WO1995010635A1 - Procede de production d'acier de forgeage a chaud presentant d'excellentes caracteristiques de resistance a la fatigue et a la deformation et une tres bonne aptitude a la coupe - Google Patents
Procede de production d'acier de forgeage a chaud presentant d'excellentes caracteristiques de resistance a la fatigue et a la deformation et une tres bonne aptitude a la coupe Download PDFInfo
- Publication number
- WO1995010635A1 WO1995010635A1 PCT/JP1994/001694 JP9401694W WO9510635A1 WO 1995010635 A1 WO1995010635 A1 WO 1995010635A1 JP 9401694 W JP9401694 W JP 9401694W WO 9510635 A1 WO9510635 A1 WO 9510635A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- steel
- machinability
- strength
- ratio
- hot forging
- Prior art date
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
-
- 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
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
-
- 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
- C21D2211/005—Ferrite
Definitions
- the present invention relates to a method for producing steel for machine structures such as automobiles by hot forging, and more particularly, to forging a steel material having a specific chemical composition into a specific metallographic structure.
- the present invention relates to a method for manufacturing a hot forged steel that can have excellent fatigue strength, machinability and yield strength simultaneously by performing aging treatment.
- the machinability is extremely deteriorated by increasing the tensile strength, and if the tensile strength exceeds 120 kgf / mm 2 , production can no longer be performed at normal production efficiency. Therefore, the realization of a non-heat treated steel that improves the fatigue strength without deteriorating the machinability has been desired.
- the endurance ratio is at most about 0.55 It can be improved at most to twice that of conventional non-heat treated payinite steel, which has extremely poor machinability.
- the present inventors first examined the fatigue properties and machinability of several types of hot forgings having a metal structure in which an appropriate amount of veneite structure was mixed in the ferrite structure. (2) low C and low N, (3) phenylite + painite precipitation of V carbide in two-phase structure, improving tensile strength and fatigue strength and improving machinability
- the tensile strength and the fatigue strength are improved in the steel having a transformed payinite structure, but the yield strength and the yield ratio are significantly reduced. Because of these problems, it has been particularly difficult to apply this technology to engine parts related to automobiles that are subject to large loads on an irregular basis.
- the present invention is directed to the production of a hot forged steel having high tensile strength, fatigue strength and yield strength, and also having good machinability at the same time, which was difficult to achieve with conventional steel hot forged steel. It provides a method.
- the yield strength is equal to the stress that initiates plastic deformation.
- the yield strength of the soft phase is mainly affected. Since the ferrite phase completes the transformation at a relatively high temperature, the amount of solute C and N is smaller than that of the bainite phase, which is a low-temperature transformation phase, so that an increase in yield strength due to aging cannot be expected.
- the inventors of the present invention have performed a aging treatment in a specific temperature range on a fluoride + painite structural steel having a specific chemical composition, thereby increasing the tensile strength, fatigue strength, and yield strength.
- the present invention has been completed to provide an ideal method of manufacturing hot forging with good machinability.
- C 0.10 to 0.35%
- Si 0.15 to 2.00%
- Mn 0.40 to 2.00%
- S 0 in terms of weight ratio. .03 ⁇ 0.10%
- Ti 0.003 ⁇ 0.05%
- N 0.0002 ⁇ 0.0070%
- V 0.30 ⁇ 0
- Cr 0.02 to 1.50%
- Mo is added to the composition of the first invention steel in order to refine the crystal grains, adjust the proportion of the paneite structure, and further improve the machinability.
- Nb 0.001 to 0.20%
- Pb 0.05 to 0.30%
- Ca 0.0005 0. in which was contained on one or more kinds of the 0 10%.
- Si an element that adjusts the deoxidation and bainite structure ratio. The effect of is small, and if it exceeds 2.00%, both the durability ratio and machinability decrease, so it is set to 0.15 to 2.00%.
