JP2023035893A - Non-foamed molded body containing polyurethane - Google Patents

Abstract

To provide a molded body having excellent chipping resistance, and capable of stably exhibiting excellent cleaning performance.SOLUTION: There is provided a non-foamed molded body containing a polyurethane: in which a length of the longest line segment LM of a portion that overlaps with the molded body is at least 180 μm, on a straight line L that passes through a center of gravity G of the molded body and a point nearest to the center of gravity G, and penetrates the molded body; which satisfies HM2>HM3>HM4, and HM1 is 1.0 N/mm2 or more, where a Martens hardness at a point SA on a surface of the molded body at which one end A of the LM is located, is HM1, and Martens hardnesses at 3 points at every 30 μm interval from the end A on the LM toward the other end of the LM are HM2, HM3, and HM4, respectively; and in which, concerning an index value Kω obtained from a scattering profile that is obtained by directing a characteristic X-ray from a Cu tube at an incident angle θ to a to-be-evaluated surface region of the molded body including the point SA, the index value obtained by varying the incident angle θ indicates that a crystallinity index gradually decreases from the surface toward a depth direction.SELECTED DRAWING: Figure 1

Description

The present disclosure relates to non-foamed moldings containing polyurethane for use in cleaning stains on windows, floors, and the like.

The present disclosure relates to non-foamed moldings containing polyurethane that can be used for cleaning and the like.
Cleaning is carried out by bringing a rubber molded plate into contact with an object to be cleaned, such as a window glass of an automobile, a window glass of a building, a floor, an electrophotographic roller, or the like. Specifically, for example, wiper blades are made of various synthetic rubbers such as natural rubber, chloroprene rubber, and EPDM rubber (ethylene-propylene-diene rubber). Further, in electrophotographic apparatuses, polyurethane resin moldings are used as cleaning blades for the purpose of cleaning toner from rollers and the like.

In order to fully exhibit the cleaning effect, the surface of the rubber molded body that contacts the object to be cleaned is hardened. Japanese Patent Application Laid-Open No. 2004-200000 proposes a structure in which the inside of the cleaning blade has a lower hardness than the surface in order to achieve both a high surface hardness and followability to a roller, which is an object to be cleaned. More specifically, by impregnating a polyurethane molding with an isocyanate compound and allowing it to react, a hardened region is formed on the surface while keeping the inside of the cleaning blade flexible.
However, according to the study of the present inventors, as described in Patent Document 1, a rubber molded body (cleaning blade) having a high-hardness contact surface with an object to be cleaned has been used for a long period of time. In this case, the toughness of the hardened surface may be insufficient. In addition, fine chipping may occur on the surface of the rubber molding. As a result, the effect of cleaning the object to be cleaned by the rubber molding may be lowered.

Japanese Patent No. 5532376

One aspect of the present disclosure is directed to providing a molded article containing polyurethane that can stably exhibit superior cleaning performance over a long period of time while maintaining stable followability to an object to be cleaned. is.

According to one aspect of the present disclosure,
Assuming that a straight line L is drawn through the molded body through the center of gravity G of the molded body and a point on the surface of the molded body located closest to the center of gravity G, the The length of the longest line segment LM in the portion overlapping with the molded body is at least 180 μm,
Let _HM be the Martens hardness measured at the point SA on the surface of the compact where one end A of the line segment LM is located,
Martens hardness measured at three points every 30 μm from the end A on the line segment LM to the other end of the line segment LM in the cross section of the molded body including the entire length of the line segment LM When HM ₂ , HM ₃ and HM ₄ respectively,
_HM2 > _HM3 > _HM4 , and
The HM ₁ is 1.0 N/mm ² or more,
Regarding the index value K _ω obtained by the following formula (1) from the scattering profile obtained by making the characteristic X-ray from the Cu tube incident at the incident angle θ on the surface area to be evaluated of the molded body including the point SA , the index value when θ=0.5° is Kω1, the index value when θ=1.0° is _Kω2 , and the index value when θ=3.0° is _Kω3 , K _ω1 >K _ω2 >K _ω3 , and
_Kω =[ _Ic /( _Ic + _Ia )]×100 (1)
( _Ic is the peak area value of the scattering profile at 2θ=21.0°, and _Ia is the peak area value of the scattering profile at 2θ=20.2°), and
Provided is a compact having an erosion rate E of 0.6 μm/g or less measured using spherical alumina particles having an average particle diameter (D ₅₀ ) of 3.0 μm in the surface region to be evaluated.

According to one aspect of the present disclosure, it is possible to obtain a molded article containing polyurethane that can stably exhibit superior cleaning performance over a long period of time while maintaining stable followability to an object to be cleaned. can.

1 is a schematic diagram of a compact according to one aspect of the present disclosure; FIG. It is a figure which shows the measuring method of an erosion rate.

In the present disclosure, the descriptions of “XX or more and YY or less” or “XX to YY” representing numerical ranges mean numerical ranges including the lower and upper limits, which are endpoints, unless otherwise specified. Moreover, when a numerical range is described stepwise, the upper limit and lower limit of each numerical range can be combined arbitrarily.

<Non-foaming molding containing polyurethane>
FIG. 1 shows a schematic diagram of a non-foamed molding containing polyurethane according to one aspect of the present disclosure.
Assume that a straight line L passing through the molded body 11 and passing through the center of gravity G of the molded body 11 and a point on the surface of the molded body 11 located closest to the center of gravity G is drawn. In the molded article 11, the length of the longest line segment LM among the portions overlapping the molded article 11 on the straight line L is at least 180 μm. Further, a point SA is a point on the surface of the compact 11 where one end A of the line segment LM is located.

[How to determine the center of gravity]
Here, the center of gravity is a point obtained by taking the arithmetic mean of all points belonging to the outline of the compact. Multiple integration may be used as a general technique for finding the center of gravity based on such a definition. In addition, since the density of the compact of the present disclosure can be regarded as uniform, a method using the outer product of vectors may be applied. Since these calculation methods are generally known mathematical concepts, detailed descriptions thereof are omitted here.

As a result of studies by the present inventors, it was found that a non-foamed, that is, a solid molded article containing polyurethane satisfying the following conditions (1) to (4) has excellent chipping resistance and excellent cleaning performance. It has been found that a cleaning blade capable of exhibiting

(1) Let the Martens hardness measured at the point SA be HM ₁ , and in the cross section of the compact including the full length of the line segment LM,
Martens hardness measured at three points (P ₂ , P ₃ and P ₄ ) every 30 μm from the end A to the other end (end B) of the line segment LM on the line segment LM HM ₂ >HM ₃ >HM 4, where HM ₂ , HM ₃ and HM _{4 .}
(2) The HM ₁ is 1.0 N/mm ² or more.

