WO2007122754A1 - 焼戻し軟化抵抗の大きいブレーキディスク - Google Patents
焼戻し軟化抵抗の大きいブレーキディスク Download PDFInfo
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- WO2007122754A1 WO2007122754A1 PCT/JP2006/320358 JP2006320358W WO2007122754A1 WO 2007122754 A1 WO2007122754 A1 WO 2007122754A1 JP 2006320358 W JP2006320358 W JP 2006320358W WO 2007122754 A1 WO2007122754 A1 WO 2007122754A1
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- brake disc
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Classifications
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- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- 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
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D65/00—Parts or details
- F16D65/02—Braking members; Mounting thereof
- F16D65/12—Discs; Drums for disc brakes
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- 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
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D2200/00—Materials; Production methods therefor
- F16D2200/0004—Materials; Production methods therefor metallic
- F16D2200/0008—Ferro
- F16D2200/0021—Steel
Definitions
- the size of the burnout ⁇ 3 ⁇ 4 ⁇ means the initial positive hardness (!, A special product that can maintain the hardness after softening after being subjected to high temperature. Background sickle
- the XV which is used in autono- ries and automobiles, is a combination of brake discs and brake pads, which are converted into vertical leggies to suppress the rotation of the vehicle and brake.
- the brake disc has an 'appropriate hardness roper handness' and is also excellent in wear resistance and tree life.
- the brake discs are low in hardness, the sickle with the brake pads (the wear and tear of the brake pads will increase and the brakes will work better) will become worse.
- the brake disc force is too high, it causes a so-called brake squeak. Therefore, the hardness of the brake disc is 32 ⁇ in the Rockwell K3 ⁇ 4M (Rodwell C hardness) (HRC) defined by JIS Z2245. It will be reduced to ⁇ 38cm.
- ⁇ protects ⁇ i ⁇ 3 ⁇ 4gbbal enviroment), so there is a strong demand for 1 ⁇ 2ifel efficiency in autonomic vehicles and automobiles.
- the brake mechanism 7 is a brake disc, and the rake is not an exception.
- the brake discs / thinning causes a reduction in the heat capacity of the brake discs themselves, the brake discs will increase over 650 ° C. There are things to do. For this reason, the conventional rake discs made of male / ⁇ and ⁇ -type stainless steel have the problem that the durability is reduced due to!
- Japanese Patent Laid-Open No. 2002_1464 $ 9 states that one or more of Ti, Nb, V, ⁇ must be iiN3 ⁇ 4r ⁇ .
- the low carbon carbon / ⁇ "ite-based stainless steel that suppresses softening has been tested by TV, and also in Japanese Patent No. 3315974 (JP 2001-220654 A), there is an Nb layer (and A stainless steel for disc y rake that suppresses I ⁇ L softening is proposed by adding 13 ⁇ 4 * or more of Ti, V, and B.
- an object of the present invention is to resolve the above-mentioned problems of the slaves and to provide a brake disc having an appropriate hardness and a large Lf appearance.
- the present invention is C: 0. Lmass% or less, Si: l. Qmass% or less, Mri: 2. Qmass% or less, Cr: l 0.5-15. Qmass%, Ni: 2. Qmass% or less, Gu: more than 0.5 to 4. Qmass%, Nb: 0 .. 02—0.3 mas s%, N: 0. Less than lmass% 3 ⁇ 4r ⁇ , and C, N, Nb, Cr, Si, Ni, Mn, Mo and Cu can be replaced by the following formula (1), formula (2);
- Chapter 15 has a collar, collar 15 has a component castle consisting of e and inevitable impurities, and the former austenite grain flatness: 3 ⁇ 4 ⁇ fiber is 8 ⁇ m or more and has & 5 m / ⁇ , 'The hardness is 3 ⁇ 4RC and t is between 32 and 38.
- 3 ⁇ 4 be fe3 ⁇ 4 with a large brake disc of 3 ⁇ 4 Li ⁇ l ⁇ 3 ⁇ 4. '
- the present invention further provides a brake disc having a ratio of the amount of precipitated Nb to the amount of ⁇ b (the amount of precipitated Nb3 ⁇ 4 ⁇ b) being less than 0.75.
- the above brake disc of the present invention should have a square root T) force of 8 to 1.3 X 103 ⁇ 4n 1 in the manolette structure.