- Mn An element that becomes the basis of composite precipitates, which are the precipitation sites of the fly by adjusting the bainite structure ratio and becoming Mn S. If the content is less than 0.40%, the effect is small, and 2.00% If it is excessive, a large amount of martensite will be generated, and both the durability ratio and machinability will decrease, so it is set to 0.40 to 2.00%.
- a 1 Element with deoxidizing and crystal grain refining effects. Less than 0.0005%, the effect is small, and if over 0.05%, hard inclusions are formed and durability ratio and machinability are low. Therefore, it is 0.0005 to 0.05%.
- T i an element that forms a complex precipitate that precipitates as nitride on MnS and forms a ferrite deposition site. Its effect is small at less than 0.003%, and less than 0.05%. Since the formation of coarse hard inclusions is promoted, and both the durability ratio and machinability are reduced, the content is 0.003 to 0.05%.
- N An element that forms a nitride or carbonitride with Ti and V. If it is less than 0.0020%, its effect is small, and if it exceeds 0.0070%, both the durability ratio and machinability are reduced. 0020 to 0.0070%.
- V An element that forms complex precipitates with MnS and TiN and strengthens the precipitation of matrix frit in bainite. If it is less than 0.30%, its effect is small, and if it exceeds 0.70%, its effect is small. Since both the durability ratio and machinability decrease, the range is 0.30 to 0.70%.
- the components of the first invention steel further include Cr, Mo, Nb, Pb, and C
- Cr, Mo, Nb, Pb, and C One or more types are contained. The reasons for limiting these chemical components are described below.
- Mo An element that has almost the same effect as Mn and Cr. If it is less than 0.02%, its effect is small. If it exceeds 1.00%, a large amount of martensite is generated, and both the durability ratio and machinability are high. Since it decreases, it is set to 0.02 to 1.00%.
- Nb An element that has almost the same effect as Ti and V. If it is less than 0.001%, its effect is small, and if it exceeds 0.20%, both the durability ratio and machinability decrease. 00 1 to 0.20%.
- Pb An element that improves machinability. If its content is less than 0.05%, its effect is small, and if it exceeds 0.30%, its effect is saturated and its fatigue strength and durability ratio decrease. %.
- C a an element having almost the same effect as Pb. If it is less than 0.0005%, the effect is small. If it exceeds 0.010%, the effect is saturated and the fatigue strength and durability ratio decrease. ⁇ 0.0 10%.
- the metal structure of the steel according to the present invention when the steel is cooled after hot forging and the transformation is completed.
- 80% or more of the metal structure is filled. + It is necessary to be a two-phase organization of perlite. Even if perlite, martensite, or residual austenite with a texture ratio of less than 20% does not hinder this effect.
- the cooling method after hot forging is not specified, but natural cooling is naturally desirable from the viewpoint of equipment and manufacturing costs.
- the metal structure shall be confirmed by observing the corroded test specimen with an optical microscope or by measuring the microhardness of the structure with a Vickers hardness tester with a microphone.
- the heating temperature for the aging treatment is set to 200 to 700 ° C.
- the time is not particularly limited as long as it is within this temperature range, but preferably should be about 10 minutes to 2 hours.
- the performance of the present invention can be obtained by any cooling method after aging treatment, such as air cooling, water cooling, or oil cooling.
- a cutting test piece was taken from the same material, and a 30 mm deep blind hole was drilled using an SKH 9 l O mm 0 straight shank drill. The sex was evaluated. The cutting speed was 5 Om / min, the feed rate was 0.35 mm / rev, and the cutting oil was 7 L / min.
- Table 2 shows the bainite microstructure ratio and performance evaluation results of each test material.
- the durability ratio of tempered steel No. 42 was 0.47 and the machinability was 1.00, whereas the durability ratio of all Nos. 1 to 20 of the present invention was 0.56 or more. Its properties are as good as 2-3 times that of No. 42.
- No. 21 of the comparative example has low fatigue strength because of low C content and low tensile strength and low durability ratio.