(3) An index value obtained by the following formula (1) from a scattering profile obtained by making characteristic X-rays from a Cu tube incident at an incident angle θ on the surface area to be evaluated of the molded body including the point SA For _Kω ,
When the index value when θ=0.5° is K _ω1 , the index value when θ=1.0° is K _ω2 , and the index value when θ=3.0° is K _ω3 , K _ω1 >K _ω2 >K _ω3 .
_Kω =[ _Ic /( _Ic + _Ia )]×100 (1)
( _Ic is the peak area value of the scattering profile at 2θ=21.0°, and _Ia is the peak area value of the scattering profile at 2θ=20.2°.)
(4) The erosion rate E measured using spherical alumina particles having an average particle diameter (D ₅₀ ) of 3.0 μm in the surface region to be evaluated is 0.6 μm/g or less.

The Martens hardness at point SA existing on the surface of the compact is defined as _HM1 . In the cross section of the molded body including the entire length of the line segment LM, three points (P ₂ , P ₃ and P ₄ ) are taken as HM ₂ , HM ₃ and HM ₄ respectively. Since HM ₂ >HM ₃ >HM ₄ at that time, the molded body has a structure in which the hardness decreases from the surface toward the inside.

The Martens hardness HM ₁ of the outermost surface of the molded article according to the present disclosure is 1.0 N/mm ² or more. If the Martens hardness of the outermost surface is 1.0 N/mm ² or more, it is possible to contact the object to be cleaned with a high contact pressure. Also, the Martens hardness HM ₁ of the outermost surface is preferably 5.0 N/mm ² or less. If the Martens hardness HM ₁ of the outermost surface is 5.0 N/mm ² or less, when the molded body is used as a cleaning blade for a long period of time, it can flexibly contact the object to be cleaned even if it has streaky unevenness. It is possible to suppress the occurrence of poor cleaning.

The index value _Kω is a value calculated by evaluating the surface area to be evaluated of the compact including the point SA by the oblique incident X-ray method. The oblique incidence X-ray method can obtain information on locations with different depths from the surface by measuring while slightly changing the incident angle of X-rays, and by increasing the incident angle, it is possible to obtain information on deeper areas. can be obtained. Structural information at a depth of 10 μm to 65 μm can be obtained with characteristic X-rays from a Cu tube by changing the incident angle from 0.5° to 3.0°. Using the structural information obtained at each depth, the index value _Kω of the degree of crystallinity is calculated from the area ratio of the crystalline peak and the amorphous peak. A larger _Kω indicates a higher degree of crystallinity (more crystal components).

For the molded body according to the present disclosure, the index value K ω obtained by the above formula (1) from the scattering profile obtained by making the characteristic X-ray from the Cu tube incident on the surface region to be evaluated at the incident angle ω ,
_{Kω 1 > Kω 1 > _ _ Kω2} > _Kω3 .
This indicates that the outermost surface has the highest degree of crystallinity, and the degree of crystallinity gradually decreases toward the inside (in the depth direction from the surface).
By achieving a state in which the degree of crystallinity gradually decreases toward the inside, a structure suitable for the present disclosure in which the surface of the molded article is moderately hard and the inside maintains flexibility is realized.

In the molded product according to the present disclosure, it is preferable that the area of the surface region to be evaluated is equal to or larger than the X-ray irradiation area. Specifically, the irradiation area is preferably 1.5 mm ² to 11.5 mm ² . When the area of the surface region to be evaluated is equal to or larger than the X-ray irradiation area, a sufficient X-ray intensity can be obtained on the surface of the compact. can be reduced. Therefore, the crystallinity can be evaluated more accurately.

The erosion rate E is a value calculated by a micro slurry jet erosion (MSE) test. In the MSE test, fine particles having an appropriate particle size are pulse-projected onto the molded article, and the erosion rate is calculated from the depth of abrasion of the molded article at the projected portion and the amount of fine particles projected. The erosion rate E is a parameter that indicates the eroded depth per unit projection amount and indicates the brittleness of the object to be evaluated. That is, the larger the value of the erosion rate E, the more fragile the object to be evaluated. Therefore, a compact having a large erosion rate E is likely to have fine cracks due to long-term use.
General polyurethane tends to become brittle as the hardness increases. However, the compact according to the present disclosure has a small parameter indicating brittleness (erosion rate E) calculated by the MSE test, although the surface of the compact is hardened. That is, despite the high hardness of the surface, it is not brittle.
The MSE test can also be considered a value that indicates the long-term durability of the molding. For example, a compact having a surface with an erosion rate E of 0.6 μm/g or less measured using spherical alumina particles having an average particle diameter (D ₅₀ ) of 3.0 μm is sufficiently strength. Therefore, chipping is less likely to occur in the contact portion with the object to be cleaned even after cleaning over a long period of time, and the occurrence of defective cleaning due to chipping can be suppressed. In the molded article according to the present disclosure, the erosion rate E is particularly preferably 0.5 μm/g or less. It is more resistant to abrasion, and can more reliably suppress the occurrence of fine chipping of the contacted portion when used for cleaning purposes.
The MSE test can be performed using, for example, an MSE-A type test apparatus (Palmeso Co., Ltd.).

<Non-foaming polyurethane>
Molded bodies containing polyurethane according to the present disclosure are preferably non-foamed, that is, solid. The polyurethane is obtained mainly from raw materials such as polyol, polyisocyanate, chain extender, catalyst and other additives. These constituent elements suitable for realizing the physical properties described above will be described in detail below.

[non-foaming]
The reason why the molded article according to the present disclosure is preferably non-foamed, that is, solid is that the molded article is less likely to break due to bubbles, and the mechanical properties of the molded article are less likely to be impaired. However, bubbles that are unavoidably mixed in during the manufacturing process are within the allowable range. Specifically, for example, the acceptable foam content is 10% by volume or less, preferably 1% by volume or less.

[Polyol]
Polyols that can be used in the production of molded articles according to the present disclosure include those having at least one hydroxyl group at a polymer terminal, branched chain terminal, or the like.
Examples of the polyol include, but are not particularly limited to, commercially available polyols used for producing polyurethane. For example: Polyester polyols obtained by polycondensation of polyhydric alcohols and polycarboxylic acids, polyether polyols obtained by ring-opening polymerization of alkylene oxide, polymer polyols obtained by radical polymerization of vinyl monomers in polyether polyols polyesteramide polyols obtained by polycondensation of polyhydric alcohols, polycarboxylic acids and amino alcohols, polylactone polyols obtained by ring-opening polymerization of lactones, polyhydric alcohols and carbonates Polycondensation polycarbonate polyols, acrylic polyols, polybutadiene polyol and hydrogenated products thereof, polyisoprene polyol and hydrogenated products thereof, partially saponified ethylene-vinyl acetate copolymer, natural oils such as soybean oil and castor oil polyols, halogen- and/or phosphorus-based polyols, phenol-based polyols, and the like.

