马氏体相变温度降低。由此，本发明的钢材经热处理后仍具有较多的马氏体，这使得由本发明的钢材制备的轴承具有非常高的硬度。马氏体内含有较多的碳，也会使得所制备的轴承具有非常高的硬度。
更重要的是，由于钢材中存在有铝，在马氏体相变后的低温热处理过程中，在马氏体相变后剩余的奥氏体即使部分发生分解，仍然会有较大量的奥氏体剩余。这些剩余的奥氏体会形成在室温下稳定的残余奥氏体。与现有技术中的GCr15轴承钢以及其他类型的轴承钢相比相比，由本发明的钢材制备的最终成型件含有更多的残余奥氏体。在成型件受到外力作用时，这些残余奥氏体会抑制脆性的马氏体(或成型件)产生裂纹及扩展。
此外，在上述的马氏体相变后的低温热处理过程中，铝会使钢材的其他组织的过量的碳进入到残余奥氏体内，这导致残余奥氏体的含碳量会大幅增加。例如，残余奥氏体的碳含量可达到以重量含量计2％到5％。与现有技术中的GCr15轴承钢以及其他类型的轴承钢相比(这些轴承钢的碳含量最高为以重量含量计1.9％)相比，由本发明的钢材制备的最终成型件的残余奥氏体的碳含量会较高，使得其稳定性非常好并且不会发生马氏体相变。对于轴承而言，在使用过程中，稳定的残余奥氏体几乎不发生马氏体转变，因此受力条件下成型件或轴承的尺寸变化非 常小。残余奥氏体含有较多的碳也会抑制奥氏体分解，这也使得由本发明的钢材制备的最终成型件内会有较大量的残余奥氏体。
此外，Al的加入还可以降低钢材的密度，这有利于降低所制备的成型件的重量。例如，常规GCr15轴承钢的密度约为7.86g/cm3，而本发明的一种钢材Fe-1.25C-1.5Cr-5Al(即，以重量含量计，C含量为1.25％左右、Cr含量为1.5％左右、Al含量为5％左右，余量为Fe和杂质)的密度约为7.34g/cm3。
应理解的是，本发明的用于制造轴承的钢材可以为铸锭、棒材、线材、管材或其他任何适当的形状。
在一个实施例中，该钢材还包括由以下元素组成的组中的至少一种：以重量含量计，1.0％以下的Mo；1.0％以下的W；0.05％以下的Ti；0.2％以下的Nb；0.2％以下的Zr；0.2％以下的V；2.0％以下的Cu；以及4.0％以下的Ni。
根据本发明的第二方面，提出了对上述用于制造轴承的钢材进行热处理的方法。该方法包括：步骤一：将钢材进行马氏体相变；步骤二：将进行马氏体相变后的钢材进行贝氏体相变；以及步骤三：冷却到室温。
正如本领域的技术人员熟知：钢材中发生马氏体相变的过程中，并不是所有的奥氏体都会转变成马氏体，而是有部分奥氏体残留下来形成残余奥氏体。在现有技术中，通常需要将这些残余奥氏体分解，以避免在外力下残余奥氏体发生马氏体相变，而造成成型件的体积发生变化。
然而，根据本发明的热处理方法，并不需要完全除去这些残余奥氏体，相反要保留一部分残余奥氏体。在本发明的热处理方法的步骤二中，进行贝氏体相变(即，马氏体相变后的再次加热的低温热处理)。在整个过程中，仅部分残余奥氏体转变成贝氏体，很多的残余奥氏体得以保留下来。由此，在根据本发明的热处理方法处理后的钢材或成型件中，会有较多的残余奥氏体。
此外，在步骤二中，Al还会抑制碳转变成碳化物，而是使贝氏体相变期间所产生的过量的碳进入到残余奥氏体内。Al同样会使马氏体内的过量的碳进入到残余奥氏体内。由此提高了残余奥氏体的碳含量，这会抑制奥氏体发生贝氏体相变，从而使得由本发明的钢材制备的最终成型件内会有较大量的残余奥氏体。
贝氏体是在残余奥氏体上形核长大的，这会将残余奥氏体切割非常细小的残余奥氏体组织，这也有助于提高残余奥氏体的稳定性。如上文所述，这种高碳且细小的残余奥氏体的稳定性非常好，即使在外力作用下，高碳的残余奥氏体也几 乎不会发生马氏体转变。钢材内高韧性的奥氏体抑制了成型件在受到外力作用时裂纹的扩展。
在一个实施例中，在步骤一中，马氏体相变的加热温度为800℃到950℃，保温时间为10分钟到300分钟。在一个优选的实施例中，在步骤一中，马氏体相变的冷却步骤为冷却到室温到零下196℃之间的温度，冷却时间为0.5分钟到300分钟。在本申请中，室温可理解为18℃到27℃之间的温度，优选为20℃到25℃之间的温度。
在一个实施例中，在步骤二中，贝氏体相变的加热温度为150℃到250℃，保温时间为6小时到240小时，优选为6小时到140小时。申请人对贝氏体相变进行如下解释。在室温下，钢材中的残余奥氏体具有发生贝氏体相变的很大的热力学驱动力。但是，由于温度较低，原子扩散速度非常慢，导致贝氏体转变实际上难以发生。在步骤二中，150℃到250℃的加热温度使得原子扩散速度得到大幅提高，使得残余奥氏体能够顺利地发生贝氏体转变。