- Comparative Example No. 22 since the amount of C was too high, martensite was generated and the condition of ferrite + painite texture ratio of the present invention could not be satisfied, and the tensile strength was high but the durability ratio was lower than that of the present invention. The machinability is also poor.
- Comparative Example No. 23 since the amount of Si was low, the degree of deoxidation was low and the durability ratio was lower than that of the present invention. In Comparative Example No. 24, since the amount of Si was high, martensite was generated, and the condition of the ratio of the structure of the furite + painite of the present invention could not be satisfied. .
- Comparative Example No. 25 since the amount of Mn was low, the precipitation of composite precipitates was small, and the durability ratio was low. It is lower than the present invention. In Comparative Example No. 26, since the amount of Mn was high, martensite was generated and the condition of ferrite + painite structure ratio of the present invention could not be satisfied, and the durability ratio was lower than that of the present invention and the machinability was poor.
- Comparative Example No. 27 since the amount of S was low, the precipitation of composite inclusions was small, the durability ratio was lower than that of the present invention, and the machinability improvement effect of MnS was not obtained, so the machinability was poor.
- No. 28 of the comparative example the amount of S was high, so that the precipitation of MnS was excessive, and the durability ratio was lower than that of the example of the present invention.
- No. 31 of the comparative example has a low Ti content, so that precipitation of composite precipitates is small, and the durability ratio is lower than that of the inventive example.
- No. 32 of the comparative example had a high Ti content, so that a hard inclusion was formed, and the durability ratio was lower than that of the inventive example, and the machinability was poor.
- N 0.33 of the comparative example has a low N content, so that the precipitation of composite precipitates is small, and the durability ratio is lower than that of the present invention.
- the matrix was hardened due to the high N content, and the durability ratio was lower than that of the inventive example, and the machinability was poor.
- N 0.35 of the comparative example has a low V content, so that the precipitation of composite precipitates is small and the effect of strengthening the precipitation of matrix ferrite is small, so that the durability ratio is lower than that of the present invention.
- Comparative Example No. 36 since the amount of V was high, the durability ratio was lower than that of the present invention, and the machinability was poor.
- Example 4 shows the bainite microstructure ratio and performance evaluation results of each test material. Nos. 43, 44, 45 and 46 satisfy the conditions of the present invention, with the ratio of fly + bainite organization being 0.8 or more, and all of them have a durability ratio of 0.56 or more.
- the machinability is also 2.5 times better than that of the currently tempered steel No. 48.
- No. 47 has a structure mainly composed of martensite by increasing the cooling rate. Although the tensile strength is high, the durability ratio is extremely low, and the tool life is short due to poor machinability. Table 3
- Comparative steel Current preparation K material Tempered, water cooled
- Example 2 Steel of the same chemical composition as in Example 2 was melted in a high-frequency furnace to form a 15 O kg steel ingot.From this, a forging material was cut out, and was once 95 (normalized by TC heating and cooling, then 1100 to 1250 ° The material was heated to C and hot forged at a temperature of 1050 to 1200 ° C, and then allowed to cool, and further charged in a heating furnace at the temperature shown in Table 5 for 1 hour to perform aging treatment. A tensile test, a fatigue test, a cutting test, and a metallographic observation were performed on the material No. 1 in the same manner as in Example 1. Table 6 shows the performance evaluation results of the test materials.
- Nos. 50, 51 and 52 satisfy the aging temperature range of the present invention, 200 to 700 ° C, and all have a durability ratio of 0.58 or more, and are machinable at the present time. Almost 2.5 times better than No. 54.