Examples of polyether polyols include the following. Polyether polyol compounds obtained by ring-opening addition polymerization of alkylene oxides such as ethylene oxide and propylene oxide to polymerization initiators such as ethylene diamine, tolylene diamine, sucrose, amino alcohols and diethylene glycol.

Halogen- and/or phosphorus-based polyols include, for example, the following. Halogen-containing polyols obtained by ring-opening polymerization of epichlorohydrin or trichlorobutylene oxide, brominated pentaerythritol/sucrose-based polyols, halogen-based polyols such as tetrabromophthalic acid polyester, and alkylene oxides obtained by adding alkylene oxides to phosphoric acid compounds phosphorus-based polyol and the like;

Examples of phenolic polyols include the following. Phenol or phenol derivatives such as nonylphenol and alkylphenol are Mannich-modified using formaldehyde and secondary amines such as diethanolamine, ammonia, primary amines, etc., and are obtained by ring-opening addition polymerization of alkylene oxides such as ethylene oxide and propylene oxide. Mannich-based polyols and the like.

Polycarbonate polyols include, for example, reaction products of the above-described polyols and dialkyl carbonates such as dimethyl carbonate. Specific examples include polytetramethylene carbonate diol, poly3-methylpentamethylene carbonate diol, polyhexamethylene carbonate diol, and the like. Examples of polyether polyols include reaction products obtained by addition-polymerizing one or more of the following monomers using one or more of the following compounds having at least two active hydrogen atoms as an initiator. It may be block addition, random addition or a mixture of both.
- Compounds having at least two active hydrogen atoms: ethylene glycol, propylene glycol, 1,3-butylene glycol, 1,4-butanediol, 1,6-hexanediol, diethylene glycol, neopentyl glycol, catechol, hydroquinone, bisphenol A etc. Monomers: ethylene oxide, propylene oxide, butylene oxide, styrene oxide, epichlorohydrin, tetrahydrofuran, cyclohexylene, etc. Specific examples include polyethylene glycol, polypropylene glycol, polytetramethylene ether glycol, and the like.

Polyolefin polyols include polyacrylate polyols, chlorinated polyolefin polyols, polybutadiene polyols, polychloroprene polyols, and polybutadiene styrene polyols.

As the polyol, polyols that are solid (crystallized) at room temperature can be used. In producing the molded article of the present disclosure, it is particularly preferable to use polyester polyols, which are used for producing polyurethane, because they are readily available and have an excellent balance between the crystallization temperature and the melting point of crystallization. Polyester polyols can be obtained by known methods such as polycondensation of polyhydric alcohols and polycarboxylic acids.

Polyester polyols include compounds derived from dibasic acids and polyhydric alcohols. Examples include, but are not limited to, the following. Polyester polyols derived from adipic acid, orthophthalic acid, terephthalic acid, isophthalic acid, phthalic anhydride, succinic acid, azelaic acid, sebacic acid, linoselic acid, dimethyl terephthalate, polyethylene terephthalate, and the like. Also included are lactone-based polyester polyols obtained by ring-opening polymerization of cyclic esters such as ε-caprolactone and methylvalerolactone.

Above all, in order to obtain the effects of the present disclosure, it is necessary to gradually attenuate the crystal structure from the surface toward the inside. It is a polyester polyol having a structural unit represented by the following chemical formula (1) and having a solid (crystallized) linear alkyl chain at normal temperature, and the crystallization temperature is 0 ° C. or higher and 150 ° C. or lower. It is preferable because it is suitable for Moreover, since it is required to be crystallized at room temperature, the melting point is preferably 30° C. or higher, more preferably 40° C. or higher. The melting point and crystallization temperature can be obtained by known methods such as differential scanning thermal analysis.

［化学式（１）中、Ｒ_１、Ｒ_２は炭素数４～１０の直鎖状の２価の炭化水素基であり、Ｒ_１、Ｒ_２は同一であっても、異なっていてもよい。ｎは１以上の整数を示す。］
製造上および結晶構造の特性の観点から、Ｒ_１、Ｒ_２が異なるポリエステルポリオールであることが好ましい。また、炭素数２～３の直鎖状の２価の炭化水素基を含有していてもよい。

[In the chemical formula (1), R ₁ and R ₂ are linear divalent hydrocarbon groups having 4 to 10 carbon atoms, and R ₁ and R ₂ may be the same or different. n represents an integer of 1 or more. ]
Polyester polyols in which R ₁ and R ₂ are different are preferred from the viewpoint of production and crystal structure characteristics. Further, it may contain a linear divalent hydrocarbon group having 2 to 3 carbon atoms.

The total number average molecular weight of the polyester polyol is preferably from 400 to 10,000, more preferably from 800 to 4,000. If it is 800 or more, the main chain of the polyol crystallizes, so that the obtained urethane has good hardness and chip resistance. excellent hardness and good hardness.

When the number of carbon atoms in R ₁ and R ₂ in chemical formula (1) is 3 or less, crystallization is difficult to progress and it is difficult to increase the hardness of the surface. In addition, when the number of carbon atoms in R ₁ and R ₂ is 11 or more, excessive crystallization occurs and embrittlement tends to occur.
On the other hand, when R ₁ and R ₂ are linear divalent hydrocarbon groups having 4 to 10 carbon atoms, the crystal structure formed by the orientation of the main chain portion of the polyol has a high hardness. disappears, the hardness becomes low. Therefore, when the crystal structure is attenuated from the surface to the inside, the hardness can be continuously lowered from the surface to the inside. Therefore, the molded body according to the present disclosure can increase the contact pressure against the object to be cleaned. In addition, it is possible to improve the followability to the shape of the object to be cleaned.

In addition, aggregated hard segments are present in the cured region formed by impregnating the isocyanate compound as in Cited Document 1, and when stress is applied, the hard segments are likely to be chipped off and chipped. On the other hand, the molded article according to the present disclosure has a high hardness region having a crystal structure in which main chains of polyols having linear alkyl chains having 4 to 10 carbon atoms are oriented by intermolecular forces. there is Therefore, the molded article according to the present disclosure is excellent in impact absorption. Therefore, when the molded article according to the present disclosure is applied as an elastic member of a cleaning blade, even when the cleaning blade is used for a long period of time, the lack of hard segments due to micro stress caused by unevenness in hardness does not occur. do not have. Therefore, it becomes excellent in chipping resistance.

