WO2017120987A1 - Matériau d'acier pour fabrication de palier, procédé de conduite d'un traitement thermique sur celui-ci et pièce formée - Google Patents

Matériau d'acier pour fabrication de palier, procédé de conduite d'un traitement thermique sur celui-ci et pièce formée Download PDF

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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
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Prior art keywords
steel
bearing
steel material
less
transformation
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PCT/CN2016/072301
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English (en)
Chinese (zh)
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易红亮
庞佳琛
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东北大学
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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.

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  • 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

La présente invention concerne un matériau d'acier pour fabriquer un palier, comprenant en poids 1,22 à 1,6 % de carbone, 0,5 à 2 % de chrome, 4 à 8 % d'aluminium, 0,1 à 1,5 % de manganèse et une quantité inférieure ou égale à 0,7 % de silicium, le reste comprenant du fer et des impuretés. Le traitement thermique met en œuvre, dans un premier temps, une transformation martensitique et une transformation bainitique, puis un refroidissement à température ambiante, de sorte que le palier ou la pièce formée après traitement thermique contienne des quantités supérieures de martensite et d'austénite résiduelle.
PCT/CN2016/072301 2016-01-15 2016-01-27 Matériau d'acier pour fabrication de palier, procédé de conduite d'un traitement thermique sur celui-ci et pièce formée WO2017120987A1 (fr)

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CN201610027568.1 2016-01-15
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

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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

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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
CN112513310A (zh) 2018-05-24 2021-03-16 通用汽车环球科技运作有限责任公司 改善压制硬化钢的强度和延性的方法
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

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