- No. 49 is the case where the aging temperature was below the range of the present invention, and the durability ratio was inferior. In No. 53, the aging temperature exceeded the range of the present invention, and the durability ratio was poor. Table 5
- the steel of the present invention obtains a high tensile strength and secures machinability by forming a ferrite ten-benite two-phase structure, and further obtains MnS, Ti nitride and V nitride. Simultaneously refines the metallographic structure and strengthens the fulite matrix in veneite with V carbides (or carbonitrides) using the composite precipitates formed from
- the present invention provides an extremely ideal hot forged steel manufacturing method capable of obtaining even higher yield strength by performing the treatment, and has an industrially significant effect L.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Heat Treatment Of Steel (AREA)
Description
Claims
Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR1019950702390A KR0180939B1 (ko) | 1993-10-12 | 1994-10-11 | 피로강도, 항복강도 및 피삭성이 우수한 열간 단조 강의 제조방법 |
EP94929027A EP0674012A4 (en) | 1993-10-12 | 1994-10-11 | PROCESS FOR PRODUCING HOT FORGING STEEL HAVING EXCELLENT CHARACTERISTICS OF RESISTANCE TO FATIGUE AND DEFORMATION AND A VERY GOOD CUTTING ABILITY. |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP5/254333 | 1993-10-12 | ||
JP25433393A JP3300500B2 (ja) | 1993-10-12 | 1993-10-12 | 疲労強度、降伏強度および被削性に優れる熱間鍛造用鋼の製造方法 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO1995010635A1 true WO1995010635A1 (fr) | 1995-04-20 |
Family
ID=17263555
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP1994/001694 WO1995010635A1 (fr) | 1993-10-12 | 1994-10-11 | Procede de production d'acier de forgeage a chaud presentant d'excellentes caracteristiques de resistance a la fatigue et a la deformation et une tres bonne aptitude a la coupe |
Country Status (6)
Country | Link |
---|---|
US (1) | US5601667A (ja) |
EP (1) | EP0674012A4 (ja) |
JP (1) | JP3300500B2 (ja) |
KR (1) | KR0180939B1 (ja) |
CN (1) | CN1039033C (ja) |
WO (1) | WO1995010635A1 (ja) |
Cited By (16)
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WO2005089829A2 (en) | 2004-03-10 | 2005-09-29 | Scil Technology Gmbh | Coated implants, their manufacturing and use thereof |
EP1719532A2 (en) | 1997-03-20 | 2006-11-08 | Stryker Corporation | Osteogenic devices and methods of use thereof for repair of bones |
US7147839B2 (en) | 1998-05-29 | 2006-12-12 | Curis, Inc. | Methods for evaluating tissue morphogenesis and activity |
WO2008082563A2 (en) | 2006-12-21 | 2008-07-10 | Stryker Corporation | Sustained-release formulations comprising crystals, macromolecular gels, and particulate suspensions of biologic agents |
EP1988395A1 (en) | 1997-05-30 | 2008-11-05 | Curis, Inc. | Methods for evaluating tissue morphogenesis and morphogenic activity |
US7575751B2 (en) | 2004-04-27 | 2009-08-18 | Research Development Foundation | Activin-A mutants |
WO2009102966A2 (en) | 2008-02-13 | 2009-08-20 | Keith Hruska | Method of treating vascular sclerosis |
WO2010093941A2 (en) | 2009-02-12 | 2010-08-19 | Stryker Corporation | COMPOSITIONS AND METHODS FOR MINIMALLY-INVASIVE SYSTEMIC DELIVERY OF PROTEINS INCLUDING TGF-β SUPERFAMILY MEMBERS |