贝氏体相变的保温时间为6小时到240小时，这有助于充分进行贝氏体相变，以提高残余奥氏体中的碳含量。保温时间小于6小时，则不能保证充分进行贝氏体相变，并且残余奥氏体中的碳含量达不到要求。
应理解的是，在贝氏体相变期间，也释放了因马氏体相变产生的内应力。
在一个实施例中，在步骤一中，马氏体相变的冷却步骤可采用冰水混合物冷却、液态氮气冷却或其他任何适当的冷却方式。
在一个实施例中，在对钢材加热和保温期间，使用保护气体来防止钢材被氧化。在一个优选的实施例中，保护气体为惰性气体或氮气。
根据本发明的第三方面，提出了一种成型件，其由上述的用于制造轴承的钢材，经上述的对钢材进行热处理的方法进行热处理而得到。以体积含量计，成型件的微观组织包括：4％至10％的残余奥氏体，80％至90％的马氏体，以及5％以下的碳化物，余量为贝氏体和杂质。如上文所述，一定含量的残余奥氏体有助于抑制成型件裂纹的扩展。
在一个实施例中，以重量含量计，残余奥氏体包含2％到5.5％的碳。如上文所述，残余奥氏体的含碳量如此高，有助于提高残余奥氏体的稳定性，防止其发生马氏体相变。优选地，残余奥氏体的尺寸10纳米到500纳米，更优选为10纳米到50纳米。此外，残余奥氏体的形貌大体为膜状。这也有助于提高成型件的 力学性质。
在一个实施例中，成型件的硬度在64HRC到69HRC之间，平面断裂韧性在16MPa.m1/2到28MPa.m1/2之间。平面断裂韧性用于表征成型件在受到外力作用下，成型件抵抗裂纹扩展、断裂的能力，吸收变形能量的能力。平面断裂韧性越高，则成型件的阻碍裂纹扩展的能力越好。
在一个实施例中，成型件为轴承的套圈、外圈、内圈、滚动体和保持架组成的组中的任意一个或多个。
与现有技术相比，本发明的优点在于：本发明的钢材中含有较多的碳和铝。在使用本发明的钢材制备的成型件中含有较多的马氏体和较多的残余奥氏体，残余奥氏体也非常稳定，因此成型件具有非常高的硬度，并且在外力冲击下也不会产生裂纹。
附图说明
在下文中将基于实施例并参考附图来对本发明进行更详细的描述。其中：
图1是根据本发明的试样1-1的微观组织照片；
图2是根据本发明的试样2-1的微观组织照片；
图3是根据本发明的试样3-1的微观组织照片；
图4是根据本发明的试样4-1的微观组织照片；以及
图5是根据本发明的试样5-1的微观组织的照片。
具体实施方式
下面将结合附图对本发明作进一步说明。
首先来说明钢材的钢材成分，以下各个钢材元素的含量均是以重量计。
C：1.22-1.6％
碳是最便宜的强化元素，其可以通过间隙固溶以及弥散强化的方式来提高钢的硬度。当碳含量低于1.22％时，在奥氏体化过程中，渗碳体完全溶解就去奥氏体之后会有部分铁素体剩余，这会降低钢材的硬度及恶化钢材韧性；且较低的碳含量不利于提高马氏体的硬度。碳含量高于1.6％时，碳会增大形成网状碳化物的倾向而使钢材以及由钢材制备的轴承因组织遗传造成的组织不均匀性而恶化轴承使用性能。所以，碳含量的范围是1.22-1.6％。在这种范围中，在奥氏体化过程 中，不会有铁素体剩余，并且碳化物只能弥散分布，而不是形成网状碳化物。这种弥散分布的碳化物可以有效地提高钢材的硬度和强度。
Al：4-8％
铝是本发明的钢材中的重要元素。铝是轻量元素，其密度很低，接近于铁的1/3，因此通过使用铝置换铁可以降低钢材的密度，从而达到降低重量的目的。通常而言，提高马氏体中碳含量是提高钢材硬度的最经济最实用的方法，但碳含量的提高会导致马氏体相变温度降低，从而降低淬火热处理得到的马氏体体积分数，进而降低材料硬度，因此简单提高碳含量不能提高轴承钢硬度。在本发明的钢材中，铝会提高马氏体相变温度点，使得提高碳含量的情况下因铝的添加确保了钢材的马氏体转变温度大体保持不变，由此马氏体的含量不会减少，因此可确保本发明钢材进行热处理后达到高硬度。另一方面，在低温热处理过程(即本发明的贝氏体相变过程)中，因铝可抑制碳转变成渗碳体或碳化物。这样，本发明钢材在贝氏体相变过程中会发生碳向奥氏体中富集，使得残余奥氏体中的碳含量大幅提高。奥氏体的高含碳量又反过来抑制了奥氏体发生贝氏体相变。由此，Al使得本发明的钢材可被制成含有较大量的残余奥氏体，并且残余奥氏体含碳量也较高的制品。此外，通过贝氏体相变可获得超细的残余奥氏体组织，且添加铝可还可提高贝氏体相变速度，有利于缩短贝氏体相变的时间。铝含量过低，不能充分实现上述作用，因此铝的下限为4％。高于8％的铝会在钢材中形成脆性的Fe-Al合金化合物，恶化材料性能。因此，铝的上限定为8％。
Cr：0.5-2％