Moreover, it is preferable to combine two or more polyester polyols having linear alkyl chains having 4 to 10 carbon atoms. As a result, the asymmetry of the crystal structure is increased, and a region with higher impact resistance can be formed. As a result, it is possible to form a hardened region with better chipping resistance.
Furthermore, when the first polyester polyol described below and the second polyester polyol described below are used in combination, the interaction between the crystal structures is promoted, and the impact resistance is further improved, which is preferable.
- First polyester polyol: a polyester polyol having a linear alkyl chain having 4 to 6 carbon atoms - Second polyester polyol: having a linear alkyl chain having 7 to 10 carbon atoms and 4 to 6 carbon atoms Polyester polyols with both linear alkyl chains

Suitable polyester polyols include the following. NIPPORUN (registered trademark) 164 (manufactured by Tosoh Corporation), NIPPOLAN (registered trademark) 4073 (manufactured by Tosoh Corporation), NIPPOLAN (registered trademark) 136 (manufactured by Tosoh Corporation), NIPPOLAN (registered trademark) 4009 (manufactured by Tosoh Corporation) Co., Ltd.), NIPPOLAN (registered trademark) 4010 (manufactured by Tosoh Corporation), NIPPOLAN (registered trademark) 3027 (manufactured by Tosoh Corporation), Polylight (registered trademark) OD-X-2555 (manufactured by DIC Corporation) ), Polylight (registered trademark) OD-X-2523 (manufactured by DIC Corporation), ETERNACOLL (registered trademark) 3000 series (manufactured by Ube Industries, Ltd.), and the like.

The structure of chemical formula (1) can be determined using a direct sample introduction type mass spectrometer that ionizes sample molecules.
Specifically, a sample sampled from the compact according to the present disclosure is heated and vaporized in an ionization chamber, and a direct sample introduction mass spectrometer that ionizes sample molecules is used at a temperature increase rate of 10 ° C./sec. , when heated to 1000°C,
When the detected amount of all ions is M1 and the integrated intensity of the peak of the extracted ion thermogram corresponding to the m / z value derived from chemical formula (1) is M2, M2/M1 is 0.0001 to 0.10000. is preferred. By including the structure of the chemical formula (1) in this range, the crystal structure of the surface can be formed more reliably.

[Polyisocyanate]
Examples of polyisocyanates include the following.
4,4'-diphenylmethane diisocyanate (MDI), 1,5-pentamethylene diisocyanate, 2,4-tolylene diisocyanate (2,4-TDI), 2,6-tolylene diisocyanate (2,6-TDI), xylene Diisocyanate (XDI), 1,5-naphthylene diisocyanate (1,5-NDI), P-phenylene diisocyanate (PPDI), hexamethylene diisocyanate (HDI), isophorone diisocyanate (IPDI), 4,4′-dicyclohexylmethane diisocyanate ( Hydrogenated MDI), tetramethylxylene diisocyanate (TMXDI), carbodiimide-modified MDI, polymethylenephenyl polyisocyanate (PAPI), trimer compounds (isocyanurates) or polymer compounds of these diisocyanates, allophanate-type polyisocyanates, buret-type polyisocyanates, water-dispersible polyisocyanates, and the like; These polyisocyanates may be used alone or in combination of two or more. Moreover, you may pre-polymerize and use by making a polyisocyanate react with various polyols. Among these, it is preferable to use a mixture of a trimer (nurate form) of xylylene diisocyanate and a monomer of xylylene diisocyanate because of its excellent mechanical properties. These may be used alone or in combination of two or more.

When the hard segment crystallizes, hardness increases but brittleness tends to decrease.
Therefore, in order to maintain proper formation of hard segments, the type and amount of isocyanate are appropriately adjusted so that the amount of chemical bonding is suitable. Among them, trimer isocyanate is particularly preferred because it has a branched structure and a strained structure in its skeleton, which can reduce the formation of hard segments.

[Chain extender]
Examples of chain extenders include the following. Ethylene glycol, propylene glycol, 1,3-propanediol, 1,3-butanediol, 1,4-butanediol, 1,5-pentanediol, 1,6-hexanediol, neopentyl glycol, diethylene glycol, dipropylene glycol , tripropylene glycol and other aliphatic diols, 1,4-cyclohexanediol, 1,4-cyclohexanedimethanol, hydrogenated bisphenol A and other alicyclic diols, bisphenol A, hydroquinone, bishydroxyethoxybenzene and other aromatic ring-containing polyhydric alcohols such as diols, trimethylolpropane, glycerin, pentaerythritol and sorbitol; These may be used alone or in combination of two or more.

[catalyst]
For the purpose of promoting the urethanization reaction between polyisocyanate and polyol, catalysts generally used for the curing reaction of polyurethane may be used in the present disclosure. Examples of catalysts include the following. Tin compounds such as tin octoate and dibutyltin dilaurate, zinc compounds such as zinc octylate and zinc acetylacetone, organic carboxylates such as potassium acetate and potassium 2-ethylhexanoate, triethylenediamine, tetramethylbutanediamine, N, N -dimethyl-N',N'-bis(hydroxyethyl)ethylenediamine, N,N-dimethyl-N',N'-bis(hydroxyethyl)propanediamine, N,N-dimethyl-N',N'-bis( hydroxyethyl)neopentanediamine, N,N-dimethyl-N',N'-bis(hydroxyethyl)hexanediamine, N-(N,N-bis(hydroxyethyl)aminoethyl)piperidine, N,N-bis( dimethylaminopropyl)-N',N'-bis(hydroxyethyl)ethylenediamine, N,N-bis(dimethylaminopropyl)-N',N'-bis(hydroxyethyl)propanediamine, N,N-dimethyl-N ',N'-bis(hydroxypropyl)ethylenediamine, N,N-dimethyl-N',N'-bis(hydroxypropyl)propanediamine, N,N-dimethyl-N',N'-bis(hydroxypropyl)neo Pentanediamine, N,N-dimethyl-N',N'-bis(hydroxypropyl)hexanediamine, N-(N,N-bis(hydroxyethyl)aminoethyl)piperidine, N,N-bis(dimethylaminopropyl) -N',N'-bis(hydroxyethyl)ethylenediamine and N,N-bis(dimethylaminopropyl)-N',N'-bis(hydroxyethyl)propanediamine, N-(2-hydroxyethyl)-N , N′,N″,N″-tetramethyldiethylenetriamine, N′-(2-hydroxyethyl)-N,N,N″,N″-tetramethyldiethylenetriamine, N-(2-hydroxypropyl)-N,N ',N'',N''-tetramethyldiethylenetriamine, N'-(2-hydroxypropyl)-N,N,N'',N''-tetramethyldiethylenetriamine, N'-(2-hydroxypropyl)-N,N, N'-trimethyl-bis(2-aminoethyl) ether, and N'-(2-hydroxyethyl)-N,N,N'-trimethyl-bis(2-aminoethyl) ether, 1,5-diazabicyclo [4.3.0 ]non-5-ene, 1,8-diazabicyclo[5.4.0]undec-7-ene, 2,3-dimethyl-3,4,5,6-teto amine compounds such as lahydro-1,3-diazine, 1,4-diazabicyclo[2.2.2]octane, 1,4-diazabicyclo[2.2.2]octane-2-methanol; These may be used alone or in combination of two or more.