- the above-mentioned brake disc of the present invention has a hardness force after cauterization at 650 ° C of lhrf3 ⁇ 4i ⁇ more than 30 'at RC 3 ⁇ 4 RC, a certain, lhr
- the average density of dislocations in the mittite after L is from 0.6 to 1.3 ⁇ 103 ⁇ 4 1 , and it is assumed that ⁇ ⁇ precipitates on wisteria ii ⁇ . '
- the above brake disk of the present invention further makes it difficult to have at least one component Sr ⁇ of the following
- Group B Ti: 0.02 to 0.3mass%, V: 0.02—0.3mass%, Zr: 0.02-vO. 3mass% and Ta: 0.02
- ⁇ 0. 3mass 0/0 is 13 ⁇ 43 ⁇ 4 other selected from among the more than 23 ⁇ 4
- Fig. 1 ⁇ and; 3 ⁇ 4 b on the hardness (HRC) after old austenite grains: ⁇ Effect of grain size
- Fig. 2 This is a graph showing the effect of precipitation (N 3 ⁇ 4 / ⁇ Nb amount) on the hardness (HC) after L ⁇ ). Aira's form to invent the invention
- Mano emission site stainless steel sheet fine consists essentially of Fe, and T3 ⁇ 4 ⁇ varied 4 level between the pressure 1000 to 1150 ° C, Hesitate for 1 minute and then 200.
- C3 ⁇ 41? Is cooled at an average cooling rate of 10 ° C / sec.
- Fig. 1 shows the influence of the flatness of old austenite (former ⁇ ) grains on the hardness (HRC) of the steel sheet surface. From Fig. 1 ', in the stainless steel plate with the above component yarn, the average particle size of the old ⁇ grains was 8! 1 ⁇ 2 ⁇ 1 ⁇ hardness 3 ⁇ 43 ⁇ 4 C: 32 to 38 : and at the same time lhr
- Figure 2 shows the effect on the hardness of the steel sheet after the Zhede (Nb3 ⁇ 4 / ⁇ Nb amount) force treatment based on the results.
- Fig. 2 shows that even after 650 ° C lhrS 1 ⁇ Lake L treatment, HRC: 30 or more can be obtained. It is necessary to be there.
- the Zheide Nb3 ⁇ 4 / quantity) is low, and the 3 ⁇ 4gL soft pile is large.
- the reason is as follows.
- Zhede 3 ⁇ 4fi 3 ⁇ 4 * is usually 0.9 or more.
- the heating beam in; ⁇ partly dissolves part of the upper fB ⁇ out Nb, and this solid precipitates in Gyoda at ⁇ 1 ⁇ 2 L and contributes to precipitation strengthening.
- the dissolution of precipitated Nb becomes insufficient, and the amount of solid b in the firing decreases, so the amount of Nb precipitates that precipitate in subsequent firing b decreases.
- I ⁇ UM ⁇ C is considered to decrease; 1 ⁇ 2.
- the ⁇ mano / ⁇ t fiber obtained from the inside has a high-density fei standing inside. It is well known that the higher the standing density, the harder it is. Therefore, the inventors investigated the relationship between the dislocation density inherent in the steel manolite and the hardness of the brake disc. Are closely related, and it is possible to control the hardness of the brake disc in the positive range by adjusting it to ⁇ (in the vertical density 3 ⁇ 4i range), and ⁇ In order to prevent such softening, some means should be used.
- Thread Iyanaka ⁇ (Suppressing the recovery of standing and maintaining a dislocation density of 3 ⁇ 4g in the positive range and a force of f3 ⁇ 4 When cu was encouraged as a component and received u ⁇ , it was found that the recovery of dislocations can be suppressed by precipitating cu on Gita in 3 ⁇ 4fi.
- C is an element that determines the hardness of the brake disc.
- HRC hardness: 32 to 38
- 0.lmass 0 / o is contained at an age, ⁇ 3 ⁇ 43 ⁇ 4 ⁇ , toughness that lowers corrosion resistance! 3 ⁇ 4 Since C is reduced, it is necessary to make C or less less than .lmass%.
- Si is a 5 element added as a reversion, and it is desirable to contain more than 0.05 ⁇ s%.
- Si is a ferrite phase stabilizing element, and 1. Omass% 3 ⁇ 4 ⁇ Therefore, Si is L Qmass. Limited to: From the viewpoint of toughness, 0.5 mass% or less is preferable.