铬能提高淬透性和耐腐蚀性，是本发明的钢材的重要合金元素。铬可提高钢材淬透性。铬可在轴承钢中形成高硬度的铬碳化物或者形成富铬渗碳体以改善轴承钢中碳化物的性能，提高轴承钢的硬度和抗滚动接触疲劳性能。铬的含量过低不能启动足够的上述作用，所以铬含量的下限是0.5％。铬含量过高会降低钢材的共析碳含量而增加生成网状碳化物的趋势；过高铬含量降低马氏体相变温度而降低马氏体分数，同时降低马氏体含量降低马氏体硬度，因此导致钢材硬度的降低。此外，铬含量过高会显著提高钢的脆性转变温度。因此，铬含量的上限是2％。
Mn：0.1-1.5％
锰能提高钢材淬透性。但锰会降低钢材的共析碳含量而增加生成网状碳化物的趋势；高的锰含量降低马氏体相变温度而降低马氏体分数，同时降低马氏体中 含量降低马氏体硬度，因此导致钢材硬度的降低。此外，锰含量过高会显著提高钢的脆性转变温度，且钢材的过热敏感性和生成裂纹的倾向也会增强。而炼钢过程中钢水中均含有一定的锰，因此锰的含量限制为0.1-1.5％。
Si：小于等于0.7％
在钢材中，硅会使钢的过热敏感性、裂纹和脱碳倾向性增大，炼钢过程中的钢水均含有Si，将Si含量控制在较低水平会导致成本增加。所以，将硅的含量控制在少于等于0.7％。
Mo、W：1.0％以下
Mo、W提高钢材的淬透性可有效提高钢的强度，也是碳化物形成元素，有助于形成高硬度的碳化物，提高钢材硬度。当其含量大于1.0％的情况下，不能进一步提高钢材的硬度，反而会增加成本。
Ti、Nb、Zr、V：0.2％以下
Ti、Nb、Zr和V可以使钢材的晶粒细化并且提高强度。Ti、Nb、Zr和V的含量过低则起不到作用，而大于0.2％则会增加不必要的成本。
Cu：2.0％以下，Ni：4％以下
Cu能提高强度，特别是大气腐蚀性能。但是，如果Cu的含量大于2.0％，则加工性会劣化，例如热轧过程可形成液相而导致开裂，另外还会导致不必要的成本增加。Ni能提高钢的强度，并且保持良好的塑性和韧性。如果Ni的浓度大于4.0％则会带来成本增加。
应理解的是，对于本申请的钢材而言，上述的Mo、W、Ti、Nb、Zr、V、Cu以及Ni并不是必须的合金元素。
表1显示了根据本发明的一些钢材的成分，余量为铁和杂质。在表1中还列出了钢材的共析碳含量。此外，在表1中的试样6是现有技术中的GCr15的成分和共析碳含量。
表1
试样 C Al Cr Mn Si 共析碳含量
1 1.25 4.98 1.48 0.38 0.25 1.25
2 1.26 5.1 1.51 0.32 0.24 1.25
3 1.38 6 1.45 0.36 0.22 1.32
4 1.45 7 1.45 0.36 0.22 1.41
5 1.5 7 1.55 0.34 0.23 1.41
6 1.07 0.02 1.3 0.41 0.21 0.5
对表1中的试样1、2、3、4和5分别制备了多个小试样，并分别进行了热处理，表征了热处理后的小试样的力学性能，如表2所示。
表2
Figure PCTCN2016072301-appb-000001
现有技术中的GCr15轴承钢的硬度在62HRC左右，平面断裂韧性在16.9MPa.m 1/2左右。由表2可知，与现有技术中的GCr15轴承钢相比，本发明的成型件具有更好的综合力学性能。此外，经测试，这些试样的压缩强度在3200MPa到3500MPa之间。由此可见，根据本发明的成型件的抗压能力也非常好。
表3显示了多个小试样的微观组织的体积含量。为了进一步地说明，图1到 5分别显示了经热处理后的小试样1-1、2-1、3-1、4-1和5-1的微观组织。在图中，附图标记α’为马氏体、αb为贝氏体、γ为残余奥氏体、θ为渗碳体。
表3
试样 马氏体(％) 残余奥氏体(％) 贝氏体(％) 渗碳体(％)
1-1 88 8 3.2 0
1-2 87.5 7.9 4.2 0
1-3 90 7 2.8 0
1-4 90 6.5 3.2 0
1-5 86 9.3 4 0
1-6 87 8.5 3.8 0
2-1 85.5 9.1 5 0
2-2 86 9.6 4.5 0
3-1 80 10 3.2 3.9
3-2 81.7 10 3 2.5
4-1 80 9 2.8 4.8
4-2 82 10 3.5 4.2
5-1 83 9.6 2.3 4.5
5-2 80 9.5 2.5 5
虽然已经参考优选实施例对本发明进行了描述，但在不脱离本发明的范围的情况下，可以对其进行各种改进。尤其是，只要不存在冲突，各个实施例中所提到的各项技术特征均可以任意方式组合起来。本发明并不局限于文中公开的特定实施例，而是包括落入权利要求的范围内的所有技术方案。