[Other additives, etc.]
Additives such as pigments, plasticizers, waterproofing agents, antioxidants, ultraviolet absorbers, light stabilizers, etc., may be added as necessary. Moreover, polyrotaxane can also be contained as a toughness improver, and in particular, polyrotaxane having a hydroxyl group can also be used as a polyol and can be preferably used.

<Method for manufacturing molded body>
An example of a manufacturing method for one aspect of the molded article according to the present disclosure will be described below.
[Curing conditions]
Generally, the reaction temperature and the reaction time of polyurethane are controlled so that the urethanization reaction proceeds reliably and the polyurethane is sufficiently cured. On the other hand, in the present disclosure, embrittlement associated with high hardness, which has been a problem of conventional polyurethanes, can be prevented by setting the following curing conditions. . The curing conditions are described in detail below.
In the conventional production of polyurethane, the polyurethane is cured by heating until the cross-linking is completed, and then aged under a predetermined atmosphere. In contrast, in the production of the elastic member according to the present disclosure, curing is stopped before the polyurethane is completely crosslinked, and then secondary curing is performed by aging in an atmosphere below the crystallization temperature of the polyol.

In the semi-cured polyurethane obtained by stopping the curing reaction in a state where the cross-linking of the polyurethane has not yet been completed, unreacted polyol exists in a state of high molecular mobility. While maintaining this state, the semi-cured polyurethane is secondarily cured in an atmosphere below the crystallization temperature of the polyol. This creates a temperature gradient from the surface to the inside of the semi-cured polyurethane. As a result, the surface of the semi-cured polyurethane is rapidly cooled by being placed in the atmosphere, and crystallization of the remaining main chain portion of the polyol proceeds. On the other hand, the inside of the semi-cured polyurethane is cooled more slowly than the surface due to being placed in the atmosphere. As a result, a structure is formed in which the amount of crystallized polyol gradually decreases from the surface toward the inside. The elastic member thus obtained has a high hardness in the vicinity of the surface due to crystallization of the main chain portion of the polyol. On the other hand, the crystallization of the polyol has not progressed relatively in the interior, and the hardness is low. Therefore, the Martens hardness is gradually attenuated from the surface toward the inside.

When the polyurethane is cured until the cross-linking is completed as in the conventional method, the cross-linked structure of the polyurethane is sufficiently developed, so even if unreacted polyol remains, its molecular mobility is low. Therefore, even if aging is performed at a temperature below the crystallization temperature of the polyol after that, it is difficult to orient the main chain portion of the polyol, and crystallization of the surface hardly progresses.
In addition, when the curing reaction is stopped in a state in which the crosslinking of the polyurethane is incomplete, and then aging is performed in an atmosphere at a temperature exceeding the crystallization temperature of the polyol, the crystallization of the main chain portion of the polyol does not proceed, Crosslinking of the polyurethane also proceeds on the surface. Therefore, it is difficult to increase the surface Martens hardness of the resulting polyurethane.

In the present disclosure, the urethane is chemically crosslinked even though the primary curing is incomplete, so the surface after the secondary curing has a structure in which the crystal structure of the main chain portion of the polyol and the chemical crosslinking of the urethane are mixed. It's becoming When only the crystal structure of the main chain of polyol exists on the surface, the Martens hardness of the surface becomes excessively high, and when used for a long time, the surface of the object to be cleaned becomes flexible with streak-like unevenness. It is not possible to make contact, resulting in poor cleaning.

The crystallization of the polyol can be adjusted by the progress of chemical cross-linking of the urethane during the primary curing and the difference between the ambient temperature and the crystallization temperature of the polyol during the secondary curing. As the chemical cross-linking of urethane during primary curing is reduced, the molecular mobility of polyol after primary curing increases, the surface becomes more likely to crystallize, and the interior also becomes more likely to crystallize. Furthermore, the greater the difference between the ambient temperature during the secondary curing and the crystallization temperature of the polyol, the easier the crystallization progresses, and the crystallization of the surface and the interior is accelerated.

After placing the support member in the mold for molding, the above polyurethane raw material composition is injected into the mold, and the primary curing and secondary curing are performed as described above, whereby the molded body and the support member are integrally molded. you can get a body Alternatively, a polyurethane elastomer sheet cured under manufacturing conditions satisfying the above curing conditions may be molded, cut into strips, and adhered onto the support member. The bonding method can be selected from a method of coating or sticking an adhesive on the support member to adhere the molding, a method of superimposing the molding and the support member, heating and pressurizing them, and adhering them.
Further, after the secondary hardening, cutting may be performed to adjust the shape of the edge of the molded article to be brought into contact with the object to be cleaned. When a polyurethane elastomer sheet is prepared in advance and adhered to a member, cutting may be performed before or after adhesion.

EXAMPLES The present disclosure will be described in detail below with reference to Examples and Comparative Examples, but the present disclosure is not limited to these Examples.
<Evaluation method>
The evaluation method is shown below.
[Method for measuring polyol component]
[Method for measuring polyol component]
The polyol component was measured by a direct sample introduction method (DI method) in which the sample was not passed through a gas chromatograph (GC) but directly introduced into the ion source.
As an apparatus, POLARIS Q manufactured by Thermo Fisher Scientific Co., Ltd. was used, and a Direct Exposure Probe (DEP) was used.
Assuming that a first line segment having a distance of 10 μm from the tip side edge is drawn on the tip surface parallel to the tip side edge, the length of the first line segment is L, Polyurethane was scraped off with a biocutter from point SA of 1/2L from one end side on the first line segment.
Approximately 0.1 μg of sample sampled in the SA was fixed to a filament located at the tip of the probe and inserted directly into the ionization chamber. After that, it was rapidly heated from room temperature to 1000° C. at a constant heating rate (10° C./s), and the vaporized gas was detected by a mass spectrometer.
The detected amount M1 of all ions was the sum of integrated intensities of all peaks in the obtained total ion current thermogram. The detected amount M2 of the polyol component was the integrated intensity of the peak of the extracted ion thermogram corresponding to the m/z value calculated by the formula (2).
m/z value:
M2=(200+{14×(R1−4)+14×(R2−4)}+1)±0.5 Formula (2) R1 and R2 in Formula (2) are respectively R ₁ in Chemical Formula (1), Indicates the carbon number of _R2 .
A numerical value obtained from a sample cut from point SA was taken as the M2/M1 value in the present disclosure.