- Mn suppresses ⁇ of ferrite phase at i temperature and improves i ⁇ A ⁇ property, so it is stable c ⁇ A ; It is an element useful for 5 and 0.3 mass% or more It is desirable to contain. However, if 2. Qmas s% is contained, it becomes S and TMnS3 ⁇ 4 ⁇ , which decreases the corrosion resistance. Therefore, it is limited to 2. Qmass%. ⁇ In order to further improve the properties, 1. Exceeding Qmass% is preferable, more preferably 1.2
- Cr is an essential element to ensure a certain corrosion resistance of stainless steel, and it is necessary to contain 10.5 mass% or more in order to ensure a sufficient corrosion resistance. On the other hand, 15. Qmass 0/0 forte containing, Workability and toughness are reduced. Therefore, Cr is limited to the range of 10. 5-15. (Ma 0 / 0. 'In addition, the corrosion resistance is more than 11.5mass% from 3 ⁇ 4m ⁇ and toughness is secured from 3 ⁇ 4 ⁇ to 1.Omass. It is preferable to be less than%.
- Ni improves H “corrosion” 14 and also causes Q: carbide precipitation at high temperatures of 650 ° C. 3 ⁇ 41 to suppress the decrease in hardness of the C3 ⁇ 4i 'saturation ⁇ ⁇ ”ite phase; 3 ⁇ 4 L soft t «t is improved. In addition, it improves the corrosion resistance of stainless steel and contributes to improved toughness p. The effect was observed at an excitement of 0. lmass% or higher; 1 ⁇ 2. However, even if 2. Qmass% ⁇ is added, the following effect is improved; 3 ⁇ 4 L softening resistance is improved, and 5 effects are reduced in content, so it is limited to 2. Qmass% or less. In addition, from the viewpoint of improving the [3 L softness], it is preferable to add 0.0.
- Cu is baked L3 ⁇ 4S 1? In this case, it is applied to the paper weave.
- 3 ⁇ 4 (It is an element that precipitates in Tsuruta as ⁇ -Cu on ⁇ , and improves its soft resistance by K. It is necessary to add 0.5 mass% to the surface, but 4. Adding Qmass% 3 ⁇ 4 ⁇ will lead to deterioration of fertility, so ⁇ is more than 0.5 to 4.
- Qmass% From the point of securing toughness, it is preferable to contain less than 1.5% s%.
- Nb is an element that, when heated to ⁇ ⁇ , 650 ° C @, forms a carbonitride and hardens out, and improves the caustic 3 ⁇ 45 ⁇ . In order to achieve this effect, there is a necessary force S of 0.02 mass% or more. On the other hand, Nb is limited to the range of 0.02-0. 3 mass% because the toughness decreases when excited by 0.3 mass%. It is preferable to improve softness. 08mass%, more preferably 0.llmass 0 / o or more of no power to splice. However, from the standpoint of ensuring toughness, it is preferably 0.2 mass% or less. .
- N is an element that increases the hardness of later steel.
- ⁇ is a C-type compound (Q3 ⁇ 4 formed in the range of 500-700 ° C and its precipitation hardening action; There are fruits.
- excessive drought of N leads to a decrease in toughness, so it is necessary to limit it to less than 0. lmass%.
- the formula (1) is excellent, and the condition to secure ⁇ A stable life is 3 ⁇ 43 ⁇ 41 ⁇ .
- excellent ⁇ x stable 14 means that the stenite region and; ⁇ the range force s is wide; when heated—the stenite ( ⁇ ) phase is 75 Y ol% or more ⁇ 3 ⁇ 4, and it stirs with St that is ⁇ Kair cooling or more. When done, this means that it transforms into the austenite phase force s Manoto phase and is stable for a certain time; 3 ⁇ 4 ⁇ ⁇ _1 force s.
- the power value on the left side is 5 or higher, the austenite phase is 75 vol% or higher when heated, or the Si range becomes extremely ⁇ and stable; 1 ⁇ 2A1 ⁇ 2g cannot be secured.
- the value on the left side of equation (1) must be restricted to less than 45. '
- Equation (2) is A strong correlation with the contents of C and N is fe3 ⁇ 4. However, C and N combined with Nb and carbonitride ⁇ F ⁇ contribute to the improvement of the hardness of 1 ⁇ 2 ⁇ ⁇ . Therefore, the hardness of! 3 ⁇ 4 ⁇ 1 ⁇ 2 is calculated by subtracting the total C, N * 3 ⁇ 4 and 3 ⁇ 4W amount of C and N in the steel.
- Intermediate term ⁇ C + N— (13/93) Nb ⁇ It is necessary to think in. If the value of the intermediate term in equation (2) is less than 0.03, the hardness force of! ⁇ A l ⁇ will be less than 3 ⁇ 4RC: 32, conversely, if it is 0.09, the hardness will exceed HRC: 38. become.