Claims (10)

  1. 一种用于制造轴承的钢材，其特征在于，以重量含量计，所述钢材包括1.22-1.6％的C、0.5-2％的Cr、4-8％的Al、0.1-1.5％的Mn以及小于等于0.7％的Si，余量为Fe和杂质。
  2. 如权利要求1所述的钢材，其特征在于，以重量含量计，还包括由以下元素组成的组中的至少一种：
    1.0％以下的Mo；
    1.0％以下的W；
    0.05％以下的Ti；
    0.2％以下的Nb；
    0.2％以下的Zr；
    0.2％以下的V；
    2.0％以下的Cu；以及
    4.0％以下的Ni。
  3. 一种对根据权利要求1或2所述的用于制造轴承的钢材进行热处理方法，其特征在于，包括以下步骤：
    步骤一：将所述钢材进行马氏体相变；
    步骤二：将进行马氏体相变后的钢材进行贝氏体相变；以及
    步骤三：冷却到室温。
  4. 如权利要求3所述的方法，其特征在于，在所述步骤一中，所述马氏体相变的加热温度为800℃到950℃，保温时间为10分钟到300分钟。
  5. 如权利要求4所述的方法，其特征在于，在所述步骤一中，所述马氏体相变的冷却步骤为冷却到室温到零下196℃之间的温度，冷却时间为0.5分钟到300分钟。
  6. 如权利要求3到5中任一项所述的方法，其特征在于，在所述步骤二中，所述贝氏体相变的加热温度为150℃到250℃，保温时间为2小时到240小时，优选为6小时到140小时。
  7. 一种成型件，其由权利要求1或2所述的用于制造轴承的钢材，经权利要求3到6中任一项所述的对钢材进行热处理的方法进行热处理而得到，
    其中，以体积含量计，所述成型件的微观组织包括：4％至10％的残余奥氏体，80％至90％的马氏体，以及5％以下的碳化物，余量为贝氏体和杂质。
  8. 如权利要求7所述成型件，其特征在于，以重量含量计，所述残余奥氏体包含2％到5.5％的碳。
  9. 如权利要求7或8所述成型件，其特征在于，所述成型件的硬度在64HRC到69HRC之间，平面断裂韧性在16MPa.m1/2到28MPa.m1/2之间。
  10. 如权利要求7至9中任一项所述成型件，其特征在于，所述成型件为轴承的套圈、外圈、内圈、滚动体和保持架组成的组中的任意一个或多个。
PCT/CN2016/072301 2016-01-15 2016-01-27 用于制造轴承的钢材、对其进行热处理的方法和成型件 Ceased WO2017120987A1 (zh)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201610027568.1A CN105671435B (zh) 2016-01-15 2016-01-15 对用于制造轴承的钢材进行热处理的方法和成型件
CN201610027568.1 2016-01-15