[Martens hardness]
Martens hardness was measured using a Shimadzu Dynamic Ultra Micro Hardness Tester "DUH-W211S" manufactured by Shimadzu Corporation. The measurement environment was set at a temperature of 23° C. and a relative humidity of 55%. A triangular pyramid diamond indenter with a ridge interval of 115° was used as the indenter, and the Martens hardness was obtained from the following formula (3).
Martens hardness: HM = α × P / D ² formula (3)
In equation (3), α represents a constant due to the shape of the indenter, P represents the test force (mN), and D represents the penetration amount (indentation depth) of the indenter into the sample (μm). The measurement conditions are as follows.
α: 3.8584
D: 2.0 μm
Load speed: 0.03mN/sec
Holding time: 5 seconds

As shown in FIG. 1, when it is assumed that a straight line L passing through the molded body and passing through the center of gravity G of the molded body and a point on the surface of the molded body located closest to the center of gravity G is drawn. ,
A point on the surface of the compact where one end A of the line segment LM is positioned on the straight line L was defined as SA, and Martens hardness HM ₁ was measured at the position of SA.
Furthermore _, Martens _hardness ( _{HM 2} , HM ₃ , HM ₄ ) was measured.

[Analysis of crystallinity]
The degree of crystallinity of polyurethane was measured by grazing incidence X-ray diffraction (XRD) using an X-ray diffractometer (trade name: ATX-G; manufactured by Rigaku Corporation).
The X-ray incident angles are ω1 = 0.5°, ω2 = 1°, and ω3 = 3°, the crystalline peak areas at each angle are _Ic1 , _Ic2 , and _Ic3, respectively, and the amorphous peak area is I _a1 , _Ia2 , and _Ia3 . The smaller the X-ray incident angle, the closer the surface is.

The measurement conditions are as follows.
・ Tube: Cu (40 kV 20 mA) ・ Slit condition: S2 (1 mm in length, 0.1 mm in width),
・R. S. , G. S. : open,
・Soller slit=0.41

Origin 2016 (manufactured by OriginLab Corporation) was used as peak area analysis software. First the background is determined and subtracted from the XRD pattern. Next, the crystal peak at 2θ=21° and the peak due to the amorphous component at 2θ=20° are separated. Numerical fitting was performed by fixing the peak position of the crystal, constraining the numerical value so that the integrated value of each component takes a positive value and the half-value width of the peak becomes an appropriate value.
The area value _Ic of the crystal peak is integrated from the baseline in the region 2θ = 13° to 30° when the baseline is drawn at 2θ = 3° to 40° at the peak with a peak top of 2θ = 21°. The area value obtained by
The area value _Ia of the amorphous peak is the peak top of 2θ = 20.2 °, when the baseline is drawn at 2θ = 3 ° to 40 °, from the baseline in the region 2θ = 13 ° to 30 ° The area value obtained by integration was used. _Ic1 and _Ia1 were substituted into the following formula (1) to obtain an index of crystallinity _Kω1 . _Similarly , the index Kω2 was obtained by substituting I _c2 and I _a2 into the following equation (1), and the index _Kω3 was obtained by substituting I _c3 and I _a3 into the following equation (1).
_Kω =[ _Ic /( _Ic + _Ia )]×100 (1)
It was evaluated whether the obtained values of Kω ₁ , Kω ₂ and Kω ₃ satisfy the following relationships. Then, in the column of "Crystallinity analysis" in Tables 2 and 3, "Y" is written when the relationship is satisfied, and "N" is written when it is not satisfied.
Crystallinity:
Y: When satisfying K _ω1 >K _ω2 >K _ω3 N: When not satisfying K _ω1 >K _ω2 >K _ω3

When _Kω1 , _Kω2 , and _Kω3 satisfy the relationship of _Kω1 > _Kω2 > _Kω3 , it indicates that the crystal peak ratio at 2θ=21° decreases from the surface side toward the inside. In other words, this indicates that the degree of crystallinity decreases from the surface of the cleaning blade toward the inside.

[Measurement of area of surface region to be evaluated]
The X-ray irradiation area is a value determined by the slit conditions and the X-ray incident angle. Under the slit conditions according to this embodiment, the X-ray irradiation area is 11.5 mm ² when ω1=0.5°, the X-ray irradiation area is 5.8 mm ² when ω2=1°, and ω3=3°. The X-ray irradiation area at the time is 1.9 mm ² . The following criteria were used to evaluate the relationship between the area of the surface region to be evaluated of the compact according to the present example and the X-ray irradiation area. Then, "Y" or "N" was written in the column of "evaluated area" in Tables 2 and 3 according to the evaluation result.
Y: The area of the surface region to be evaluated is equal to or larger than the X-ray irradiation area.
N: The area of the surface region to be evaluated is less than the X-ray irradiation area.

[Erosion rate E]
The erosion rate was measured using a “MSE-A type testing device” manufactured by Palmeso Co., Ltd.
Spherical alumina powder with an average particle diameter of 3.0 μm (product name “AX3-15” manufactured by Nippon Steel & Sumikin Materials Co., Ltd. Micro Company) is dispersed in water, and the spherical alumina is added at 3% by mass with respect to the total mass of the slurry. A slurry was prepared containing

As shown in FIG. 2, the compact 23 was fixed to a table (not shown) so that the slurry 22 projected from the nozzle 21 was perpendicular to the surface of the compact 23 . Slurry 22 in which spherical alumina 24 was dispersed in water 25 was sprayed with a distance of 4 mm between the surface of compact 23 and the lower end of nozzle 21 .
The measurement environment is a temperature of 23° C. and a relative humidity of 55%, the slurry projection speed is 100 m/sec, and the cutting depth is measured by a stylus-type surface profiler manufactured by Kosaka Laboratory Co., Ltd., and a diamond needle with a tip radius R of 10 μm. was measured using a stylus. The projection conditions at this time were adjusted by the following method.
Using an existing hardness reference piece (trade name “HRC-45”, manufactured by Yamamoto Scientific Tool Laboratory Co., Ltd.) in the previous measurement environment in advance, cutting 6.0 μm when 6.0 g of slurry is projected The slurry projection conditions were adjusted so that The erosion rate E at this time is 1.0 μm/g.
Measurement was performed at the measurement point SA, the slurry was projected until the cutting depth was 20 μm, and the erosion rate E was obtained from the amount of the projected slurry using the following formula (3).
Erosion rate E (μm/g)=cutting depth 20 μm/projection amount of spherical alumina particles (g) (3)