- the brake disc of the present invention can apply the following components in addition to the above-described components:
- Both Mo and Co are components that are excellent in improving corrosion resistance, and can be added in an amount of 0.01 mass% or more as required.
- MO has a great effect of suppressing the precipitation of carbonitrides and improving firing.
- the improvement effect of knee resistance of Mo can be sufficiently 5 even if it is less than 0.05 mass%. Even if Mo contains 1. Qmass% and Co contains 1. Qmass% 3 ⁇ 4®, Mo and Co corrosion resistance improving effect Mo calcination L $ ⁇ pile improving effect is saturated. Therefore, the upper limit is preferably 2.
- Ti 0.02 ⁇ 0.3mass%
- V 0.02 ⁇ 0.3mass%
- Zr 0.02—0.3.s%
- Ta 0.02 ⁇ 0.3m ass%
- Ti, V, Zr and Ta are all elements that precipitate carbonitride 3 ⁇ 4f and increase! 3 ⁇ 4 L $: feib «: Depending on the situation, it can be burned.
- This effect of increasing the ML softness can be achieved with an additive of 0.02 mass% or more for each of Ti, V, Zr and other elements.
- the effect of V is large, so V is 0.05 mass. /.
- Ti, V, Zr and Ta are Ti: 0.02 ⁇ 0.3mass%, V..02 ⁇ 0.3mass% Zr: 0.02 ⁇ 0.3mass%, Ta: 0.02— it forces preferably ⁇ in the range of 0. 3mass 0/0.
- B and Ca are effective in increasing the amount of steel and the toughness of the steel, and if necessary, it can be applied B over 0005 mass%. However, even if ⁇ Te 0. 0050mass 0/0 3 ⁇ 4r3 ⁇ 4i, except that the effect is saturated, so also reduces the corrosion resistance, It is preferable to set the upper limit to 005Qmass%. ⁇ .
- the brake disc of the present invention comprises Fe and unavoidable impurities other than the above components.
- I, P, S and A1 as inevitable impurities are preferably in the following ranges.
- P 0. 0 mass ° /. Less than P is an element that reduces hot workability, and is preferably as fine as possible. However, it is preferable that the upper limit is 0. O4mass 0 / o, because ii3 ⁇ 4P ′ ⁇ causes an increase in cost. Furthermore, from 3 ⁇ 4 ⁇ to ensure heat ductility, 3 ⁇ 4). It is better than S to have 03ma SS % or less.
- S like P, is preferred for lower levels to reduce hot workability! /, But because of the trade-off between cost and S cost-0 ⁇ 010 mass% or less S preferable.
- the S content is more preferably 0.005 mass% or less.
- A1 is an element added as a deoxidizer, but remains as an impurity in X, and corrosion resistance, toughness ("raw and surface degenerate state, ⁇ hatching. Therefore, A1 it forces preferably be limited to 0. 2ma SS% or less, in order 3 ⁇ 4 further sufficient corrosion '13 ⁇ 4 is, 0. 05mass% or less is more preferable.
- the break disk of the present invention includes Na, L thin alkali males, alkaline earth metal such as Mg and Ba, rare i ⁇ elements such as Y and La, and Hf as components of the above inevitable impurities. Even if it contains less than lO.05mass% of T, etc., this does not interfere with the effect of this statement.
- Old millet flat 8 ⁇ m or more
- the material integrity of the material key (mano ⁇ Ito-type stainless steel plate) is in the above range; as described above, the hardness of ⁇ ⁇ ⁇ can be controlled in the range of HRC: 32 to 38. it can. But in addition, 650. Even after the lhr ⁇ f ⁇ b key in C, even if HRC: 30 or more can be secured; 3 ⁇ 4 To have L softness, the average particle size of the old y grain is It must have a mano: / ⁇ ite thread ridge of 8 ⁇ or more.
- the average grain size of the old grains is less than 8 / zm *, there are few fine precipitates precipitated in the old ⁇ grains; Whether the resistance to softening and the softening resistance to be more stable and to maintain T3 ⁇ 4 is not less than 10 ⁇ m.
- the strength of the old milled grains is preferably 10 zm or more, more preferably 15 ⁇ or more.
- the old ⁇ difficulty is 30 m, the fracture surface unit of brittle fecture increases and the toughness decreases, so the old ⁇ grain size is preferably 30 or less. ; Zelade of ⁇ A l ⁇ Nb3 ⁇ 4 ⁇ Nb: 0 less than 75.