Publications (1)

Publication Number Publication Date
WO2017120987A1 true WO2017120987A1 (zh) 2017-07-20

Family

ID=56301055

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2016/072301 Ceased WO2017120987A1 (zh) 2016-01-15 2016-01-27 用于制造轴承的钢材、对其进行热处理的方法和成型件

Country Status (2)

Country Link
CN (1) CN105671435B (zh)
WO (1) WO2017120987A1 (zh)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111961811A (zh) * 2020-09-04 2020-11-20 燕山大学 一种利用相变速度差制备耐冲击钢制零件的方法
CN114686661A (zh) * 2022-03-21 2022-07-01 燕山大学 一种调控贝氏体钢中偏析与基体性能差方法及钢工件

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106591697A (zh) * 2016-11-09 2017-04-26 安徽千禧精密轴承制造有限公司 一种轴承合金钢和热处理方法
CN107130181A (zh) * 2017-06-22 2017-09-05 合肥力和机械有限公司 一种家电专用轴承钢球及其制备方法
CN108220807B (zh) * 2017-12-21 2020-07-24 钢铁研究总院 一种低密度高铝超高碳轴承钢及其制备方法
WO2019222950A1 (en) * 2018-05-24 2019-11-28 GM Global Technology Operations LLC A method for improving both strength and ductility of a press-hardening steel
CN112534078A (zh) 2018-06-19 2021-03-19 通用汽车环球科技运作有限责任公司 具有增强的机械性质的低密度压制硬化钢
US11530469B2 (en) 2019-07-02 2022-12-20 GM Global Technology Operations LLC Press hardened steel with surface layered homogenous oxide after hot forming
CN117551941A (zh) * 2023-10-31 2024-02-13 中国科学院金属研究所 一种耐高温轻质轴承钢及其制备方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH11293410A (ja) * 1998-04-07 1999-10-26 Nippon Shirikoroi Kogyo Kk 析出硬化型高珪素鋼製品の熱処理方法
JP2000204443A (ja) * 1998-11-11 2000-07-25 Ntn Corp 高温用転がり軸受部品
CN101586216A (zh) * 2009-06-25 2009-11-25 莱芜钢铁集团有限公司 一种超高强韧贝氏体钢及其制造方法
CN103122433A (zh) * 2013-01-31 2013-05-29 西安交通大学 一种超高碳型轴承钢
CN103540726A (zh) * 2013-09-25 2014-01-29 西安交通大学 一种超高碳型轴承钢的热处理方法