WO2010093925A2 (en) | 2009-02-12 | 2010-08-19 | Stryker Corporation | PERIPHERAL ADMINISTRATION OF PROTEINS INCLUDING TGF-β SUPERFAMILY MEMBERS FOR TREATMENT OF SYSTEMIC DISORDERS AND DISEASE |
WO2010110974A1 (en) | 2009-03-24 | 2010-09-30 | Stryker Corporation | Methods and compositions for tissue engineering |
WO2010144696A1 (en) | 2009-06-11 | 2010-12-16 | Burnham Institute For Medical Research | Directed differentiation of stem cells |
WO2011031856A1 (en) | 2009-09-09 | 2011-03-17 | Stryker Corporation | Bmp -7 for use in treating pain induced by injuries and diseases of an articular joint |
EP2298335A1 (en) | 2004-05-25 | 2011-03-23 | Stryker Corporation | Use of morphogenic proteins for treating cartilage defects |
WO2011035094A1 (en) | 2009-09-17 | 2011-03-24 | Stryker Corporation | Buffers for controlling the ph of bone morphogenetic proteins |
WO2011087768A1 (en) | 2009-12-22 | 2011-07-21 | Stryker Corporation | Bmp-7 variants with reduced immunogenicity |
EP2540310A1 (en) | 2006-05-17 | 2013-01-02 | Stryker Corporation | Methods of treating cartilage defects using a soluble morphogenic protein complex |
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DE19639062A1 (de) * | 1996-09-16 | 1998-03-26 | Mannesmann Ag | Modellgestütztes Verfahren zur kontrollierten Kühlung von Warmband oder Grobblech in einem rechnergeführten Walz- und Kühlprozeß |
JP3888865B2 (ja) * | 2000-10-25 | 2007-03-07 | 株式会社ゴーシュー | 鍛造方法 |
KR20020094603A (ko) * | 2001-06-12 | 2002-12-18 | 현대자동차주식회사 | 링기어와 드라이브 피니언의 고강도 침탄 강재 및 그제조방법 |
JP5200634B2 (ja) * | 2007-04-11 | 2013-06-05 | 新日鐵住金株式会社 | 鍛造及び浸炭用熱間圧延棒鋼 |
JP5815946B2 (ja) * | 2008-12-25 | 2015-11-17 | 日立金属株式会社 | 鋼の焼入方法 |
WO2010090238A1 (ja) * | 2009-02-04 | 2010-08-12 | 住友金属工業株式会社 | 時効硬化性鋼および機械部品の製造方法 |
BR112014009103A2 (pt) * | 2011-10-19 | 2017-04-18 | Jfe Steel Corp | material de camada de superfície de rolo para laminação a quente com excelente resistência à fadiga produzido por fundição centrífuga e rolo compósito para laminação a quente produzido através de fundição centrífuga |
JP5825199B2 (ja) * | 2012-05-24 | 2015-12-02 | 新日鐵住金株式会社 | 時効硬化性鋼および機械部品の製造方法 |
US20140283960A1 (en) * | 2013-03-22 | 2014-09-25 | Caterpillar Inc. | Air-hardenable bainitic steel with enhanced material characteristics |
JP5880795B2 (ja) * | 2013-10-02 | 2016-03-09 | 新日鐵住金株式会社 | 時効硬化性鋼 |
KR101449511B1 (ko) * | 2014-07-29 | 2014-10-13 | 한국기계연구원 | 가공 경화형 항복비 제어강 및 그 제조방법 |
PL3168312T3 (pl) * | 2015-11-16 | 2019-09-30 | Deutsche Edelstahlwerke Specialty Steel Gmbh & Co. Kg | Stopowa stal konstrukcyjna o strukturze bainitycznej, wytworzony z niej element kuty i sposób wytwarzania elementu kutego |
CN106480279B (zh) * | 2016-12-28 | 2018-01-02 | 长春实越节能材料有限公司 | 一种提高高氮钢石油钻铤表面耐腐蚀耐磨损的方法 |
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JPH04285118A (ja) * | 1991-03-13 | 1992-10-09 | Nippon Steel Corp | 高強度高靭性熱間鍛造非調質鋼の製造方法 |
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- 1993-10-12 JP JP25433393A patent/JP3300500B2/ja not_active Expired - Fee Related
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1994
- 1994-10-11 CN CN94190782A patent/CN1039033C/zh not_active Expired - Fee Related
- 1994-10-11 KR KR1019950702390A patent/KR0180939B1/ko not_active IP Right Cessation
- 1994-10-11 WO PCT/JP1994/001694 patent/WO1995010635A1/ja not_active Application Discontinuation
- 1994-10-11 EP EP94929027A patent/EP0674012A4/en not_active Ceased