- the brake disc of the present invention has a heel after lap treatment of lhr ⁇ T at 650 ° C, and has a 3 ⁇ 43 ⁇ 43 ⁇ 4 L3 ⁇ 4bffi: at 30 or more in HRC.
- Nb ⁇ / ⁇ Nb amount must be less than 0.75. If the (precipitation 3 ⁇ 4 * ⁇ b *) of; ⁇ is 0.75 or more, the amount of Nb that forms a solid solution in the grains is small and sufficient! 3 ⁇ 4 Soft softness is low. Because. In order to obtain a higher tempering L $ -depleted defect, (the amount of precipitated Nb3 ⁇ 4 ⁇ Nb) is preferably a force S of 0.5 or less, more preferably 0.4 or less.
- the brake disc of the present invention needs to have a hardness of! ⁇ A l ⁇ in the range of 32 to 38 in 3 ⁇ 4RC.
- the dislocation density p inherent in the mannosite structure of the fired brake disc is required.
- flat facilities of ( ⁇ ⁇ ) is, 0. '8 ⁇ 10 8 ⁇ 1. is preferably 3 ⁇ 103 ⁇ 4 ⁇ one 1.
- the brake disc of the present invention preferably has a hardness after calcination at 650 ° C. of lhri3 ⁇ 4f1 to 30 or more in HRC.
- the square root of dislocation density ⁇ (T p) is 0.6
- X io 8 ⁇ i. 3x ⁇ 3 ⁇ 4 ⁇ force transducer preferable that a range of one 1.
- the upper density after 1 ⁇ 2 U is difficult to deposit in Cu «field at ⁇ L.
- the steel / key-type stainless steel key is made of steel that is suitable for the component component, usually in the manner of P (eg, 3 ⁇ 4) steel converter) or electric tace) etc.
- VOD Vauum Oxygen Deca burization
- AOD Argon Oxygen Decarbu
- the ingot lump method i3 ⁇ 4 ⁇ ⁇ ntinu 0 us cas is generally used as a method for producing steel materials. However, from the viewpoint of productivity and quality, the method is preferred.
- the brake disc material can be a stainless steel plate, a cold plate, or misalignment.
- the thermal reaction of W is 3 to & nm ⁇ li, and the power S is large.
- the upper material is reheated to 1100-125 ° C and then hot-rolled to form a predetermined hot metal strip (key), and if necessary, a batch furnace, etc. Therefore, it is preferable to heat the steel for 10 hours at a temperature of more than 750 ° C to 900 ° C and use it as a material for brake discs. Further, if necessary, a scale such as acid blasting may be performed.
- the thickness is 0mmS3 ⁇ 4, so generally cold-rolled steel sheets are used; ⁇ . This is 600-800 after further cold rolling the above hot rolled steel strip). After C, if necessary, further acid refuge is performed and used as a disc material!
- the ⁇ region is a region in which the fraction of austenitic H is 75 vol% or more.
- the hardness of ⁇ 3 ⁇ 4 ⁇ ⁇ can be kept within the range of 3 ⁇ 41 (H C32 ⁇ 38) and the former 0; the grain flatness is 8 m or more and Z or (precipitation ⁇ Nb *) 3 ⁇ 40.
- the temper- ature is improved by K, and even with # ⁇ which has been tempered for lhr 1 at a high temperature of 650 ° C, it can suppress the decrease in hardness.
- the force is less than SlOOO ° C
- the time may be lengthened, the old ⁇ grain size may be increased, and / or this may reduce the amount of precipitated N and improve softness.
- the temperature is below the Ms point (manoite & 3 ⁇ 4 dnartsitc transfonnation starting temperature)) on CZsec3 ⁇ 4, preferably below 200 ° C.
- the brake disc of the manotype stainless steel rod of the present invention has a hardness force in the range of RC: 32 to 38, and the average grain size of the old grains is more and / or (Deposited Nb amount Since / ⁇ b4) is less than 0.75, it has excellent strength that it can maintain a hardness of HRC: 30 or more even after baking at 650 ° C for lhrf3 ⁇ 4 T.
- Stainless steel is beaten in a high-frequency melting furnace (frequency meMngiimace), sickleed to 50 lumps, and then hot rolled under normal ⁇ P conditions to a thickness of 5 mm In the reducing atmosphere, the thermal stress of 80 0.
- the CX8hr job was gradually cooled after being heated, and the scale on the surface was removed with difficulty, and the heat excavation of ⁇ 1 ⁇ was taken as a boat sickle plate, and a sample of X3QmmX30mm was collected.