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102221495A (zh) * 2011-03-31 2011-10-19 洛阳Lyc轴承有限公司 一种显示40Cr15Mo2VN轴承钢原始奥氏体晶界的方法
CN102108433B (zh) * 2011-04-01 2012-07-25 瓦房店轴承集团有限责任公司 一种轴承钢淬火的方法

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH11293410A (ja) * 1998-04-07 1999-10-26 Nippon Shirikoroi Kogyo Kk 析出硬化型高珪素鋼製品の熱処理方法
JP2000204443A (ja) * 1998-11-11 2000-07-25 Ntn Corp 高温用転がり軸受部品
CN101586216A (zh) * 2009-06-25 2009-11-25 莱芜钢铁集团有限公司 一种超高强韧贝氏体钢及其制造方法
CN103122433A (zh) * 2013-01-31 2013-05-29 西安交通大学 一种超高碳型轴承钢
CN103540726A (zh) * 2013-09-25 2014-01-29 西安交通大学 一种超高碳型轴承钢的热处理方法

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111961811A (zh) * 2020-09-04 2020-11-20 燕山大学 一种利用相变速度差制备耐冲击钢制零件的方法
CN111961811B (zh) * 2020-09-04 2022-05-24 燕山大学 一种利用相变速度差制备耐冲击钢制零件的方法
CN114686661A (zh) * 2022-03-21 2022-07-01 燕山大学 一种调控贝氏体钢中偏析与基体性能差方法及钢工件
CN114686661B (zh) * 2022-03-21 2023-03-24 燕山大学 一种调控贝氏体钢中偏析与基体性能差方法及钢工件

Also Published As

Publication number Publication date
CN105671435A (zh) 2016-06-15
CN105671435B (zh) 2018-01-09

Similar Documents

Publication Publication Date Title
CN105671435B (zh) 对用于制造轴承的钢材进行热处理的方法和成型件
CN105026602B (zh) 高频淬火构件的半成品及其制造方法
JP6432932B2 (ja) 耐ピッチング性および耐摩耗性に優れる高強度高靱性機械構造用鋼製部品およびその製造方法
CN101421425B (zh) 马氏体系工具钢的淬火前处理方法和淬火处理方法
CN104321454A (zh) 卷绕性和耐氢脆性优异的高强度弹簧用钢丝及其制造方法
CN105925880A (zh) 轴承钢
CN111511936A (zh) 用于冷镦的线材、使用其的加工产品、及其制造方法
JP2021535278A (ja) 靭性及び腐食疲労特性が向上されたスプリング用線材、鋼線及びその製造方法
CN109161667B (zh) 一种轴承构件及其制备方法
JP7464822B2 (ja) 軸受軌道用鋼材、および軸受軌道
JP2012237052A (ja) 冷間鍛造性および結晶粒粗大化抑制能に優れた肌焼鋼とその製造方法
JP6055397B2 (ja) 耐摩耗性に優れた軸受部品、およびその製造方法
JP2012158827A (ja) 表面硬化用熱間加工鋼材
JP6390685B2 (ja) 非調質鋼およびその製造方法
JP6205960B2 (ja) 軸受用鋼
JP2008248282A (ja) 高周波焼入れ部品およびその製造方法
CN108866442B (zh) 超高碳钢的热处理方法及制品
JP6205961B2 (ja) 軸受及び転がり軸受並びにこれらの製造方法
KR101713677B1 (ko) 전동피로수명 특성이 우수한 고질소 공기 경화형 베어링강 및 그 제조방법
KR100940724B1 (ko) 베어링용 고탄소 강선재의 제조방법, 고탄소강 베어링의 열처리 방법 및 고탄소강 베어링
TW200418997A (en) High tensile strength steel having excellent fatigue strength and method of producing the same
JP4631617B2 (ja) 疲労特性に優れた軸受用鋼部品の製造方法
CN112853049B (zh) 一种高性能轴套材料及其热处理方法
WO2014019670A1 (en) Low temperature heat treatment for steel alloy
JP2013255925A (ja) 中空ばね用シームレス鋼管の製造方法

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 16884549

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

32PN Ep: public notification in the ep bulletin as address of the adressee cannot be established

Free format text: NOTING OF LOSS OF RIGHTS PURSUANT TO RULE 112(1) EPC

122 Ep: pct application non-entry in european phase

Ref document number: 16884549

Country of ref document: EP

Kind code of ref document: A1