[Evaluation of cleaning performance]
In order to evaluate the cleaning performance, spherical silica powder with an average particle size of 3.0 μm (product name “AX3-15” manufactured by Nippon Steel & Sumikin Materials Co., Ltd. Micro Company) was dispersed in water, and the total mass of the slurry was A slurry containing 3% by mass of spherical alumina was prepared. The prepared slurry was applied to the surface of the glass substrate, and after drying, deionized water was again dropped onto the surface of the glass substrate.
The glass substrate was fixed to the table of the surface property measuring machine described below, and the surface of the glass substrate was coated with the slurry and 1 g of deionized water was dropped. It is made to contact so that it may become 24 degrees. Then, a slide test was conducted by reciprocating the table on which the glass substrate was fixed.
Surface property measuring machine: TYPE38, manufactured by Shinto Kagaku Co., Ltd. Molded body:
Shape: Strip Size: Width 30mm, Length 20mm, Thickness 2mm
Test condition:
Sliding load: 100g
Sliding speed: 100mm/sec
Sliding time: 5 minutes Setting distance of reciprocating motion: 50mm
After the sliding test, the silica particles remaining in the cleaning range were visually confirmed and evaluated using the following criteria. Then, in the column of "cleaning performance rank" in Tables 2 and 3, "A", "B" or "C" was written according to the evaluation results.
Rank A: All silica particles have been removed.
Rank B: Remaining silica particles were observed, but stains in which silica particles remained in streaks could not be confirmed.
Rank C: Contamination in which silica particles remain in streaks due to chipping of the molded body was confirmed.

<Material>
The materials used in the examples are shown below.

[Polyisocyanate component]
(1) A mixture of a trimer (nurate form) of xylylene diisocyanate and a monomer of xylylene diisocyanate (molar ratio-trimer:monomer=1:1.2): trade name "Takenate (registered trademark) ) XD-131R”, manufactured by Mitsui Chemicals, Inc. (2) A trimer whose main component is 4,4′-diphenylmethane diisocyanate (MDI): trade name “Millionate (registered trademark) MR-200” manufactured by Tosoh Corporation (3) Trimer of 1,5-pentamethylene diisocyanate (isocyanurate): trade name “STABIO (registered trademark) D-370N” manufactured by Mitsui Chemicals, Inc. (4) Xylylene diisocyanate: trade name “XDI” Tokyo Chemical Industry Co., Ltd. (5) 4,4'-diphenylmethane diisocyanate: trade name "Millionate (registered trademark) MT" (manufactured by Tosoh Corporation)

[Polyol component]
(1) Polyester polyol: trade name "Nippolan (registered trademark) 164" manufactured by Tosoh Corporation A combination of R ₁ and R ₂ having 4 and 6 carbon atoms in the chemical formula (1).
(2) Polyester polyol: trade name "Nipporan (registered trademark) 4009" manufactured by Tosoh Corporation R ₁ and R ₂ in chemical formula (1) have 4 carbon atoms.
(3) Polyester polyol: trade name “Polylite (registered trademark) OD-X-2555” manufactured by DIC Corporation A combination of R ₁ and R ₂ having 6 and 10 carbon atoms in chemical formula (1).

[Chain extender]
1,4-butanediol (1,4-BD): manufactured by Tokyo Chemical Industry Co., Ltd. [catalyst]
(1) Dibutyl tin dilaurate: manufactured by Tokyo Chemical Industry Co., Ltd. (2) Tertiary amine catalyst: trade name "RZETA (registered trademark)" manufactured by Tosoh Corporation

[Example 1]
A polyol component, a chain extender, and a urethanization catalyst were blended in the weights shown in Table 1. Each component was dehydrated by heating under reduced pressure, if necessary. The blended mixture was stirred under reduced pressure for 5 minutes to obtain a homogeneous polyol-based solution.
A polyisocyanate component was blended in the solution containing the polyol as the main component in the mass shown in Table 1, stirred again under reduced pressure for 3 minutes, and then a mold (thickness 2 mm, height 40 mm, width 200 m) heated to 130 ° C. ). After primary curing for 3 minutes, the mold was rapidly cooled to 25° C. and held in the mold for 12 hours for secondary curing. After that, the mold was removed from the mold to obtain a compact 1.

The mold used was coated with a release agent before injecting the polyurethane elastomer composition. A mixture of the following materials was used as the release agent.
ELEMENT14 PDMS 1000-JC (trade name, manufactured by Momentive Performance Materials) 5.06 g
ELEMENT14 PDMS 10K-JC (trade name, manufactured by Momentive Performance Materials) 6.19g
SR1000 (trade name, manufactured by Momentive Performance Materials) 3.75g
EXXSOL (registered trademark) DSP145/160 (trade name, manufactured by Exxon Mobil) 85 g
This molded body was appropriately cut to obtain a test piece used for the above evaluation. Table 2 shows the obtained evaluation results.

[Examples 2 to 10]
Molded articles 2 to 10 were obtained in the same manner as in Example 1, except that the formulation and curing conditions were changed as shown in Table 1. The same evaluation as in Example 1 was performed, and the results are shown in Table 2.

[Comparative Examples 1 and 2]
Molded articles 11 and 12 were obtained in the same manner as in Example 1, except that the formulation and curing conditions were changed as shown in Table 1. The molded bodies 11 and 12 thus obtained were evaluated in the same manner as in Example 1. Table 3 shows the results.

[Comparative Example 3]
An impregnating agent was prepared by mixing the following materials.
Polymeric MDI (MR-100, made by Nippon Polyurethane) 10g
Silicone resin (Modiper FS-700, manufactured by NOF Corporation) 2 g
2-butanone (manufactured by Tokyo Chemical Industry Co., Ltd.) 88 g
A molded article 11 obtained in the same manner as in Comparative Example 1 was immersed in the prepared impregnating agent for 180 seconds, and then aged for 3 hours in an environment of a temperature of 23° C. and a relative humidity of 55% to obtain a molded article 13. The molded article 13 thus obtained was evaluated in the same manner as in Example 1. Table 3 shows the results.

The present invention is not limited to the embodiments described above, and various modifications and variations are possible without departing from the spirit and scope of the present invention. Accordingly, the following claims are included to publicize the scope of the invention.