- Table 2 For this test of ⁇ , observe the male crane and measure the amount of precipitated N, as described below; 3 ⁇ 4A L stability ⁇ ,; ⁇ ⁇ and calcination of ⁇ ⁇ ⁇ and standing density after calcination :: In Table 2-1 to 3, “the highest in the y region?” Is the highest generated austenite) force S75vol%. Above this, the 5-phase (ferrite phase) force S increases. This means that the ⁇ phase cannot be secured at 75 vol% or more.
- the above ⁇ is further heated at 3 ⁇ 4650 ° C, heated for FL for the time shown in Table 2 ⁇ , and then emptied 3 ⁇ 4L ⁇ before removing the surface scale. Then, work on JIS Z2245 and measure the Rockure hardness tester “ ⁇ surface hardness (HRC) 5 points at a time, find the average value, and if the hardness force 3 ⁇ 4RC: 30 or more, sufficient firing M MMft T, say ffiU 'Measure dislocation density>
- the dislocation density p is determined from the above ⁇ ⁇ specimen and ⁇ i ⁇ after firing at 650 ° C.
- the technology of the present invention requires a high stake soft pile; 1 ⁇ 2, turbid ⁇ etc .; ⁇ »resistant, can be adapted to the field of high bow daughter steel used for springs, etc. .
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Abstract
Description
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Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP06811655A EP2011891A1 (en) | 2006-04-21 | 2006-10-05 | Brake disc having high temper softening resistance |
US12/297,091 US20090162240A1 (en) | 2006-04-21 | 2006-10-05 | Brake disk having high temper softening resistance |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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JP2006117375A JP5200332B2 (ja) | 2005-04-21 | 2006-04-21 | 焼戻し軟化抵抗の大きいブレーキディスク |
JP2006-117375 | 2006-04-21 |
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Publication Number | Publication Date |
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WO2007122754A1 true WO2007122754A1 (ja) | 2007-11-01 |
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PCT/JP2006/320358 WO2007122754A1 (ja) | 2006-04-21 | 2006-10-05 | 焼戻し軟化抵抗の大きいブレーキディスク |
Country Status (6)
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US (1) | US20090162240A1 (ja) |
EP (1) | EP2011891A1 (ja) |
KR (1) | KR20080110623A (ja) |
CN (1) | CN101426941A (ja) |
RU (1) | RU2008141688A (ja) |
WO (1) | WO2007122754A1 (ja) |
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WO2022176707A1 (ja) | 2021-02-18 | 2022-08-25 | 日鉄ステンレス株式会社 | ブレーキディスクローター用マルテンサイト系ステンレス鋼板、ブレーキディスクローターおよびブレーキディスクローター用マルテンサイト系ステンレス鋼板の製造方法 |
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- 2006-10-05 US US12/297,091 patent/US20090162240A1/en not_active Abandoned
- 2006-10-05 KR KR1020087025090A patent/KR20080110623A/ko not_active Application Discontinuation
- 2006-10-05 EP EP06811655A patent/EP2011891A1/en not_active Withdrawn
- 2006-10-05 CN CNA2006800543001A patent/CN101426941A/zh active Pending
- 2006-10-05 RU RU2008141688/02A patent/RU2008141688A/ru not_active Application Discontinuation
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US9752143B2 (en) | 2013-03-15 | 2017-09-05 | MiRagen Therapeutics, Inc. | Locked nucleic acid inhibitor of miR-145 and uses thereof |
WO2022176707A1 (ja) | 2021-02-18 | 2022-08-25 | 日鉄ステンレス株式会社 | ブレーキディスクローター用マルテンサイト系ステンレス鋼板、ブレーキディスクローターおよびブレーキディスクローター用マルテンサイト系ステンレス鋼板の製造方法 |
KR20230144607A (ko) | 2021-02-18 | 2023-10-16 | 닛테츠 스테인레스 가부시키가이샤 | 브레이크 디스크 로터용 마르텐사이트계 스테인리스 강판, 브레이크 디스크 로터 및 브레이크 디스크 로터용 마르텐사이트계 스테인리스 강판의 제조 방법 |
Also Published As
Publication number | Publication date |
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CN101426941A (zh) | 2009-05-06 |
EP2011891A1 (en) | 2009-01-07 |
KR20080110623A (ko) | 2008-12-18 |
RU2008141688A (ru) | 2010-04-27 |
US20090162240A1 (en) | 2009-06-25 |
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