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- 1995-06-08 US US08/454,138 patent/US5601667A/en not_active Expired - Fee Related
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JPS60208414A (ja) * | 1984-03-31 | 1985-10-21 | Kobe Steel Ltd | 直接焼入れ熱間鍛造品の製造方法 |
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Cited By (18)
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EP1719532A2 (en) | 1997-03-20 | 2006-11-08 | Stryker Corporation | Osteogenic devices and methods of use thereof for repair of bones |
EP1719531A2 (en) | 1997-03-20 | 2006-11-08 | Stryker Corporation | Osteogenic devices and methods of use thereof for repair of bones |
EP1988395A1 (en) | 1997-05-30 | 2008-11-05 | Curis, Inc. | Methods for evaluating tissue morphogenesis and morphogenic activity |
EP2309261A1 (en) | 1997-05-30 | 2011-04-13 | Stryker Corporation | Methods for evaluating tissue morphogenesis and morphogenic activity |
US7147839B2 (en) | 1998-05-29 | 2006-12-12 | Curis, Inc. | Methods for evaluating tissue morphogenesis and activity |
WO2005089829A2 (en) | 2004-03-10 | 2005-09-29 | Scil Technology Gmbh | Coated implants, their manufacturing and use thereof |
US7575751B2 (en) | 2004-04-27 | 2009-08-18 | Research Development Foundation | Activin-A mutants |
EP2298335A1 (en) | 2004-05-25 | 2011-03-23 | Stryker Corporation | Use of morphogenic proteins for treating cartilage defects |
EP2540310A1 (en) | 2006-05-17 | 2013-01-02 | Stryker Corporation | Methods of treating cartilage defects using a soluble morphogenic protein complex |
WO2008082563A2 (en) | 2006-12-21 | 2008-07-10 | Stryker Corporation | Sustained-release formulations comprising crystals, macromolecular gels, and particulate suspensions of biologic agents |
WO2009102966A2 (en) | 2008-02-13 | 2009-08-20 | Keith Hruska | Method of treating vascular sclerosis |
WO2010093941A2 (en) | 2009-02-12 | 2010-08-19 | Stryker Corporation | COMPOSITIONS AND METHODS FOR MINIMALLY-INVASIVE SYSTEMIC DELIVERY OF PROTEINS INCLUDING TGF-β SUPERFAMILY MEMBERS |
WO2010093925A2 (en) | 2009-02-12 | 2010-08-19 | Stryker Corporation | PERIPHERAL ADMINISTRATION OF PROTEINS INCLUDING TGF-β SUPERFAMILY MEMBERS FOR TREATMENT OF SYSTEMIC DISORDERS AND DISEASE |
WO2010110974A1 (en) | 2009-03-24 | 2010-09-30 | Stryker Corporation | Methods and compositions for tissue engineering |
WO2010144696A1 (en) | 2009-06-11 | 2010-12-16 | Burnham Institute For Medical Research | Directed differentiation of stem cells |
WO2011031856A1 (en) | 2009-09-09 | 2011-03-17 | Stryker Corporation | Bmp -7 for use in treating pain induced by injuries and diseases of an articular joint |
WO2011035094A1 (en) | 2009-09-17 | 2011-03-24 | Stryker Corporation | Buffers for controlling the ph of bone morphogenetic proteins |
WO2011087768A1 (en) | 2009-12-22 | 2011-07-21 | Stryker Corporation | Bmp-7 variants with reduced immunogenicity |
Also Published As
Publication number | Publication date |
---|---|
KR0180939B1 (ko) | 1999-02-18 |
US5601667A (en) | 1997-02-11 |
CN1115581A (zh) | 1996-01-24 |
KR950704521A (ko) | 1995-11-20 |
CN1039033C (zh) | 1998-07-08 |
EP0674012A4 (en) | 1997-03-19 |
JP3300500B2 (ja) | 2002-07-08 |
EP0674012A1 (en) | 1995-09-27 |
JPH07109518A (ja) | 1995-04-25 |
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