This application claims priority based on Japanese Patent Application No. 2021-141902 filed on August 31, 2021, the entire contents of which are incorporated herein.

［化学式（１）中、Ｒ_１、Ｒ_２は炭素数４～１０の直鎖状の２価の炭化水素基であり、Ｒ_１、Ｒ_２は同一であっても、異なっていてもよい。ｎは１以上の整数を示す。］
［構成５］
前記成形体からサンプリングされる試料をイオン化室内で加熱気化させ、試料分子をイオン化する直接試料導入方式の質量分析計を用いて、昇温速度１０℃／秒で１０００℃まで加熱したときに得られる、全てのイオンの検出量をＭ１とし、前記化学式（１）に由来するｍ／ｚ値の範囲に対応する抽出イオンサーモグラムのピークの積分強度をＭ２としたときに、Ｍ２／Ｍ１が、０．０００１～０．１００００である構成４に記載の成形体。
［構成６］
前記ＨＭ_１が５．０Ｎ／ｍｍ^２以下である構成１～５のいずれかに記載の成形体。 The present disclosure includes the following configurations.
[Configuration 1]
A non-foamed molded article containing polyurethane,
Assuming that a straight line L is drawn through the molded body through the center of gravity G of the molded body and a point on the surface of the molded body located closest to the center of gravity G, the The length of the longest line segment LM in the portion overlapping with the molded body is at least 180 μm,
Let _HM be the Martens hardness measured at the point SA on the surface of the compact where one end A of the line segment LM is located,
Martens hardness measured at three points every 30 μm from the end A on the line segment LM to the other end of the line segment LM in the cross section of the molded body including the entire length of the line segment LM HM ₂ , respectively
When HM ₃ and HM ₄ ,
_HM2 > _HM3 > _HM4 , and
The HM ₁ is 1.0 N/mm ² or more,
Regarding the index value K _ω obtained by the following formula (1) from the scattering profile obtained by making the characteristic X-ray from the Cu tube incident at the incident angle θ on the surface area to be evaluated of the molded body including the point SA , the index value when θ=0.5° is K _ω1 , the index value when θ=1.0° is K _ω2 ,
When the index value at θ=3.0° is K _ω3 , K _ω1 >K _ω2 >K _ω3 ,
_Kω =[ _Ic /( _Ic + _Ia )]×100 (1)
( _Ic is the peak area value of the scattering profile at 2θ=21.0°, and _Ia is the peak area value of the scattering profile at 2θ=20.2°), and
A compact having an erosion rate E of 0.6 μm/g or less measured using spherical alumina particles having an average particle diameter (D ₅₀ ) of 3.0 μm in the surface region to be evaluated.
[Configuration 2]
The molded article according to Configuration 1, wherein the area of the surface region to be evaluated is equal to or larger than the X-ray irradiation area.
[Configuration 3]
The compact according to configuration 2, wherein the irradiation area is 1.5 mm ² to 11.5 mm ² .
[Configuration 4]
3. The molded article according to any one of structures 1 to 3, wherein the molded article contains a structural unit represented by the following chemical formula (1).

[In the chemical formula (1), R ₁ and R ₂ are linear divalent hydrocarbon groups having 4 to 10 carbon atoms, and R ₁ and R ₂ may be the same or different. n represents an integer of 1 or more. ]
[Configuration 5]
Obtained when a sample sampled from the compact is heated and vaporized in an ionization chamber, and heated to 1000° C. at a heating rate of 10° C./sec using a direct sample introduction mass spectrometer that ionizes sample molecules. , where M1 is the detected amount of all ions and M2 is the integrated intensity of the peak of the extracted ion thermogram corresponding to the range of m/z values derived from the chemical formula (1), M2/M1 is 0 The molded article according to Structure 4, which is from 0.0001 to 0.10000.
[Configuration 6]
6. The compact according to any one of configurations 1 to 5, wherein the HM ₁ is 5.0 N/mm ² or less.

11 compact 21 nozzle 22 slurry 23 compact 24 spherical alumina 25 water

Claims (6)

A non-foamed molded article containing polyurethane,
Assuming that a straight line L is drawn through the molded body through the center of gravity G of the molded body and a point on the surface of the molded body located closest to the center of gravity G, the The length of the longest line segment LM in the portion overlapping with the molded body is at least 180 μm,
Let _HM be the Martens hardness measured at the point SA on the surface of the compact where one end A of the line segment LM is located,
Martens hardness measured at three points every 30 μm from the end A on the line segment LM to the other end of the line segment LM in the cross section of the molded body including the entire length of the line segment LM HM ₂ , respectively
When HM ₃ and HM ₄ ,
_HM2 > _HM3 > _HM4 , and
The HM ₁ is 1.0 N/mm ² or more,
Regarding the index value K _ω obtained by the following formula (1) from the scattering profile obtained by making the characteristic X-ray from the Cu tube incident at the incident angle θ on the surface area to be evaluated of the molded body including the point SA , the index value when θ=0.5° is K _ω1 , the index value when θ=1.0° is K _ω2 ,
When the index value at θ=3.0° is K _ω3 , K _ω1 >K _ω2 >K _ω3 ,
_Kω =[ _Ic /( _Ic + _Ia )]×100 (1)
( _Ic is the peak area value of the scattering profile at 2θ=21.0°, and _Ia is the peak area value of the scattering profile at 2θ=20.2°), and
A compact, wherein an erosion rate E measured using spherical alumina particles having an average particle diameter (D ₅₀ ) of 3.0 μm in the surface region to be evaluated is 0.6 μm/g or less. 2. The compact according to claim 1, wherein the surface area to be evaluated is equal to or larger than the X-ray irradiation area. 3. The molded article according to claim 2, wherein the irradiation area is 1.5 mm ² to 11.5 mm ² . The molded article according to any one of claims 1 to 3, wherein the molded article contains a structural unit represented by the following chemical formula (1).

[In the chemical formula (1), R ₁ and R ₂ are linear divalent hydrocarbon groups having 4 to 10 carbon atoms, and R ₁ and R ₂ may be the same or different. n represents an integer of 1 or more. ] Obtained when a sample sampled from the compact is heated and vaporized in an ionization chamber, and heated to 1000° C. at a heating rate of 10° C./sec using a direct sample introduction mass spectrometer that ionizes sample molecules. , where M1 is the detected amount of all ions and M2 is the integrated intensity of the peak of the extracted ion thermogram corresponding to the range of m/z values derived from the chemical formula (1), M2/M1 is 0 5. The molded article according to claim 4, which is 0.0001 to 0.10000. The molded article according to claim ₁ , wherein the HM1 is 5.0 N/ ^mm2 or less.

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